latest2@manchester.ac.ukwww.manchester.ac.uk/latest2

PROGRAMME GRANT FINAL REPORT

The LATEST2 VisionThe LATEST2 Programme was aimed at providing the underpinningfundamental research required to facilitate a step change in theapplication of high-performance, light alloy and multi-material solutionsin the transport sector that would lead to a reduction in energyconsumption and CO2 emissions. The programme was carefully tailoredto meet the needs of industry and provide the supporting researchneeded to maintain UK global competitiveness in the realignment ofmanufacturing towards more sustainable transport technologies.

Visibility and reputationThe EPSRC LATEST2 Programme Team strived to build the visibility andreputation of the research group, on both the national and internationalstage. We developed clear and consistent branding across all ourcommunication media and the EPSRC LATEST2 Programme is nowinternationally recognised. The team hosted a large number of eventsthat have been well-attended with delegates from countries around the world and we will continue to develop the UK’s reputation for research in this field.

Knowledge Transfer andresearch TranslationFor the EPSRC LATEST2 Programme to be a successful and sustainableresearch activity, the team worked hard to develop wider engagementwith academic institutions, research organisations and industrialcompanies across the transport sector supply chain. Since launch, theProgramme has been very successful at leveraging additional fundingfrom UK and European Research Councils and industrial companies and the team continues to be committed, both to knowledge transferand research translation.

Programme managementThe EPSRC LATEST2 Programme was led by the Programme Director(Professor Phil Prangnell), and supported by the LATEST2 ManagementTeam consisting of the Programme Co-Investigators, the administrativeteam led by the LATEST2 Programme Manager which included theProgramme Administrative Assistant and Science Communication Officer.The Management Team has been advised by its International Advisory Panel.

LATEST2 ProgrAmmE grAnT

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LATEST2 Programme Grant

Welcome

Research Context

The Research Programme

Theme 1: Conquering Low Formability for Optimised Design ArchitecturesResearch Article: Understanding Formability by Observing Deformation at the Microstructural Scale

Research Article: Developing Titainum Alloys with Higher Strength and Improved Ductility

Research Article: The Assessment and Quantitative Measurement of Formability in Aluminium Alloys Using Digital Image Correlation (DIC)

Research Article: Near-Net-Shape and Property Tailoring in Rolled Aerospace Products

Research Article: Improving the Quality of Magnesium Castings using Modelling and 3-Dimensional Imaging

Research Article: Control of Twinning in Magnesium Alloys Using Precipitates

Research Article: Warm Forming of High Strength Aluminium Alloys for Automotive Applications

Research Article: Understanding and Improving Formability in Magnesium Alloys

Research Article: Thermomechanical Processing of α+β Titanium Alloy – TIMETAL407

Theme 2: Joining Advanced Alloys and Dissimilar MaterialsResearch Article: Optimisation of Ultra-Short Cycle Friction Stir Spot Welding for Thin Automotive Sheet

Research Article: Critical Assessment of Welding Techniques for Dissimilar Joining of Aluminium to Steel

Research Article: Coating Design for Controlling IMC Formation in Dissimilar Al-Mg Metal Welding

Research Article: Assessment of the Advantages of Static Shoulder FSW for Joining Aluminium Aerospace Alloys

Research Article: Laser Welding of Advanced Aerospace Aluminium Alloys

Research Article: Surface Engineering Metal - Composite Hyperjoints

Research Article: Understanding Defects in Additive Manufacturing

Research Article: Understanding Heterogeneity in Additive Manufacturing with Titanium

Research Article: Integration of In-Process Deformation with Additive Manufacture of Ti-6Al-4V Components - for improved β Grain Structure Refinement and Texture Control

Theme 3: Surface Engineering for Low Environmental ImpactResearch Article: Environmentally Friendly Surface Treatment for New Generation Aluminium-Lithium Aerospace Alloys

Research Article: Nanotomography Coupled with RF-GDOES for Evaluation of the Corrosion Performance of Processed Aluminium Alloys

Research Article: Effects of Sulphur Impurity in Chromic Acid Anodizing of Aluminium

Research Article: Impact of Shot Peening Forming on Surface Integrity of Aluminum Alloys

Research Article: New Insights into Pore Initiation in Anodic Alumina

Research Article: Plasma Electrolytic Oxidation of Coupled Light Metals

Research Article: Electrochemical Testing Coupled with Real Time Imaging Provides a New Tool for Practical Assessment of Anticorrosion Performance

Research Article: Understanding the Influence of Alloying Elements/Impurity on Corrosion Property of Magnesium Alloys

Research Article: Anodic Film Formation on a Magnesium Alloy Using a Glycerol-based Electrolyte

Research Article: Formation of Electroless Nickel-Boron on Magnesium and AZ91D Alloy

Research Article: X-ray Computed Tomographic Investigation of the Porosity of Plasma Electrolytic Oxidation Coatings

Research Project List

Publications and Conference Proceedings

Prestige, Awards and Invited Lectures

Human Capital Impact

IMPACT – Science Communication

Collaborators

Management Team

International Advisory Panel

LATEST2 Team Members

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wELcomE

Dear All,

On behalf of the Management Team, it gives me great pleasure tointroduce the final ‘Showcase’ Report for LATEST2 (Light AlloysTowards Environmentally Sustainable Transport: 2nd Generation), aproject funded by an EPSRC Programme Grant (EP/H020047/1) fromJuly 2010 – July 2016. Since its inception, LATEST2 has grownorganically to become a world renowned centre in Light Metalsresearch. The LATEST2 Team have strived for research excellence and successful knowledge transfer to the academic and industrialcommunities, as well as to provide a high quality trainingenvironment. This report reflects the extensive research undertakenacross the breadth of LATEST2’s interdisciplinary themes.

LATEST2 has delivered on all its key objectives and performanceindicators. Progress has been beyond expectation, with 110 projectsinitiated at PhD/RA level (including associated projects), conductedwith 43 collaborating organisations (including 33 companies). Thetotal value of £10.95M (£8.1 direct, £2.85 in-kind support) inleveraged funding reflects the importance of research within thisfield. Over its life time the project has published 391 journal and 99conference papers, and team members have given 70 invited lectures.In addition, the Programme has attracted 34 scientific visitors frommore than 11 countries. While the project was expanded to includenew associated topics, only small modifications were made to theoriginal work plan. In particular, Theme 1 was refocused more towardsunderstanding the fundamental material factors that limit formabilityin HCP metals and high strength aluminium alloys, and to be lesstechnology driven.

Through fundamental research, in key ‘enabling’ topics, LATEST2 hasaimed to provide the underpinning science that will accelerate theintroduction of more mass efficient solutions in the transport sectorunder the three themes of i) Conquering Low Formability, ii) JoiningAdvanced Light Alloys and Dissimilar Materials, and iii) AdvancedSurface Engineering, the main outcomes of which are detailed in this report.

Knowledge transfer has been actively facilitated through workshopsand directly to our industrial collaborators’. The impact from the workis focused on manufacturing industries in the aerospace and automotivesectors, defence, and their related supply chains, both in the UK and internationally. LATES2 research is already contributing to thecompetitiveness of international and UK-based companies involved in producing high-value-added products and will result in a lowerfuture environmental impact from transport.

LATEST2 has also executed a comprehensive “IMPACT” ScienceCommunication strategy through which the Programme engagedwith a wide range of audiences to increase awareness of theimportance of the research and its industrial application. The Teamachieved strong growth in contact numbers, year-on-year, across alltarget audiences with events designed for schools, the community,industry and academia.

We hope that you enjoy reading this report, and find something ofinterest. We encourage you to visit our website and join our mailinglist so we can keep you informed of further developments and newsof future events. We would like to hear from you and have theopportunity to discuss opportunities for collaboration in futureResearch Programmes.

Yours sincerely,

Professor Philip. B. PrangnellEPSRC LATEST2 Programme Director

With a turnover of £100 billion andemploying around 600,000 people directlyand within the supply chain, it is difficult tooverstate the importance of aerospace andautomotive manufacturing to the UKeconomy. Our over-dependence on fossilfuels is clearly unsustainable, both in termsof the demand on supply and the effect ofthe pollution it creates. The world producedapproximately 35 billion tonnes of carbondioxide in 2011, which is double that seenonly twenty five years ago. This upwardtrend can be attributed to the rapidindustrialisation of Brazil, Russia, India andChina (the BRIC nations) and continuedworld population growth (Figure 1).Transport is currently responsible for 14%of global emissions of which road trafficaccounts for by far the greatest share.Airbus predicts a more than doubling of theworld passenger airline fleet by 2030 and,while this presents an unprecedentedbusiness opportunity with an estimatedvalue of $5 trillion in aircraft orders, thisgrowth rate is unsustainable without a stepchange in fuel efficient airfcraft designs.Fortunately, this impending crisis is nowbeing taken seriously by governments andindustry. In the EC the automotive sector is on track to reach the 130 CO2 g/kmaverage fleet limit by 2015. However, thenext target of 95 g/km by 2020 is far moredemanding and there is already talk of a 65g/km limit by 2050. Other importantaspects of sustainability include the impact

of the entire product life cycle, and thus theavoidance of the use of energy intensivematerials and manufacturing processes, aswell as issues such as resource scarcity, andthe need for closed loop recycling.

Energy use in transport is closely linked tovehicle mass and, due to the low energystorage density of batteries, electric vehiclesalso need to be as light as possible toextend their range to the level where theybecome a credible alternative.

Materials and manufacturing technology isnow advancing at a frenetic pace to meetthis challenge, with demand out-strippingthe supply of new scientists and researchersacross the sector. LATEST2 is thus proud tobe involved in the Sheffield-ManchesterEPSRC Centre of Doctoral Training (CDT) inMetallic Systems, which is aimed at trainingindustrially focused, PhD graduates, tobecome the next generation ofmetallurgical specialists.

In order to reach these ambitious emissionreduction targets, applications for lightalloys within the transport sector areprojected to more than double in the nextdecade and the trend is accelerating.However, in many cases the properties andcost of the materials and manufacturingprocesses are inhibiting progress in weightreduction. In the automotive industry thematerial mix depends on the intendedmarket position. The high volume sector iscurrently still dependent on steel intensive

vehicles. At the top end, carbon fibrereinforced composites are increasinglymaking their presence felt, but until thecost falls below $10 /kg CFRP will not enterthe mass car market. In between these twoextremes, in order of volume, companiesare introducing hybrid steel-light alloydesigns, fully light alloy car bodies and lightalloy CFRP composite multi-materialproducts. With reducing costs andincreasing pressure it is predicted that thehigher cost options will move to highervolume production and fully steel vehiclebodies will soon be replaced with a lightalloy intensive multi-material approach.Indeed, the slogan ‘right material, rightplace’ has become the mantra of manyautomotive designs teams. Examplesinclude the ultra-high strength boron steel safety cell with aluminium crashmembers and closure panels used byDaimler in the 2013 S-class, and the CFRPcomposite-aluminium BMW3i, whichincorporates an aluminium intensive chassis,or ‘drive module’, with a carbon fibre body,‘life module’.

rESEArch conTExT

LATEST2 And ThE InduSTrIAL LAndScAPE

Fig. 2 Comparison of the energy required to produce 1 kgof aluminium, steel and carbon fibre reinforced plastic.

Fig. 1 Annual global CO2 emissions, by sector (Center for Climate and Energy Solutions)

To be able to introduce lighter materials invehicle designs, there is an increasing focuson offsetting their higher cost by reducingthe part count through the use of largerintegral components and near-net-shapetechnologies. A further issue with the use ofcarbon fibre composites is that they require286 MJ/kg to produce compared to 23MJ/Kg for recycled aluminium, and theenergy is not easily recoverable as CFRPscannot currently be recycled into the sameproduct form (Figure 2).

In the aerospace sector metals use is alsorapidly changing. The first generation ofcomposite dominated multi-material aircraftthat are now entering service still containover 40% metallic structure, but have amuch higher reliance on titanium alloysowing to incompatibility problems betweenCFRP and aluminium. The greater use ofexpensive materials like titanium hasincreased the focus on near-net-shapemanufacturing processes, to improve thehigh buy-to-fly ratio, and similar issues have been highlighted in automotivemanufacturing where reducing coststhrough greater use of integrated structuresand new joining technologies is a high priority. New higher performance titanium and aluminium alloys will also besubstituted into existing legacy airframedesigns to achieve incremental weightsavings for many years to come andessential research is required to industrialisepotential solutions for replacements tohexavalent chromate corrosion protectiontreatments, to comply with REACHlegislation. In the UK Airbus are investing £1 billion in the ‘wing of the future’ to

develop new ultra-efficient wing concepts,an ambitious project in which LATEST2 in is participating.

In this rapidly changing landscape it is essential to develop the knowledge base that supports advanced metalsmanufacturing. LATEST2 serves this role by providing a fundamental view onstrategically important materials issues.Examples within the three themed areas offorming, joining and surface engineeringinclude: developing crystal plasticity modelsof important materials like magnesium andtitanium so that we can use sound scientificprinciples to improve formability of higherspecific strength materials than are currentlyused in industry; developing models ofinterface reaction between dissimilar metalsso that we can design alloy compositions, orcoating systems, that prevent intermetalliccompound formation during weldingdissimilar metals like aluminium tomagnesium, or titanium; studying thefundamentals of electrochemical oxidegrowth on metals so that we can tailorsurfaces to have better performance in bothcorrosive environments and for adhesivebonding and paint finishing, with lowerenergy input processes.

LATEST2 benefits from a multidisciplinaryteam, which allows an integrated approachto tackling challenging problems. Forexample, 7xxx aluminium alloys have thepotential to deliver yields stresses in excessof 600 MPa and could be used inautomotive applications with a substantialweight saving, if we can better understandhow to form them with a cost-effectiveprocess. However, at the same time, we alsoneed to tackle their poor stress corrosionbehaviour particularly when welded, oraround self-piercing rivets or fasteners.Other examples of important topics thatbenefit from this multidisciplinary approachinclude: the effect of surface deformation insituations such as forming or rectificationon corrosion; protection of heterogeneousmicrostructures associated with weldedjoints; the application of microstructuremodels developed for welding processes to predict product variability in additivemanufacturing; and the prediction of theinfluence of elements accumulating inclosed loop recycling on forming andcorrosion behaviour.

The EPSRC LATEST2 programme's primegoal was to facilitate a step change inweight reduction in transport, bydeveloping the science base required toovercome critical issues inhibiting progresstowards second generation, light alloy,multi-material designs. LATEST2 wasdesigned to accelerate the exploitation of new transformative, low energy,environmentally-compliant manufacturingprocesses, by providing solutions to theimportant materials challenges andpredictive capabilities required by industry.This required the development of anenhanced fundamental scientificunderstanding and modelling capability.

As anticipated by LATEST2, the futuredirection of the transport industry requiresmore geometrically complex designs with alower part count and the efficient utilisationof more expensive, lighter alloys. At thesame time, industry has to cope with thedifficulties presented by the introduction ofless formable, higher performance andmore recycled materials. These conflictingrequirements require a better understandingof the fundamental issues controllingforming, joining and surface engineering of light alloy products, as well as the development of more reliable predictive models.

LATEST2 research has been supported bythe development of new approaches tomaterials analysis, modelling and simulationto facilitate more rapid industrialoptimisation, while maintaining costcompetitiveness and recyclability. A focus onthe use of low energy manufacturing routesand recycled materials was an importantaspect of the research, to ensure acompetitive cost base as well as a lowenvironmental footprint.

The LATEST2 programme has involved threeinteracting themes in formability, joiningand surface engineering illustratedopposite, which have expanded over thetime frame to include other importanttopics, such as additive manufacturing,accelerated testing and organic coatings.

ThE rESEArch ProgrAmmE

I enjoyed the creative freedom of undertaking academic researchwith industrial relevance.

Arnas Fitzner, PhD Student

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THEME 2 JOINING ADVANCED ALLOyS AND DISSIMILAR MATERIALS• Joining for multi-material high performance light alloy structures

• Joining dissimilar material combinations• Modelling interface reactions,

weld microstructures and performance

THEME 1 CONQUERING LOW FORMABILITy

• Forming high performance light alloys • Modelling microstructural evolution

• Advanced forming processes and techniques• Modelling micromechanics of deformation

• Exploiting recrystallization and texture control

THEME 3 SURFACE ENGINEERING FOR LOW

ENVIRONMENTAL IMPACT• In service protection and cosmetic control

• Surface engineering for adhesion (e.g. composite to metal bonding)

• Fundamentals of corrosion at all length scales

OUTPUT AND TECHNOLOGY TRANSFEREnabling knowledge for manufacturing advanced light alloy materials and their interfacing in multi-material systems with more complex, mass efficient,

design and architecture

SIMULATION AND MODELLING RECYCLABILITY

Being part of the LATEST2research Team was a greatopportunity and a decisive step for my career.

Andronikos Balaskas, PhD Student

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ThEmE 1

Our aim has been to develop the scientificbase required for forming advanced lightalloy materials, to achieve the morecomplex shapes required by industry inthese difficult materials in a cost effectivemanner. A key ambition was to developmicrostructure sensitive models andintelligently optimise innovative techniquesfor extending formability in higher strength,lower ductility, materials and recycled alloys.

Whereas formability has been extensivelyinvestigated in steel and some automotivealuminium alloys, a new approach has beenrequired for studying warm deformation inhigh strength alloys and in hexagonalmetals (HCP) e.g. titanium, magnesium. Thishas involved understanding and modellingthe development of precipitate distributionsand its simultaneous interaction withdeformation during warm forming and thenextending modelling to describe advancedwarm forming processes. For titanium andmagnesium, the aim was to clarify themicromechanics of deformation, includingtwinning processes, for implementation incrystal plasticity models that could capturethe influences of microstructural and textureheterogeneity that lead to strain localisationand limit formability.

Another important component of the work in Theme 1 was the control ofmicrostructure during thermomechanicalprocessing, which is essential for goodformability. There has been particular focuson the role of particles in recrystallization of aluminium alloys, which is increasinglyimportant as recycled content increases, and on the texture homogeneity of titaniumand the control of texture and grain size inwrought magnesium alloys. There has alsobeen a growing activity on microstructuralcontrol of additive manufactured titanium material.

conquErIng Low FormABILITy ForoPTImISEd dESIgn ArchITEcTurES

The research has been aimed at developing the fundamental sciencerequired to underpin the following application areas:

Developing models for microstructural evolution, including texture, during themomechanical processing of light alloys.

Extending shape capabilities in conventional cold forming of mediumstrength aluminium alloys with increased recycled content.

Selection and optimisation of new warm forming operations for highstrength aluminium alloys.

Energy efficient, warm forming of HCP materials (magnesium, titanium).

Exploiting recrystallization and texture control to improve formability of HCP metals.

From Theme 1, to date, LATEST2 has generated significant industrial and academicinterest in the following areas, which have high potential for longer term impact:

Development of a new crystal plasticity model that can account for twinning in hcp metals, enabling better texture predictions during thermomechanicalprocessing and forming.

Using computational modelling to show how the texture of hcp metals, like titanium and magnesium, can affect formability by promoting the formation oftwin clusters that lead to strain localization.

Development of a new understanding of how precipitation can be used tostrengthen magnesium alloys, leading to new strategies for alloy development.

Obtaining the first direct evidence that grain boundary segregation occurs inrare earth element (RE) containing magnesium alloys and that it is crucial tocontrolling texture, a mechanism which can be exploited without using costly and scarce RE elements.

Discovering that dynamic precipitation can be used to improve the drawability of high strength aluminium alloys, producing a product with amore homogeneous final microstructure.

Demonstrating that the development of substructure in aluminium alloys isdirectly linked with the strain heterogeneity during deformation, opening theway for the development of new descriptions of the deformed state andmicrostructure evolution models.

Explaining the effect of particle size on the development of particle deformation zones.

Explaining the role of aluminium on the twinning behaviour of titanium,demonstrating that it actually acts to enhance twinning at small addition levels, informing alloy development.

Measuring strain localization in Ti6Al-4V with sub-micro resolution for the firsttime and establishing it as a new, powerful tool for comparing the fatiguebehaviour of different microstructures.

THEME 1: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT

An important part of understandingformability is studying the mechanisms ofdeformation at the microstructural scale.Traditionally this has been carried out bypost-mortem analysis of deformed samplesusing TEM and more recently EBSD.Although this provides useful information, it can only show the remnants ofdeformation, leaving one to speculateabout the actual deformation mechanisms.At Manchester we have developed a newtechnique that makes it possible to measurestrain with sub-micron resolution [1]. Thisapproach relies on the deposition of a veryfine gold pattern, which is then imagedduring deformation and analysed usingdigital image correlation (DIC). In LATEST2,this technique has now been used to studytwo fundamental issues in the formability oflight alloys: deformation around particles inaluminium and strain localisation andtwinning in titanium.

The deformation around particles inaluminium is important for formability intwo ways. Particles are fundamental formicrostructure control during processing as they act as preferential sites forrecrystallization and help randomize thetexture, which improves formability. At thesame time, particles are also preferentialsites for void nucleation during failure.Lawrence Ko, a PhD student in LATEST2,used high-resolution digital imagecorrelation (HRDIC) to study thedeformation around small particles duringplain strain compression. The results ofthese experiments, shown in Figure 1,revealed that deformation is highlydiscontinuous in nature, making theinteraction between deformation andparticle sensitive to particle size, shape andorientation, aspects of which cannot becaptured using current continuum models.The unique data we can obtain with thisapproach will be used to develop newmodels for deformation around particles inaluminium alloys, which can be used toimprove recrystallization predictions in anindustrial context.

The formability of hexagonal metals liketitanium and magnesium is difficult tounderstand due to their inherentmechanical anisotropy, which evolvesrapidly during deformation because oftwinning. Furthermore, twinning and strainlocalization are important to ductility. Forexample, it is known that adding aluminiumto titanium increases its strength butdecreases ductility, probably because it leadsto more slip localization and less twinning.During his final year undergraduate project,Albert Smith used HRDIC to observetwinning in-situ and to unravel the detailsof this important mechanism. As can be seen in Figure 2, this new approachallows us to measure the strain duringtwinning inside individual grains andquantify slip localization. This work, part of the PhD project of Arnas Fitzner andsponsored by TIMET, aims to explain theeffect that aluminium and other commonalloy additions have on these mechanismsand help develop new, stronger alloys, withhigher ductility and improved formability.

Understanding formability byobserving deformation at themicrostructural scaleJ. quinta da FonsecaLATEST2, School of materials The university of manchester

Fig. 1 a) Shear strain around a Si particle in an Al-0.1Si alloy andb) corresponding EBSD map of relative misorientation.Deformation is clearly heterogeneous at the microstructuralscale, and the rotations of the lattice are affected by theintensity, density and curvature of the slip bands.

Shear strain Relative misorientation

Fig. 2 Strain maps obtained during thetwinning of a Ti-2Al alloy. In a) a 65°compression twin can be seensurrounded by a matrix of zero strain,indicating a hard oriented grain. Themap clearly shows the high levels ofstrain generated by twinning and thedeformation in the grain above wherethe twin impinges. b) shows the strainmap moments after, clearly illustratinghow deformation in this grain occursprimarily by twin thickening.

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[1] Fabio Di Gioacchino and João Quinta da Fonseca. 2013. “Plastic Strain Mapping with Sub-micron Resolution Using Digital Image Correlation.” Experimental Mechanics 53 (5): 743–754

Publications:1. "Plastic strain mapping with sub-micron resolution using digital image correlation", F. Di Gioacchino, J. Quinta da Fonseca, Experimental Mechanics, 53, 5, 743-754, DOI: 10.1007/s11340-012-9685-2

Titanium alloys are high strength,lightweight materials that are becomingincreasingly important in the aerospacesector where they are a much better matchfor the composite fuselage than aluminiumalloys. Light weighting can be achieved byincreasing the strength of alloys but intitanium, increased strength often comeswith decreased ductility. This LATEST2project, a collaboration with TIMET, aims tounderstand the fundamental strengtheningmechanisms in titanium alloys and to helpdevelop new compositions that have higherstrengths without sacrificing ductility.

Conventionally studies of deformationmechanisms have relied on ex-situobservations of the microstructure andtexture via optical or electron microscopyand x-ray diffraction. However, these onlyshow the effects of deformation, leavingmuch of the active mechanisms to bedivined. In-situ studies using digital imagecorrelation (DIC) are more appropriate totrack slip activity during deformation. Toachieve a spatial sub-grain resolution, goldfeatures in the nanometer scale (Figure 1,top left) are applied on the sample surface.The advantage of having small goldparticles on the surface of the material isthe fact that they enable, for the first time,strain mapping with sub-micron spatialresolution. The downside of the techniqueis the tremendous effort to record imagesusing electron microscopes. Patterns

obtained using spray paint or etching markson grain boundaries can be imaged onoptical microscopes and are therefore mucheasier to use, but do not give sub-grainresolution and many of the questions posedby alloy development require sub-grainresolution answers.

Figure 1 shows schematically how the highresolution strain mapping approach works.The top left image is an electronbackscattered image of gold droplets on apolished titanium specimen. The strain mapshows 0% strain for the macroscopicallyunloaded state. The microstructure mapfrom electron backscattered diffractionmeasurements (EBSD) of this alpha titaniumalloy shows equiaxed grains. The colourscorrespond to the crystal orientation, withblue and green tones representing crystalswith the prismatic planes orientated towardsthe loading direction. Images of the golddroplets were acquired step-wise duringcompression. In accordance with thedeformation of the underlying metal grain,the droplets will move on the imaged

surface. The DIC software DaVis convertsthese relative movements into displacementvectors which can be differentiated to givestrain. Areas without strain stay dark blue,while areas of high strain appear in brightblue, up to yellow-red for higher strains. Asthe strain increases slip lines 1-10µm apartbecome apparent. Finally, at 8.7% strain, a big area of strain localisation is present,which was identified as a deformation twinfrom the EBSD map after the test. The ex-situ EBSD microstructure maps represent the microstructural evolution from a biggerarea: they are not appropriate to representthe slip activity but show therefore thedeformation induced twin lamellas. Thetwins appear red as the basal plane pointstowards the loading.

It is thought that the interaction betweenslip localization and deformation twinning is key to obtaining strong alloys with goodductility and with high resolution strainmapping we can study the mechanism as ithappens and understand how it is affectedby alloy compositions.

Developing Titanium Alloys with Higher Strength and Improved DuctilityA. Fitzner, J. quinta da Fonseca, m. PreussLATEST2, School of materialsThe university of manchester

Fig. 1 Starting with a nano-scaled gold pattern (left), usedfor digital image correlation toevaluate strain localisation(middle) with increasingcompressive deformation, whichrelates to microstructure (right))development during uniaxialcompression.

Acknowledgements:TIMET (Sponsor) with special thanks to Matthew Thomas.

Publications:1. “The effect of aluminium on deformation and twinning in alpha titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas, S. Y. Zhang, Materials Science Forum, 765, 549-553 (2013).

The aim of the research on formability inLATEST2 is to understand the interplaybetween microstructural parameters (grainsize and distribution, second phase particledistribution, texture, etc.) and theformability of different light alloys. Key tothis work is the ability to assess the degreeof anisotropy in the material by measuringr-values and building forming limit diagrams(FLDs). In the past, these have beenmeasured by measuring the deformation ongrids etched on the surface. These methods,however, provide limited spatial resolutionand cannot be used to measure theevolution of deformation during straining,which often provides valuable clues. Toovercome these limitations, the testing inLATEST2 will make use of state-of-the-artdigital image correlation (DIC) techniques.DIC is a non-contact optical method ofmeasuring fullfield surface deformation.With DIC it is possible to make timeresolved, in-situ measurements of the full2D deformation tensor. Since the techniqueis essentially magnification independent, it can be used to measure deformationdevelopment at different scales, opening up the possibility of observing directly how microstructural features affect local deformation.

The formability tests will make use of a 3D version of the method, developed byLaVision, Göttingen. Two sets of images ofthe surface of the specimen are recorded atpre-determined time intervals duringtesting, using two digital high-speedcameras. These images are then filtered,calibrated and cross-correlated to givedeformation data i.e. strains and theirdistribution and inhomogeneity. Our setupprovides a strain resolution of 0.002 withsub mm spatial resolution. Figure 1 showsthe setup in our lab. for a LaVision imagecorrelation system and an Erichsen 145/60Hydraulic sheet forming press.

DIC will be used to compile forming limitdiagrams for different materials. FLDs areusually determined by the Nakazima or theMarciniak tests in accordance with ISO12004. The principle of the Nakazima testuses a hemispherical punch to deformwasted specimens of different widths untilfailure. The maximum characteristicdeformations achievable (before failure)of the different shapes of specimens aredetermined and thus define the forminglimit curve of a material. Figure 2 shows the camera views of a specimen before and

after deformation as well as the straindistribution over a typical Nakazima test sample.

The data, in here, true strains, obtained and calculated by the DIC method areusually presented in a 2D diagram withperpendicular axes where the vertical andhorizontal axes give the major and minorprincipal strains, respectively. This allows the determination of formability limits indifferent processes such as stretch forming,deep drawing or the combination of both.Figure 3 below shows a typical forming limitdiagram for aluminium alloys.

The Assessment and Quantitative Measurement of Formability in AluminiumAlloys Using Digital Image Correlation (DIC)J. quinta da Fonseca and K. SotoudehLATEST2, School of materialsThe university of manchester

Fig. 1 Materials Science Centre, The University of Manchester. Experimentalsetup including an acquisition computer system and a hydraulic sheetforming press a) Computer system for data acquisition and analysis. b) Ring LED light source. c) High-speed cameras. d) Specimen clamped overthe punch. e) Forming press. f) Acquisition system for mechanical data.

Fig. 2 Shows typical forming limit diagram for aluminium alloys, the red curve delineates theonset of local necking, above which a successful deformation is attainable. Four strain paths/straining modes (the dashed lines and the vertical axis) are also shown on the diagrams to guidethe user. The non-deformed state of an element of the sheet, dotted circle; and the deformedstate, unfilled circle and ellipses elongated along the major axis are observable.

Fig. 3 a) non-deformed; b) deformed specimen; and c) strain distribution of the deformed sample.

In the aerospace industry, many majorcomponents are currently machined fromhot rolled aluminium plate with a very lowlevel of material utilisation. LATEST2 isworking with Primetals Technologies(formerly Siemens VAI Metals), toinvestigate the metallurgical issuesassociated with applying advanced rollingmill control-systems to produce thickness-tailored aluminium plates, for application inthe aerospace industry. This new approachto rolling can be employed to manufacturenearer-net-shape variable thickness, ortapered sections, which can potentiallyreduce machining waste of expensiveaerospace alloys and increase the platedimensions achievable from a single DCingot. In this feasibility study, the potentialfor rolling tapered, wing skins fromadvanced Al-Li alloys has been investigated.In the production of such plates, the mainmetallurgical challenges surround thenecessity to stretch the plates after solution

treatment, to reduce residual stresses and optimise the microstructure throughprecipitation of the dislocation nucleated,main strengthening phase, TI. FE modellingand simulation with digital image correlationwas performed to show that it has beenpossible to achieve a greater than 2%stretch in the entire plate with the requiredskin blank taper (Figure 1) without fracture, but this would lead to a much higher pre-stretch in the range of up to 15% at the thin end of the plate.

Following on from this analysis, a detailedinvestigation was performed on the effectof excessive stretching on the propertiesand microstructure evolution in a typical 3rd

generation, high strength, aerospace alloy,2195. This work has come to some excitingand important conclusions. Firstly, it hasbeen found that by increasing the pre-stretch, to far higher levels than arecurrently used in industry, a large increase instrength could be achieved after artificial

ageing, above that expected. For example,the benefits of pre-stretching werepreviously thought to saturate at relativelylow strain levels of < 6%. However, on pre-stretching to 15% the yield strength ofthe AA2195 alloy investigated was found tocontinue to increase to 670 MPa, comparedto 580 MPa with the standard stretch andT8 temper. Although this resulted in areduction in ductility (Figure 2), elongation to failure retained was still within the rangeacceptable for application in a compressive-loaded top wing skin. As well as this studybeing successful in demonstrating it ispossible to produce nearer-net-shapesections by rolling, it has also shown thatextending the pre-deformation prior toageing can be exploited so that theproperties can be improved and locallytailored within products: for example, toproduce higher strength at a wing tip andgreater damage tolerance at the root.

Near-Net-Shape and Property Tailoring in Rolled Aerospace ProductsPhil PrangnellLATEST2, School of materials, The university of manchester

Fig. 1 Simulation of the effect of stretching on the plastic strain distribution in plateswith different roll-taper ratios.

Fig. 2 Effect of excessive stretching on the yield Stress (0.2% proof), tensile strengthand ductility (plastic strain to failure) of AA2195 in its final T8 Temper AA2195.

The origin of the strength improvementsfound has also been studied in this project.Detailed analysis using XRD line broadeningmeasurements and TEM showed that acontinual increase in dislocation densitywith pre-strain and a very uniformdislocation distribution were seen in the2195 alloy, even at very high pre-strainlevels. The XRD results indicated asurprisingly low reduction in dislocationdensity after artificial ageing, implying thatrecovery is greatly inhibited in alloys like2195. This has been attributed to strongsolute interactions between dislocations andthe Cu and Mg in solution, as well as thestrong segregation of Cu and Mg to, andthe nucleation of TI plates on, dislocationsduring the early stages of artificial ageing.

Measurements from STEM images revealeda continued decrease in the TI plate’saverage diameter, as well as a narrowing oftheir size distribution and an increase innumber density, with increasing pre-strainlevels up to 15% (Figure 3). The spatialdistribution of the TI phase was also foundto reflect the uniform dislocation densitystill seen in the samples subjected to largepre-strains. Good agreement was foundbetween the experimental results andpredictions of the effect of pre-stretch onthe upper bound strain hardening andprecipitation hardening contributions to thealloy’s yield stress (Figure 4). Modelling hasshown that the strength contribution fromprecipitation hardening actually decreaseswith increasing pre-stretch, owing to the

stronger dependence of the obstaclestrength on the plate diameter relative to the precipitate density. In contrast, due to the low level of recovery, thecontribution from strain hardeningincreased parabolically with pre-stretch.Thus, while previous research has attributedthe increase in yield strength seen in alloyslike AA2195 with increased pre-strain to anincrease in the number density of TIprecipitates, the results here suggested theopposite. In that, there is a reduction in theTI strengthening contribution withincreasing levels of pre-strain and theincrease in strength that results from highlevels of pre-strain is a consequence of thehigh level of strain hardening retained in the material following artificial ageing.

Fig. 3 Effect of pre-strain on T1 phase refinement; (a) and (b) STEM HAADF images showing in theT8 condition for 3% and 15% pre-strain, respectively, (c) Eevolution of the average plate diameterand number density with increasing pre-strain.

Fig. 4 Effect of Pre-Strain on the main components contributing to the yieldstrength in the T8 temper, as a function of pre-strain.

Partners: Primetals Technologies , Constellium

Acknowledgements:Ben Rodgers (PhD Student)

Publications:1. “Quantification of the influence of increased pre-stretching on microstructure-strengthrelationships in the Al-Cu-Li alloy AA2195”, P. B. Prangnell, B. I. Rogers, Acta Materialia,In press (2016).

Magnesium alloys are increasingly beingconsidered for critical structural parts inaerospace and automotive applications dueto the weight saving potential associatedwith their use in place of aluminium orsteel. Key to realizing this potential is thedevelopment of processing methods thatreliably produce components that are freefrom internal defects that could producepremature failure. The magnesium industryis increasingly making use of non-destructive testing methods such asultrasonic inspection to ensure that as-castmagnesium billets can meet the stringentrequirements demanded by aerospaceindustry regulation. At present this results inscrapping a large number of defectcontaining billets, which adds a significantand undesirable penalty to the alloyproduction cost. A key difficulty is that littleis understood about the nature and sourceof the defects that lead to failure duringultrasonic inspection.

The purpose of this work was to use 3-dimensional imaging methods such as X-ray tomography and serial sectioning tounderstand in detail the nature of thedefects that form in magnesium alloycastings, and then use modelling andtargetted experiments to improve theprocessing to reduce the incidence of such defects.

Material containing defects, as identified by ultrasonic inspection, was isolated andexamined using 3-dimensional X-raytomography across a range of length scales.A tomography image of one of the largerdefects inspected is shown in Figure 1. Itwas found that these defects consisted oftwo main features; an entrained oxide filmsurrounded by an agglomeration of largeintermetallic particles which were identifiedby EDX analysis as insoluble Al-Mn phase(Al8Mn5). Serial sectioning using focussedion beam milling (FIB) revealed furtherdetails, showing that the oxide filmscontained trapped pockets of gas (Figure 2);it is these trapped pockets that lead to astrong signal response in ultrasonic inspection.

A study of the liquid metal filtering used inthe casting process and a simulation of themetal flow (Figure 3) and intermetallicevolution was used to understand theorigins of the defects during casting. It wasdemonstrated that the agglomeration ofthe oxide and coarse intermetallics, which isparticularly undesirable, was produced by atrawling effect as the oxide circulates in themelt pool. The model was used to develop abetter casting procedure that provided animproved metal flow path. This was testedand demonstrated to greatly reduce theincidence of oxide becoming trapped, andthus significantly reduce failure rates atultrasonic inspection.

Improving the Quality of Magnesium Castings using Modelling and 3-Dimensional Imagingd. mackie1, J. d. robson1, P. J. withers2, m.Turski3

1LATEST2, School of materials, The university of manchester2henry mosely x-ray Imaging Facility, The university of manchester3magnesium Elektron, manchester

Fig. 1 X-ray tomography image showing a large defectin a magnesium alloy casting. Green regions indicateentrained oxide film, blue indicates large Al8Mn5intermetallic particles.

Fig. 2 Slice from serial sectioning experimentrevealing a gas pocket trapped between oxidefilms in a magnesium casting.

Fig. 3 Simulation of liquid metal circulation in the sump during casting showing velocity vectors.

Acknowledgements:This LATEST2 associated project was performed through the EngD centre for advanced manufacturing and processing with support from Magnesium Elektron.

Publications:1. "Analysis of Casting Defects in Magnesium-Aluminium-Zinc Direct Chill Castings by X-Ray Tomography", D. Mackie, J. D. Robson, P. J. Withers, and M. Turski, TMS (2012)

2."Study of Defects in Direct Chill Magnesium Castings Using X-Ray Tomography", D. Mackie, J. D. Robson, P. J. Withers, M. Turski, T. Wilks, EuroMat 2011, France (2011)

3. “Characterisation and modelling of defect formation in direct-chill cast AZ80 alloy” D. Mackie, J. D. Robson, P. J. Withers and M. Turski, Materials Characterization, 104, 116-123, DOI: 10.1016/j.matchar.2015.03.033 (2015).

Poor low temperature formability andtension/compression asymmetry are oftenobserved in wrought magnesium productsand are detrimental to performance. Theorigin of these effects is now wellunderstood, and is due to the largedifferences in critical resolved shear stress(CRSS) for the deformation systemsoperating in the hexagonal crystal. As aresult the strength in directions in whicheasy deformation modes (basal slip and {10-12} c-axis tension twinning) can beactivated is low compared to strength indirections where the resolved shear stressfor these systems is low.

One potential method to reduce asymmetryand increase formability is to directlysuppress twinning by strengthening this

deformation mode, whilst promotingalternative slip deformation modes. Thecurrent work explores the potential to useprecipitates to achieve this objective. On afundamental level it also aims to betterunderstand the interactions betweenprecipitation and twinning in hexagonal(hcp) metals, a subject that has to datereceived little attention in the literature butis critical to the performance of mostcommercial hcp alloys.

In this work, magnesium alloys known toform precipitates of different shape andhabit were tested before and afterprecipitation treatment to study the effectof precipitation on asymmetry and explorein detail how precipitates and twinsinteract. It was shown (Figure 1) that

precipitation in some alloys (e.g. AZ91)leads to a reduction in asymmetry, whereasin other alloys (e.g. Z5) precipitationincreases asymmetry. Detailed microscopywas used to explore how precipitates inhibittwin growth. Figure 2 shows an example ofa basal plate precipitate in AZ91 entering atwin and becoming elastically bent, whichintroduces an additional back stressinhibiting propagation of the twin.

Based on this understanding a model wasdeveloped to predict which precipitates aremost effective at reducing asymmetry whilstalso increasing alloy strength. The modelcan be used to produce strengthening maps(e.g. Figure 3) that can be used to predictthe precipitate balance needed to meetgiven property goals.

Control of Twinning in Magnesium Alloys Using PrecipitatesJ. d. robson1, n. Stanford2, m. r. Barnett2

1LATEST2, School of materials, The university of manchester, uK2centre of Excellence in Light metals, deakin university, Australia

Acknowledgements:This work was carried out with the support of a Global Research Fellowship from the Royal Academy of Engineering (JDR).

Publications:

1. "Reducing Mechanical Asymmetry in Wrought Magnesium Alloys", J. D. Robson, Materials Science Forum, 765, 580-584, DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

2. "On the impact of second phase particles on twinning in magnesium alloys”, M. R. Barnett, N. Stanford, J. Geng, and J. D. Robson, 2011, in TMS 2011, 289-293 (2011).

3. “Effect of precipitate shape on slip and twinning in magnesium alloys” J. D. Robson, N. Stanford, M. R. Barnett, Acta Materialia, 56 (5), 11, DOI: 10.1016/j.actamat.2010.11.060 (2011).

4."Effect of particles in promoting twin nucleation in a Mg–5 wt.% Zn alloy", D. Robson, N. Stanford, M. R. Barnett, Scripta Materialia, 63 (8), 823-826, DOI: 10.1016/j.scriptamat.2010.06.026 (2010).

Fig. 1 TEM micrograph showing a plate shaped precipitate in the matrix (M)entering a twin (T) and becoming deflected due to the imposed shear.

Fig. 2 Stress-strain curves of AZ91 extrusion tested incompression and tension. In the precipitate free case,the compressive strength is low due to twinning leading to a high level of mechanical asymmetry. After precipitation, twinning is suppressed andasymmetry reduced.

Fig. 3 Model predicted strengthening map showing theeffect of different mixtures of the three main precipitatetypes observed in magnesium.

Weight saving is a powerful strategy forimproving energy efficiency in transportapplications. In the automotive industry, thiscan be achieved by replacing steel withcomposite materials and light alloys likealuminium and magnesium. At themoment, light alloys have cost advantagesand are much easier to reuse and recyclethan composites materials. Currentautomotive aluminium alloys are based on6xxx precipitation hardened alloys. There isan interest in replacing these with higherstrength 7xxx aerospace alloys. However,their applicability to the automotive sector iscurrently limited by their lower ductility,which hampers formability, and stresscorrosion cracking (SCC) susceptibility intheir peak-hardened condition.

The low formability of 7xxx alloys is a directconsequence of their unstablemicrostructure. In these alloys, precipitationhappens at room temperature,strengthening the material, but alsoreducing its ductility. One way to avoid thedifficulties generated by precipitation is toform the material hot, right after solutionheat treatment. This is not only difficult tocontrol, it also produces an undesiredmicrostructure that needs further heattreatment and which is susceptible to SCC.In this project, a collaboration withConstellium, we explored the possibility ofwarm forming between 150 and 250°C,well below the recrystallization temperaturebut at the temperatures at whichprecipitation occurs. The aim was tounderstand the impact of dynamicprecipitation on formability and on the finalmicrostructure and associated hardness. Thematerial was tested in the T4 (naturallyaged) and T6 (peak aged conditions) inuniaxial and biaxial tension at differenttemperatures. Cup drawing was used todetermine drawability.

Tensile testing showed that peak ageingincreases the room temperature (RT)strength, but reduces the work hardeningability, resulting in a lower elongation tofailure, as can be seen in Figure 1.Increasing the testing temperature has adrastic effect on the strength of the T6condition and reduces the work hardeningability further but the ductility increases due to an increase in the extent of stablenecking. In the T4 condition, the effect oftemperature on both strength and ductilityis much more unpredictable. Increasing thetemperature to 150°C reduces the strengthconsiderably, however, further increasingthe temperature leads to an increase in theflow stress, peaking at 220°C, although the work hardening ability is significantlydecreased. Despite this, the ductility ishighest at this temperature, which, as in the T6 condition, is a consequence of anextended period of stable necking. Biaxialtensile testing showed that ductility in thebiaxial condition varied in a similar way.

Warm Forming of High Strength Aluminium Alloys for Automotive Applicationsr. nolan, P. B. Prangnell and J. quinta da FonsecaLATEST2, School of materials, The university of manchester

Fig. 1 Tensile test results for Al 7021 tested atdifferent temperatures in the (a) T4 condition and (b) T6 condition.

A B

Warm cup drawing tests with a cold punchrevealed that the T4 material showssuperior drawability at all temperatures,except at 250°C, at which both materialsshow similar behaviour, as can be seen inFigure 2. In the T4 condition, drawability at190 °C was significantly better than at170°C and 220°C. This increase indrawability was accompanied by anoticeable increase in the hardness afterdrawing, shown in Figure 3, with the T4material showing hardness comparable tothat of the T6 tested at the sametemperature.

Microstructural studies revealed that thiswas a result of the strong interactionbetween precipitation and deformation,which peaks at 190-200°C. The typicaldeformed microstructure in this material isshown in Figure 4. This not only enhancesdrawability and produces a strong finalproduct, but also leads to a veryhomogeneous precipitate distribution(Figure 5), which will be beneficial for SCC performance.

Fig. 2 Maximum draw depths for a 110mm disk.30 mm corresponds to a fully drawn cup.

Fig. 3 Comparison of the hardness of the drawn material at the top of the cup and thewall. Note that after drawing at 190 °C thehardness is higher than after drawing at RT andcomparable to the material deformed at 220 °C.

Fig. 4 Dark field TEM image of the material drawnat 190 °C showing the different precipitates andtheir interaction with a dislocation.

Fig. 5 High resolution SEM images of the T4 and T6 microstructure. The T6 material shows obvious grainboundary precipitation and denuded grain boundaries.

Acknowledgements:David Strong, Research Technician, School of Materials, The University of Manchester.

The increased use of magnesium for weightreduction in wrought products such asautomotive body sheet is hampered by itspoor room temperature formability. It isnow well established that this formabilitycan be improved by modifying the texture.This texture modification can be achievedby adding a small (often <0.1wt%) additionof rare-earth (RE) elements [1]. However,REs are expensive with concerns aboutsecurity of supply. Therefore it is desirable tofind alternative, lower cost methods toachieve the same effect. This first requiresthe RE texture effect to be understood sothat it can be replicated.

Binary Mg-RE alloys were produced with arange of different RE elements. These alloyswere chosen to cover a range of solubilitiesand size misfit since these are both believedto be important factors in the RE textureeffect. Figure 1 plots these parameters forall REs and shows the binary systems thatwere selected. These alloys were rolled andannealed to study recrystallization andtexture evolution.

It has been demonstrated that an essentialfunction of the RE additions is to suppressdynamic recrystallization (DRX) during hotdeformation. This enables staticrecrystallization from deformed materialwith a greater spread of orientations.

Studies using the unique TITAN G2 80-200ChemiSTEM in the School of Materials haveproved that segregation of RE elements tograin boundaries is critical to produce thesuppression of DRX and the texture changeeffect. Figure 2 shows an example of Ysegregation on a grain boundary in Mg-0.15 at% Y alloy. High-resolutionimages (Figure 2c) demonstrate that the REforms very small clusters at the boundary.

When this segregation does not occur, even in RE containing alloy, the RE texture is not produced. Using the high resolutionEDX system on the TITAN ChemiSTEM, a semi quantitative estimate of the REconcentration on the boundary has beenpossible for the first time; it has beenshown for Y that the boundaryconcentration is approximately 20 times that in bulk.

Understanding and Improving Formability in Magnesium AlloysJoseph robson, Sarah haigh, david griffithsLATEST2, School of materials, The university of manchester

Fig. 1 Rare earth (RE) elements used to produceMg-RE alloys in this work.

Fig. 2 Y distribution on a grain boundary in Mg-0.15at%Y alloyHAADF STEM images and EDX composition map (a-c) increasingmagnification showing clustering of Y on the boundary.

The effect of RE segregation on grainboundary drag has been explored using theclassical Cahn-Lücke-Stüwe (CLS) model [2].From this, processing maps can be predictedshowing regions of temperature andboundary velocity where SRX and graingrowth will be suppressed by RE addition(Figure 3). The model predictions supportthe hypothesis that for typical processingconditions RE segregation does not provideenough boundary drag to prevent SRX butwill suppress grain growth, enabling adesirable fine grained structure with a weaktexture to be obtained after processing.

Summary It has been proven that strongsegregation of RE elements to grainboundaries is an essential requirement toproduce the weaker characteristic REtexture in magnesium alloys that leads toimproved formability. This segregation alsoexplains why RE can be effective even whenadded in low concentrations. The worksuggests that other elements with a strongtendency to segregate could produce asimilar texture effect without the need forexpensive RE additions. Recent work on Mg-Ca alloys suggests this is indeed the case.

Fig. 3 Predicted boundary drag map showing regions whereaddition of Y will lead to a drag pressure that suppresses staticrecrystallization (Pd>Prex) or grain growth Pd>Pgg.

Acknowledgements:This LATEST-2 associated project was performed through the EPSRC Centre for Doctoral Training in Advanced Metallic Systems with support from Magnesium Elektron.

Publications:1. "Explaining texture weakening and improved formability in magnesium rare-earthalloys", D. Griffiths, Materials Science and Technology, Volume 31, 1, 10-24, DOI: 10.1179/1743284714Y.0000000632 (2015).

2. “Effect of rare-earth additions on the texture of wrought magnesium alloys: the role of grain boundary segregation”, J. D. Robson, Metallurgical and Materials Transactions A 45 (8), 3205-3212, DOI: 10.1007/s11661-013-1950-1 (2014).

3. “Grain boundary segregation of rare-earth elements in magnesium alloys”, J. D. Robson,S. J. Haigh, B. Davis, D. Griffiths, Metallurgical and Materials Transactions A, 47 (1), 522-530, DOI: 10.1007/s11661-015-3199-3 (2016).

Thermomechanical processing of titaniumalloys is essential to generate products withtailored microstructures and a balance ofstrength, improved damage tolerance, andfatigue resistance. For example, fineequiaxed or bi-modal microstructures areobtained by deformation and annealing inthe α+β phase field. The crystallographictexture depends greatly on thetemperatures used and on the relativephase fraction during deformation.

Recently, TIMET’s Henderson Technicallaboratory in the US, in collaboration withTIMET UK, developed a new α+β titaniumalloy, TIMET407 (or Ti407) for applicationsrequiring a high degree of energyabsorption and manufacturability. TIMET arenow collaborating with LATEST2 to studythe microstructure evolution duringthermomechanical processing of this newalloy. The aim of this project is twofold: to quantify the evolution of microstructureand deformation texture duringthermomechanical processing and todetermine an effective process window for this new alloy.

Ti407 blocks in the β-annealed conditionwere uni-directionally rolled at twotemperatures, 820 and 650 °C, to 50 and75% reductions in thickness in multiple passeswith intermediate reheating between eachpass. Subsequently, after rolling at the twotemperatures, blanks were recrystallizedannealed at 820 °C for 8 h. The microstructures obtained afterrolling and annealing are shown in (Figure 1)demonstrating that spherodisation was onlyachieved when the material was rolled at650 °C to 75% reduction.

The driving force for static spherodisationdepends upon the stored energy duringdeformation which, in turn, depends on theextent of deformation and the deformationtemperature. From these results, it appearsthat only the material rolled to 75% at 650°C had the required stored energy forcomplete spherodisation.

.

The texture of the rolled materials is shownin (Figure 2). Two major texture componentswere identified – one is the transversetexture and the other is a texture in which<c> axis is tilted ~30 ° from the normaldirection towards RD. Rolling and annealingTi407 to 50 and 75% at 820 °C, gavedominance to a transverse texture with 4-6X random pole intensity (Figure 2a and 2b).On the other hand, rolling Ti407 to 50% at650 °C and annealing at 820 °C led to aweak transverse texture component whilethe tilted basal-normal texture componentstrengthened to 5-7 X intensity. Thetransverse texture component completelyvanished when Ti407 was rolled to 75% at650 °C and annealed at 820 °C.

Thermomechanical Processing of α+β Titanium Alloy – TIMETAL407 gaurav Singh1, J. quinta da Fonseca1, m. Thomas2, m. Preuss1

1The university of manchester, School of materials, manchester, uK2 TImET uK, Po Box 704, witton, Birmingham, uK

Fig. 1 Optical micrographs of Ti407. Rolled at 820 °C to (a) 50 and(b) 75% reduction and annealed at 820 °C. Rolled at 650 °C to (c) 50 and (d) 75% reduction and annealed at 820 °C.

Fig. 2 (0002) and (101 ¯0) α-phase pole figures of Ti407.Rolled at 820 °C to (a) 50 and (b) 75% reduction andannealed at 820 °C. Rolled at 650 °C to (c) 50 and (d) 75% reduction and annealed at 820 °C.

It is well known that hot workability oftitanium alloys decreases rapidly with fallingtemperature. Thus, the processing windowfor titanium alloys is usually narrower inthan in conventional steel and Al alloys. Aprocessing map of Ti407 was constructedfor the determination of optimum hotworking conditions. Maps of powerdissipation and deformation instability for Ti407 were generated at a strain of ε = 0.5 and are shown in (Figures 3a and 3b), respectively.

These maps show different peaks andvalleys of η and ξ (where η is thedeformation efficiency and ξ is theinstability parameter), which signifydifferent deformation mechanismsoperating at different combinations of T and ε .̇ A domain in these maps is definedas the window over the values of η and ξare high and constant. From the processingmap, four domains could be identified: I-A- T= 825-875 °C, ε ̇= 10-1 s-1, η = 45-65, ξ= positive; II-A- T= 725-775 °C,ε ̇= 10-2.3-10-0.8 s-1, η = 30-35, ξ= positive;III-A- T= 680-720 °C, ε ̇= 10-3-10-2.6 s-1, η = 35-40, ξ = negative; and I-B- T= 900-950 °C, ε ̇= 10-3 s-1, η = 40-65, ξ= positive. Microstructural analysis of the deformedsamples in these domains was then carriedout to determine the key microstructuralfeatures. Domain I-A is characterized bypeak efficiency of 65% and a positive ξvalue. Microstructural analysis in domain I-A indicates dynamic spherodisation (Figure4c), where the α lamellae are shearedduring deformation and subsequentlyspherodise during annealing by diffusioncontrolled process to minimize the surface energy.

Domain II-A is associated with low values ofη varying between 30-35%. In this domainpartial spherodisation of the α lamellaeoccurred with no formation of flowinstabilities. Ti407 exhibited flow instabilityonly in domain III-A, which was manifestedin flow localization bands, kinking andbending of α laths (Figure 4d). Processing ofthe alloy above the β-transus regime, i.e., in domain I-B, showed a peak efficiency of65% with dynamic recovery as the ratecontrolling mechanism.

Fig. 3 (a) Power dissipation and(b) instability maps of Ti407.Microstructures of Ti407

Fig. 4 (c) domain I-A and (D) III-A, flowlocalization and kinking of α laths arehighlighted with broken rectangles.Acknowledgements:

David Strong, Research Technician, School of Materials, The University of Manchester.

I joined LATEST2 because I wanted to work with leading academics.

Liam Dwyer, PhD Student

ThEmE 2

The main aim of Theme 2 was to developthe underpinning metallurgical sciencerequired to support cost effective, routes forjoining advanced high strength light alloysand multi-material structures. Key areasrequiring solutions included; the poorweldability of high strength alloys,interfacial reaction between dissimilarmetals, thermal damage, distortion andresidual stress, as well as the issuesassociated with manufacturing metal-composite hyper joints. Theme 3 alsocontributed to the Joining topic, throughimproving current knowledge of tailoringoxide films on metal surfaces for improvedadhesion and investigating the protection of dissimilar material joints, where galvaniccoupling is a major issue.

The dissimilar metal combinations requiredby industry, e.g. Al-steel, Mg-Al, Al-Ti, arevery difficult to join by traditional fusionwelding methods. We have thus focused onlow energy friction joining processes, fordissimilar metal combinations, andadvanced surface engineering to facilitateadhesive bonding and composite to metaljoining (Theme 3). Solid state frictionwelding techniques are highly efficient andhave the advantage of far greaterweldability and reduce the risk of interfacialreaction when welding dissimilar materials.New advances in welding technology thatwere targeted included, friction stir spotwelding (FSSW) stationary shoulder frictionstir welding (SSFSW), and high powerultrasonic spot welding (USW), inconjunction with selected fusion weldingtechniques, such as laser conduction spotand conventional laser seam welding.

A key aspect of the theme was to developmodels to predict the microstructure andmechanical behaviour of welds in high-performance multicomponent alloys. Wehave also developed a better understandingof the thermodynamic and kinetic factorsthat affect the metallurgical reactionsbetween dissimilar metals in welding, whichhas enabled us to develop strategies forinhibiting detrimental interactions, such asthe formation of brittle intermetallic layersat the weld interface.

JoInIng AdVAncEd ALLoyS And dISSImILAr mATErIALS

The research has been targeted at under pinning the following application areas:

Energy efficient joining of Mg and Al in automotive bodies.

Friction welding advanced alloys for aerospace structures with new welding techniques.

Friction welding dissimilar metal combinations requiring control of interfacial reaction (e.g. Al to galvanised steel, Ti to Al).

Low heat input laser welding light alloys and dissimilar metals.

High performance metal-composite joints; facilitated by manufacturingmechanical locking features on the metal surface to increase shear transfer (so called hyper-joints).

Surface engineering to facilitate adhesive bonding (Theme 3)

Modelling joint performance through linking process models to microstructure and weld zone property predictions.

Microstructure optimisation of additive layer manufacturing higher performanceaerospace components.

From Theme 2, to date, LATEST2 has generated significant industrial and academicinterest in the following areas, which have high potential for longer term impact:

Delivery of a full description of the performance of titanium hyper-pins for metal-composite joining and the development of a new, cheaper, more effectivemethod of manufacturing hyper-pin arrays.

Systematic assessment of new friction stir spot welding technologies for joiningaluminium automotive alloys and using fundamental process understanding todevelop new techniques for high speed welding (<1 second).

Development of friction spot welding technologies capable of producing highintegrity joints between dissimilar metals (aluminium to steel).

The development of integrated process and microstructure models, incollaboration with industry, that predict joint performance in light alloy welds, including in laser and friction welding.

The development of integrated process and microstructure models that predictintermetallic reaction rates in dissimilar metal joints.

The development of new coating systems for controlling intermetallic reaction in dissimilar joints in highly reactive systems (e.g. Al-Mg) and for the first timedemonstrating a viable welding technology for Al to Mg spot welds.

The development of models capable of predicting joint performance in highstrain rate conditions and the application of these models to predicting blastperformance of aluminium armoured vehicles, in collaboration with DSTL.

Development of 3D defect quantification and automated microstructureheterogeneity measurement tools, to provide funadamental process-understanding and aid industrial partners (Airbus, GKN, Rolls-Royce) in qualifying additive manufacturing processes for aerospace components.

THEME 2: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT

Friction stir spot welding (FSSW) (Figure 1a)is a low heat input solid-state process highlysuitable for joining difficult-to-weld highstrength aluminium alloys and for formingjoints between dissimilar materials.However, the standard process has not beenwidely adopted in the automotive industrydue to a number of problems, whichinclude too long a weld cycle time and theformation of a ‘key hole’ from the plunge ofthe tool probe that causes cosmetic issuesand weakens the joints. Research inLATEST2 has used a range of techniques,

including 3D tomography, to gain a betterunderstanding of the material flow in FSSW (Figure 2), as well as thermal andmicrostructure modelling, to try to optimisefriction spot welding processes for formingmore rapid and higher quality welds in thinaluminium sheet.

This work has shown that the probe on the tool used in conventional FSSW is not necessary in thin sheet welding. Byremoving the probe from the tool(Figure1b), we have demonstrated that it ispossible to weld faster, simplify the process,

and solve the keyhole issue. We haveshown that high quality welds can beproduced within 1 second using a pinlesstool that has been redesigned to reduce slipwith the sheet top surface (Figure 2). As anadded advantage, the more rapid weldingcycle leads to little heat affected zonedamage and after a paint bake cycle thewelds become stronger than the parentmaterial, due to the positive effect of theshorter natural ageing time of the weldzone on the artificial ageing kinetics (Figure 3).

Optimisation of Ultra-Short Cycle Friction Stir Spot Welding for Thin Automotive SheetPhil PrangnellLATEST2, School of materials, The university of manchester

Fig. 1 Schematic diagrams of (a) conventional friction stir spotwelding (FSSW), (b) Pinless FSSW and (c) the Refill FSSW processes.

Fig. 3 Hardness distributions across FSSWproduced in 0.5 seconds, immediately afterwelding and following natural ageing and thepaint bake cycle.

Fig. 2 Examples of flow studies of FSSW with a pinless tool, usingmarker materials with welds produced in 0.5 and 1 second.

We have also applied a similar systematicapproach to evaluate and optimise theRefillTM variant of FSSW, developed by HZGGermany, which employs a two part toolthat refills the probe hole as part of theweld cycle (Figure 1c). Following on from afull analysis of the material flow behaviour,we have modified the process by adding anextra stage that better consolidates thematerial after the ‘refill’ step. With this

modification, we have shown it is possibleto produce welds in under 0.5 seconds with the Refill method (Figure 4). The failurebehaviour of the spot welds has also beenmodelled with good agreement shownbetween predictions and real shear tests(Figure 5). The welds are defect free andhave excellent properties, although there isan ongoing concern surrounding tool wearwith this technology.

Overall, comparison of the lap shear testfailure loads recorded, for the optimisedshort-cycle time FSSW processes, showedsuperior joint properties to competingprocesses (Figure 6).

Fig. 4 Failure behaviour of a FSSW-Refill weld producedin 0.55 seconds, from 6111 1 mm thick sheet, duringlap shear testing.

Fig. 5 Example of FE modelling ofthe failure process of a Refill FSSW,showing the principal tensile stressdistribution in a Refill weld duringlap-shear testing.

Acknowledgements:Dr Ying-Chun Chen, Basem Al-Zubaidy (PhD Student)

Collaborators: JLR, Novelis

Publications:1. “Assessment of rapid refill FSSW for 6111-T4 aluminium automotive alloys”, B. Mohysen Al-Zubaidy, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI, On CD (2014).

2. “Dissimilar friction spot welding of aluminium and magnesium for automotive applications using novel approaches - abrasion circle FSSW and refill FSSW”, Y. C. Chen, B. Mohysen Al-Zubaidy and P. B. Prangnell in 14th International Friction Stir Welding Symposium, Beijing, China, Publ. TWI On CD (2014).

3. “The effect of a paint bake treatment on joint performance in friction stir spot welding AA6111-T4 sheet using a pinless tool”, Y. C. Chen, S.F. Liu, D. Bakavos, and P. B. Prangnell, Materials Chemistry and Physics, 141 (2-3), 768-775, DOI: 10.1016/j.matchemphys.2013.05.073 (2013).

4. “Material interactions in a novel pinless tool approach to friction stir spot welding thin aluminium sheet”, D. Bakavos, Y. C. Chen, L. Babout and P. B. Prangnell, Metallurgical and Materials Transactions A, 42A (5), 1266-1282, DOI: 10.1007/s11661-010-0514-x (2011).

Fig. 6 Comparison of the lap shear test failure loadsrecorded, for conventional FSW, FSW with a pinless tool(developed in LATEST) and the FSSW-Refil method, tobenchmark data for USW and SPR* and RSW*.

*Data taken from * L. Han et al. Materials and Design 31(2010).

New design concepts for light weightvehicles will increasingly involve multi-material structures, as they provide the best compromise solution between massreduction, performance, and cost. Suchdesigns allow materials to be used moreefficiently and will involve combining lightalloys with high strength steels andcomposites. Dissimilar joining is thus a keytechnology area for enabling increased fuelefficiency in transport.

Within LATEST2 we have taken an objectivefundamental look at a range of weldingtechnologies that could potentially be usedfor joining steel to aluminium. This workhas focused on solid state processes, orprocesses with rapid thermal cycles, to tryto reduce the tendency for intermetallic(IMC) reaction at the joint interface, whichis the main limiting factor in producingjoints with acceptable failure energies.Examples of the processes studied, include;ultrasonic spot welding (USW), the main

variants of friction stir spot welding (FSSW),and laser conduction spot welding. Efforthas also been directed at developing abetter understanding of the IMC reactionsseen in dissimilar metal welding andmodelling so that solutions can beevaluated for reducing the IMC, in parallel with process developments.

A full range of techniques has been used to study the reaction behaviour, defectsformed and, in the case of solid statewelding, the material flow and bondingprocess; including 3D tomography,modelling and high resolution microscopyof the weld interfaces. With laser spotwelding it has been shown that it is verydifficult to control the IMC layer to a thinenough level. There are also distinctproblems when welding coated steels due to evaporation of the zinc. Frictionbased solid state processes appear morepromising, but forming a reliable bondbetween a hard steel surface and a soft

aluminium alloy has been found to greatlyincrease the weld cycle time, which stillallows significant IMC reaction to take place(Figure 1-2). In FSSW this occurs becauseflow studies have shown that thealuminium sheet develops a stickingcondition with the steel surface at an earlystage in welding and, as a result, there islittle relative motion of the two materialsacross the interface. There is thus littlebenefit, in terms of cleaning oxide off thesteel surface, and the joining mechanism isprincipally one of diffusion bonding,facilitated by frictional heating. There is alsoan issue with galvanised steels due to thelow melting point eutectic reaction betweenaluminium and zinc, which creates a liquidfilm at the join line, leading to a slipcondition which causes weld defects.

Critical Assessment of Welding Techniques for Dissimilar Joining of Aluminium to SteelPhil PrangnellLATEST2, School of materials, The university of manchester

Fig. 1 Examples of typical thin IMC reactionlayers seen in dissimilar welds between DC04steel and 6111 Al; (a) a TEM image from a 2sec. conventional pinless tool FSSW, (b) SEMphase identification performed on a 1.5second USW.

Fig. 2 (a) IMC reaction layer thicknessesmeasured across weld interfaces in Al

(6111)-steel (DC04) ultrasonic and FSSWs(produced with a pinless tool), compared tothe predicted temperature profile modelledin a LATEST2 collaboration with Shercliff,

Cambridge Engineering. (Note the averageIMC thickness data was measured from the

weld centre to the edge and has beenreflected to aid comparison with the model).

As a result of the fundamental studiesperformed within LATEST2, the mostpromising solution that has immerged has been termed ‘abrasive circle welding’(ABC-FSSW). This technique (Figure 3a)involves adapting the friction stir spotwelding technique to use a slight orbitalpath, so that the tool probe lightly abradesthe steel surface over a circular area toproduce a full clean oxide-free surfaceduring the welding cycle. This technique hasallowed successful welds to be producedbetween steel and aluminium, with a veryrapid weld cycle of less than one second.The abrasion of the tool and short weldtime substantially reduces the thickness ofthe IMC layer and under low heat inputconditions can lead to a completely cleaninterface (Figure 4). As a result, weld failureenergies equivalent to that of aluminium-aluminium joints have been achieved (Figure 3c). With the same approach,successful dissimilar welds have also beendemonstrated between aluminium andgalvannealed zinc coated steel sheets.

Fig. 3 (a) Schematic diagram and (b) surface appearance of an abrasive circle friction spot weld (ABC-FSSW) betweenAl and steel; (c) comparison of the lap shear test load displacement curves with that found from a conventional FSSW.

Fig. 4 (a) Pull-out failure mode and (b) and (c) SEM and TEM images of the ‘clean’ interfaceproduced by the ABC-FSW process.

Acknowledgements:Dr. Hugh Shercliff, P. Jedrasiak (Uni. Cambridge Engineering) Dr. S. Ganguly (Uni. Cranfield) Dr Farid Haddadi (PhD Student), Dr YingchunChen (Latest RA), Lei Xu (PhD student).

Collaborators: JLR, Tata Steel.

Publications:1. “Effect of interfacial reaction on the mechanical performance of steel to aluminium dissimilar ultrasonic spot welds”, P. B. Prangnell, L. Xu, L. Wang, Y. C. Chen, J. D. Robson, Metallurgical and Materials Transactions A, 334-346, DOI: 10.1007/s11661-015-3179-7 (2016).

2. “Modelling of the thermal field in dissimilar alloy ultrasonic welding”, P. Jedrasiak, H. R. Shercliff, Y. C. Chen, L. Wang, P. B. Prangnell and J. D. Robson, Journal of Materials Engineering and Performance, 24, 799-807, DOI: 10.1007/s11665-014-1342-8 (2015).

3. “Modelling and visualisation of material flow in friction stir spot welding”, P. B. Prangnell, A. Reilly, H. R. Shercliffe, Y. C. Chen, Journal of Materials Processing Technology, 473-474, DOI: 10.1016/j.jmatprotec.2015.06.021 (2015).

4. "Interface structure and bonding in abrasion circle friction stir spot welding: A novel approach for rapid welding aluminium alloy to steel automotive sheet", Y.C. Chen, A. Gholinia, P.B. Prangnell, Materials Chemistry and Physics, 134, 459-463 (2012).

5. “Effect of zinc coatings on joint properties and interface reaction in aluminium to steel ultrasonic spot welding”, F. Haddadi, D. Strong and P. B. Prangnell, TMS, San Diego, Sup. Proc. Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

6. “Interface structure and bonding in rapid dissimilar FSSW of al to steel automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W. A. Cassada, TMS, Pittsburgh, PA (2012).

The automobile industry is facing ever moredemanding emissions targets, which hasaroused wide interest in replacingtraditional materials with lighter metals,such as Al and Mg. In the future moreefficient new vehicle designs will also beincreasingly based on multi-materialstructures, where the best attributes ofdifferent materials can be exploited. Thisnew direction of the automotive industrythus presents major challenges in joiningdissimilar metals. Direct joining ofaluminium to magnesium alloys is verychallenging, with virtually all weldingmethods producing poor weld propertiesthat suffer from low toughness. This is eventrue for lower temperature solid statejoining techniques, like friction stir welding[1,2]. The problem mainly lies in the rapidformation of Al - Mg intermetalliccompounds (IMCs) which can severelyembrittle the joint interface.

In particular, the Al3Mg2 phase is reportedto have the highest growth rate among thecommon Al - Mg compounds [1-3] and isthe phase in which cracks are most prone toinitiate, owing to its low strength and highlybrittle nature.

In LATEST2 this reactive system has nowbeen fully characterised, including theidentification of the previously controversialAl30Mg23 phase and a full description hasbeen made of the reaction kinetics, grainstructure and texture of the reactions layer(Figure 1). We have also now shown, usinga FIB ring-core milling procedure, that theIMC layer contains large residual stressesthat develop as it grows. Previous work inLATEST2 has both modelled the IMCreaction in this system [2,3] and shown thatbarrier inter-layers, such as PVD Mn, can beeffective in controlling the Al-Mg interfacialreaction rate [4]. Unfortunately, such thinbarrier coatings were found to becomereadily damaged by friction weldingprocesses, reducing their effectiveness [4].

To address the intermetallic reactionproblem, now thermodynamic calculationshave been used to predict more ductile Al-alloy compositions that could be applied asthicker coatings by cheap establishedtechnologies, like the Novelis FusionTM

process, and change the reaction path toavoid the formation of the problematic βphase [5]. Two candidate alloys werepredicted to have potential: i) a Si-richcoating; and ii) an Al-Zn-rich solid solutioncoating. In the former case, calculationsshowed the addition of Si favours the morestable Mg2Si phase over β and, in thesecond, with a high enough Zn content, theternary phase τ-(Al,Zn)49Mg32 was predictedto replace the β phase. Long-termannealing and refill friction stir spot welding(Refill-SSW) experiments were carried out tostudy the effect of these new coatingsystems on the intermetallic growthbehaviour, under static and weldingconditions. For the Al-Si alloy coating,Novelis provided a 6xxx alloy coated by their

Coating Design for Controlling IMC Formation in Dissimilar Al-Mg Metal WeldingP. B. PrangnellLATEST2, School of materialsThe university of manchester

Fig. 2 Interface characterisation of Al-Mg diffusion couples afterannealing at 400°C for 3 hrs; (a) unclad Al (6111) and (b) theAl(Si) clad material, both joined to Mg AZ31; (c) identification ofthe Mg2Si phase in the Al(Si)-Mg IMC layer, and (d) EDX lineprofile along the red line shown in (b).

Fig. 1 Examples of the IMC reaction layer kinetic (a)and microstructural data (b) obtained from Al-Mgdiffusion couple experiments).

proprietary FusionTM process, while the Al-Zn coating material was made in house.The results of static heat treatments areshown in Figs. 2 and 3, where it can beobserved that in both cases the β-Al3Mg2

phase did not develop when the coatingalloys were used. With the Al-Si coating(Figure 2) the IMC layer was much thinnerand only the γ-Al12Mg17 and Mg2Si phaseswere identified. In the second case, aspredicted, the β-Al3Mg2 phase was found tobe replaced by the τ-(Al,Zn)49Mg32 (Figure 3)but unfortunately the new IMC layer stillgrew at the same rate.

Results for the Al-Si coating from Refillfriction stir spot welding showed that the Sirich coating was less effective than hoped inreducing the IMC layer reaction rate,because it was discreetly distributed withinsecond phase particles and with the veryrapid heating cycle seen in welding therewas insufficient time for diffusion of Si.However, the Al-Si coating was still effectivein increasing the strength of the Al-Mgdissimilar welded joints. In lap shear testsfailure loads of within 97% of that ofsimilar welds in the weakest weld member(i.e. Mg-Mg) were achieved, which is the

best performance ever reported for Al toMg spot welds (Figure 4a). Analysis ofpartially failed welds showed that this couldbe related to a reduced IMC reaction layerthickness, but also the residual Si particleswithin the IMC layer deflected the crackpath along the weld interface into thealuminium substrate (Figure 4b). This work has thus demonstrated there is potential to ‘engineer’ the IMC reaction layer indissimilar welding to mitigate its negativeimpact on joint properties.

Fig. 2 Comparison of interface microstructures after annealing Al - Mgcouples at 360°C for 24 hrs in (a) unclad Al (6111) and in (b) whenwelded to an Al(52%Zn) alloy. The inserts are from EBSD phase ID maps.

(a) (b)

Fig. 3 (a) Results from lap shear tests conducted on Refill-FSSWs comparing thefailure load for welds produced with the new Al-Si coated Al sheet to that foroptimised standard uncoated Al-Mg welds and the target properties of Mg-Mgsimilar welds. In (b) with the Al-Si coating, more limited IMC reaction and crackdeflection by the Si particles embedded in the IMC layer can be seen at thejoint interface. It can be noted that with the coated sheet the failure load ofthe dissimilar weld has reached 97% of that for the Mg-Mg benchmark.

Acknowledgements:Yin Wang, Basem Mohysen Al-Zubaidy, Lexi Panteli - project PhD StudentsDr Ying Chun Chen – Theme 2 PDRA.

Collaborators: Novelis and Magnesium Electron.

Publications:1. “Optimisation of aluminium to magnesium ultrasonic spot welding”, A. Panteli, Y. C. Chen, D. Strong, X. Zhang and P. B. Prangnell, Journal of Materials, 64 (3), 414-420, DOI:10.1007/s11837-012-0268-6 (2012).

2. “The effect of high strain rate deformation on intermetallic reaction during ultrasonic welding a luminium to magnesium”, A. Panteli, J. D. Robson, I Brough and P. B. Prangnell, Materials Science and Engineering A, 556, 31-42; DOI:10.1016/j.msea.2012.06.055 (2012).

3. “Interfacial reaction during dissimilar joining of aluminum alloy to magnesium and titanium alloys”, J. D. Robson, A. Panteli, C. Q. Zhang,D. Baptiste, E. Cai, P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A.D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

4. “The effectiveness of surface coatings on preventing interfacial reaction during ultrasonic welding of aluminum to magnesium”, A. Panteli, J. D. Robson, Y. C. Chen and P. B. Prangnell, Metallurgical and Materials Transactions A, DOI: 10.1007/s11661-013-1928-z (2013).

5. “Coating design for controlling b phase imc formation in dissimilar Al-Mg-metal welding”, Y. Wang, L. Wang, J. D. Robson, B. M. Al-Zubaidy and P. B. Prangnell, Friction Stir Welding and Processing VIII, 171, DOI: 10.1002/9781119093343.ch19 (2015).

Friction Stir Welding (FSW) is now a well-established process that is widely used tojoin aluminium alloys, owing to theexcellent weld properties that can beobtained. The technology was originallydeveloped in the UK by the TWI andinvolves translating a rotating tool along thejoin line between two butted plates, whichforges the two weld members togetherwithout melting. Stationary (Static) ShoulderFriction Stir Welding (SSFSW) is a newvariant of FSW that was first developed toimprove the weldability of titanium alloys,because their low thermal conductivityresults in a severe temperature gradientthrough the plate thickness. This is becausein conventional FSW heat is generatedpredominately by the tool shoulder andwith thicker material it is not normallypossible to maintain a high enoughtemperature at the base of the weld to

avoid pin failures, unless a low travel speedis used. SSFSW can also provide severaladditional advantages over the conventionalmethod, including: i) a non-rotatingshoulder irons the surface and leads to animprovement in surface quality and ii) theshoulder acts as a heat sink rather than asource so that the heat distribution shouldbecome narrower at the top surface andmore uniform through the plate.

Surprisingly, despite these clear advantagesstatic shoulder FSW has largely beenignored by the aluminium weldingcommunity. In LATEST2 we have developeda systematic approach for comparing thetwo processes, when applied to joining highstrength Al-aerospace alloys. The approachwe adopted was to use an identicalshoulder and pin geometry for each method(Figure 1) and to first understand and modelthe relationship between the heat input and

the welding parameters, using torque/power curves, so that both processes can be compared using a rational selection ofthe optimum welding conditions. Modellinghas also been used to fit the thermal fieldfor each process and predict the systematiceffect of varying the contribution of theshoulder heat generation on the HAZ shape (Figure 2b). We have also studied the surface finish that can be achieved(Figure 3) and the formation of weld defectsthat can be specific to the SS-FSW processand the residual stress distribution in eachprocess (Figure 4).

It has been shown that stationary shoulderwelding requires an approximately 30%lower heat input than conventional FSW.Welding with a stationary shoulder alsoproduces welds with a narrower, moreparallel, heat affected zone and lowerthrough-thickness microstructure and

Assessment of the Advantages of Static Shoulder FSW for JoiningAluminium Aerospace AlloysPhilip Prangnell, matt royLATEST2, School of materials, The university of manchester

Fig. 1 Tool designs and HAZ profiles for the two process variants; (a) FSW, (b) SS-FSW) under optimised conditions, note the narrower andmore parallel HAZ with static shoulder FSW.

Fig. 2 (a) comparison of the relationship to rotation rate to the power curves for conventional FSW and SSFSW, with optimum process windows marked by the vertical dashed lines; (b) thermal model showing the effect on thetemperature field profile of reducing the shoulder power input, while increasing the probe power to maintain the same weld temperature near the weld root.

property gradients (Figure 1). The weldsperformed better than conventional FSWs incross-weld tensile tests. DIC analysis of thestrain distribution in the test pieces revealedthat this resulted from their narrower HAZ helping to prevent premature failure,by imposing greater constraint on the localisation of plastic strain during deformation.

Thermal simulation, combined withhardness modelling, confirmed that theabove benefits arose from changing the

FSW process from one, where the majorityof heat is introduced by conduction into theworkpiece from the energy dissipated by arotating shoulder, to one where heat isgenerated more uniformly through the platethickness by only the probe (Figure 2). Inaddition, it was shown that the ironingeffect of the stationary shoulder could beused to greatly reduce the weld’s surfaceroughness (Figure 3). Furthermore, thecolder surface temperature dramaticallydecreased the reduction in workpiece

thickness normally seen along the weld linein the standard FSW process, caused by theshoulder plunge. The distribution of residualstresses was also found to change, with areduction in the peak tensile stresses seen incertain welding conditions and a narrowerresidual stress profile (Figure 4). A negativeeffect of welding with a stationary shoulderwas noted in this work under hotterwelding condition, in that it can lead tosurface ‘speed cracking’ similar to that seen in extrusion.

Fig. 3 Comparison of the difference in surface roughness found between (a) conventional FSW and (b) static shoulder SSFSW.

Fig. 4 Comparison of the longitudinal residual stress distributions seen in (a) FSW and (b) SSFSW, determined by the contour method.

Acknowledgements:Hao Wu (PhD Student), Tianzhu Sun, (PhD Student), Dr. Yingchun Chen.

Publications:1. “Stationary shoulder FSW for joining high strength aluminium alloys”, H. Wu, Y-C, Chen, D. Strong and P. B. Prangnell, Journal of Materials Processing Technology, 221, 187-196, DOI: 10.1016/j.jmatprotec.2015.02.015 (2015).

2. “Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, and P. B. Prangnell, Thermec, Las Vegas, USA (2013).

3. “Systematic evaluation of the advantages of static shoulder fsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong and P. B. Prangnell, Materials Science Forum, 794-796, 407-412 (2014).

Advanced high strength aluminium-lithiumalloys, such as AA2198 and AA2196, have acombination of excellent strength and lowdensity that means they are now thematerial of choice for future single aisleairframes. To maximize the cost and weightsaving benefits of these alloys, there is astrong motivation to replace currentmechanical fastening technologies (e.g.riveting) with a welding process. Laserwelding is one of the most promising ofsuch processes, allowing fully automatedwelding at high speed with minimalmicrostructural damage. However, it ishighly challenging to weld Al-Li alloys usingany fusion welding process due to the highalloy content and the sensitivity of thestrength of the base materials to thermaldamage. The high alloy content of the basemetals can make the alloys susceptible tohot cracking. Understanding the complexinteractions during welding is key tosuccessful laser welding of Al-Li components.

The work described here aims to developsimulation tools to develop laser welding forjoining of Al-Li alloys. In parallel, advancedcharacterization techniques have been usedto obtain a better understanding of theeffect of process parameters on the weld integrity.

The integrated model that has beendeveloped consists of two maincomponents, as shown in Figure 1. The first is a process model that takes the weldprocess parameters, geometry etc. andcalculates the thermal profile at anyposition. This output is used as an input to the microstructure and hot cracksusceptibility (HCS) models. The processmodel is implemented in the ABAQUS finite element framework.

Once the thermal history of the weld isknown, this can be combined with thecalculated melt pool chemistry to estimatethe HCS. Both the freezing behaviour and

thermal history are considered. Hot cracksform under conditions where thermalcontraction leads to cracks that cannot behealed by inward liquid flow. The HCS canbe expressed in terms of a critical strain rate(due to thermal contraction) that can betolerated before cracking. A high value ofthe inverse of this critical rate indicates acondition with a high susceptibility to HCS.By considering the local thermal conditionsand composition in the weld pool, HCSmaps can be produced for differentconditions and used to identify positionsand weld parameters that lead to a high risk of HCS (Figure 2).

In addition to HCS, weld integrity can alsobe limited by porosity that arises fromentrained gas. It is not yet possible topredict such porosity, so this has beencharacterized experimentally using 3-dimensional X-ray tomography (XCT). Using the unique capabilities of the HenryMoseley X-ray Imaging Facility (HMXIF) atManchester, it has been possible for the firsttime to determine the size and distributionof such pores for a range of weld powers.An example image for a low weld power isshown in Figure 3. It was found that therewas an optimum weld power giving thebest compromise between HCS and gasporosity. This is being used to produce afull-scale skin-stringer demonstrator panel.

Ongoing work using the HCS model isunderway to further improve the weldperformance by identifying promising fillerwire chemistries that could replace thestandard Al-Si filler typically used in laserwelding of Al-Li.

Laser Welding of Advanced Aerospace Aluminium Alloysyingtao Tian1, Joseph robson1, Stefan riekehr2, nikolai Kashaev2

1LATEST2, School of materials, The university of manchester2helmholtz-Zentrum geesthacht, Zentrum für material und Küstenforschung gmbh

Fig. 1 Flow chartshowing thecomponents inthe integratedmodel for laserwelding ofaerospacealuminium alloys.

Fig. 3 Porosity(red) identified ina weld producedwith low power(1400W) by X-raytomography.

Fig. 2 Fusion zone macrographs and predictions of the hotcrack susceptibility (HCS) model for three welds producedat different powers (a) 1400W, (b) 1720W, (c) 2000W.Bright colours indicate higher HCS.

Acknowledgements:This project was co-funded by LATEST2 and the EU-FP7 CleanSkys programme LAWENDEL. Thanks to Constellium for the provision of materials used in this work.

The use of composites is increasing inadvanced civil airframe designs, to improvefuel efficiency. However, metallic materials,and in particular titanium alloys, still featurestrongly where a higher temperaturecapability, or multi-axis loading is required.For example, the new A350XWB‘composite’ aircraft is actually a multi-material design and contains over 40%metallic structure. Producing reliable jointsbetween high performance titanium alloysand composite components is challengingbecause of their very different chemical and physical properties. There is a need toimprove load transfer efficiency and moveaway from the reliance on fasteners, which create bearing issues in compositelaminates. At the same time, adhesive onlymetal-composite joints currently do nothave a long enough safe design life, or loadtransfer capability without a large lap area,which increases weight.

‘Hyperjoints’ are a new class of joint thataim to address some of these problems byincorporating both mechanical and adhesivebonding into one joint design. InHyperjoints’, arrays of locking features areengineered on to the metal part that arethen imbedded into the composite laminateto increase the shear transfer, via bothbetter adhesion and mechanical ‘fit’,through the thickness of the laminate. This approach can greatly improve the joint strength and failure energy.

A typical aerospace hyperjoint designrequires the ability to reliably manufacturearrays of small pins (typically ~ 1 mmdiameter) with an accurate geometry on atitanium substrate (Figure 1). In partnershipwith EADS, within LATEST2 we haveexplored methods of assessing the qualityand predictability of the failure load ofhyperpins manufactured by differenttechniques, so that an industrially viableprocess can be identified for their full-scalemanufacture. Approaches that have beenexplored, include electron beam surfacesculpting (Surfi-Sculpt®) laser additivemanufacture (AM), and micro-weldingtechnologies that can attach pre-forgedpins sufficiently rapidly for industrialisation.Such methods can have drawbacksincluding, restrictions in the pin shape(Surfi-sculpt) and slow production rates(AM). In LATEST2 we have studied themetallurgical issues associated with eachapproach, including the critical areabetween the base of the pins andcomponent substrate (Figure 2), wherethere is usually a sharp microstructuralgradient. Methods have also beendeveloped to test and model theperformance of individual pins (Figure 3), aswell as to study the damage that develops

in a laminate joint assembly under loadusing the 3-D imaging X-ray ComputedTomography (XCT) facilities in theManchester X-Ray Imaging Facility (MXIF)(Figure 1). Within Theme 3 on surfaceengineering, work is also on-going tounderstand how to use electro-chemicaltreatments more effectively to tailortitanium surface oxide films pore structuresto improve adhesion on metal surfaces.

A potentially viable manufacturing routehas now been identified and plans are afootto expand this activity to investigate theissues associated with scaling up thetechnology for industrial application.

Surface Engineering Metal -Composite HyperjointsP. B. Prangnell, J. d. robsonLATEST2, School of materialsThe university of manchester

Collaborators: EADS Innovation works, TWI.

Acknowledgements:Rotimi Oluleke (EADS- PhD Student) Dr. Fabien Leonard (MXIF)).

Publications:1. "Mechanical and microstructural characterization of percussivearc welded hyper-pins for titanium to composite metal joining", R. J. Oluleke, D. Strong, O. Ciuca, J Meyer, A. De Oliveira and P. B. Prangnell, in LMT2013, 6th International Symposium on Light Metals Technology, Materials Science Forum, 765 , 771-775.,DOI: 10.4028/www.scientific.net/MSF.765.771 (2013).

Fig 3. (c)

Fig. 3 (a) FE model and (b) failure of anadditive manufactured hyperpin, duringshear testing, (c) an alpha phase EBSDmap of the Ti64 AM pin near its base,with prior β grains outlined.

Specimen 11205

Fig 1. Fig 2.

Fig 3. (a)

Fig 3. (b)

2mm

2µm

50µm

Fig. 1 X-ray micro tomography imageshowing the hyper pin array in a loaded lapjoint with the development of damage inthe composite indicated in red.

Fig. 2 High resolution SEM image showingthe microstructure variation across the meltpool fusion boundary of a ‘welded on’hyper-pin with a Ti64 rolled plate substrate.

Additive manufacturing (AM) is an excitingup-and-coming near-net-shape technologythat is in the process of being rapidlyindustrialised for aerospace manufacturing.AM is extremely attractive to the aerospaceindustry as it allows great design flexibility,reduces lead times, and most importantlygreatly reduces the amount of machiningrequired to produce components made outof expensive and difficult materials liketitanium alloys. For example, the buy-to-flyratio for a typical titanium componentmachined from forged billet is 10 – 20:1compared to 2 – 5:1 when manufactured byAM. A particular issue in the qualification ofAM for aerospace applications is the controlof defects that can arise and their effect onfatigue life. In titanium AM the defects thatare generated arise primarily from gas

porosity and a lack of fusion of the powderparticles, caused by process instability.Within LATEST2 we have been activelyengaged in using advanced characterisationtools, such as 3D X-ray computedtomography (XCT) to characterise thedefects formed in different AM processeswith statistically reliable data and correlatetheir size and positon to the processparameters (e.g. Figure 1).

This work has shown that in somecommercial powder bed AM processes thecontrol software does not always performas expected and can over-correct for factorssuch as overhang regions, or on beam pathreversal in rastering, which results in toolow a local heat input and a high defectdensity (Figure 2). We have also investigatedthe effectiveness of HIPing operations to close pores in AM components (Figure 2d,e). In addition, work has been performedto understand the effect of pores on highcycle fatigue life. This has includeddeveloping procedures for reducing thescatter in fatigue data and predicting worstcase defects in components, by ranking the

local stress concentration factor calculatedfrom pore data-sets obtained from full XCTscans of test samples. In this procedure, theproximity of pores to a surface, or to otherpores, and the effect of sample geometrywere estimated using simplified linearmechanics. By using this method to plot the number of cycles to failure against thestress intensity factor at the crack initiationlocation, rather than the global stress, the scatter in fatigue data was greatlyreduced (Figure 3).

The role of porosity in AM parts in fatiguecrack growth has also been studied byrepeatedly re-scanning fatigue samples ascracks initiate and grow, which has revealedthat pores within most powder bed partsare generally to widely spaced to have asignificant effect on fatigue crack growth.This observation has been confirmed bymeshing of the XCT data within FE models,which has shown that pores don’t greatlyinfluence the stress field at a crack tipunless it is approached to within one porediameter of the crack front (Figure 4).

Understanding Defects inAdditive ManufacturingPhil PrangnellLATEST2, School of materials, The university of manchester.

Fig. 1 Examples of pore types (a) and (b) densitynear the edge and centre of selective electron beammelted (SEBM) Ti64 samples, measured by XCT.

Fig. 3 High cycle fatigue life data: (a) plotted as astandard S-N plot of stressrange against cycles tofailure; and (b) re-plotted interms of the stress intensityfactor range generated bythe specific pore found atthe crack initiation site,against cycles to failure.

Fig. 2 Example of the effect of process themes on the distribution of porosity in cubic SEBM testsamples; (a) and (b) projections of all the defects inthe x-y pane for (a) separate standard contouringand hatching routines and (b) when just using thecontour setting; (c) corresponding plot of the porevolume fraction with distance from the samplesurface. (d) and (e) show the high effectiveness of HIPing in closing extreme defects in samples built with poor process control.

Fig. 2 (a) Growth of afatigue cracks past apoor in an AM sample,tracked by XCT and (b)the influence of poreson the stress field at acrack tip (von Mises)modelled usingautomated messhingof XCT data.

Acknowledgements:Airbus, UK, EADS, Innovation Works, Filton, UK, GKN Aeropsace, UK.

Collaborators: Prof Iain Todd Sheffield (Collaborator) Sam Tammas-Williams (RRs- PhD student).

Publications:1. “XCT analysis of the influence of process parameters on defect population in Ti-6Al-4V components manufactured by selective electronbeam melting”, S. Tammas-Williams, H. Zhao, F. Leonard, F. Derguti, I. Todd and P. B. Prangnell, Journal of Material Characterisation, 102, 47 - 61, DOI: 10.1007/s10008-015-2864-1 (2015).

2. “The effectiveness of hot isostatic pressing for closing porosity in titanium parts manufactured by selective electron beam melting”, P. B. Prangnell, S. Tammas-Williams, I. Todd, P. J. Withers, Metallurgical and Material Transactions. A, In press (2016).

3. “Predicting the influence of porosity on the fatigue performance of titanium components manufactured by selective electron beammelting”, S. Tammas-Williams, J. Donoghue and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

AM is attractive to the aerospace industry asit allows great design flexibility, and near-net-shape manufacture of componentsmade from expensive and difficult tomachine materials like titanium alloys. Forexample, the buy-to-fly ratio for a typicaltitanium component machined from forgedbillet is 10 - 20:1, compared to 2 - 5:1when manufactured by AM. A range of AMplatforms are available from laser andelectron beam powder bed, to blownpowder and wire based systems, such asplasma or laser wire deposition. Thesesystems vary in resolution (layer height) andthe deposition rate and size of componentsthat can be built. There is thus a trade-offbetween precision and component scale;i.e. SLM laser powder bed is most suitablefor complex high precision, but small(typically less than 0.5 m), components,whereas plasma-arc wire deposition can beused to produce large less complex parts

(over 10 m in length). Although a lot ofwork has been done to develop thesetechnologies, to date surprisingly little efforthas been devoted to understanding thematerials issues they present, particularly interms of the uniformity and isotropy of themicrostructure and texture developed in AM components, which is of concern tothe aerospace industry.

In AM the material solidifies in a smallmoving melt pool, and material is built upwith many overlapping raster tracks, leadingto very high solidification and cooling ratesand a complex cyclic thermal history. Themoving melt pool solidification conditions inAM tend to promote very coarse directionalprimary grain structures, particularly intitanium alloys which exhibit little solutepartitioning on solidification. WithinLATEST2 this phenomenon has beeninvestigated across a full range of AM

platforms. This work has conclusively shownthat the coarse β grain structure primarilydevelops by epitaxial re-growth of β grainsat the fusion boundary, which re-form andcoarsen every time the material is re-heatedabove the β transus temperature as theheat source approaches (Figure 1).Columnar growth follows the solidificationfront at the rear of the melt pool and canoccur up through many added layersallowing, selection of preferentiallyorientated grains and leading to a strong βtexture. Work has shown that the grainstructure and texture seen in AMcomponents is thus very dependent on themelt-pool shape, size, and travel speed. Thegrain structure is also affected by the beampath and in powder bed AM systemsproximity to the part surface, where thepowder can provide opportunities forheterogeneous nucleation (Figure 2).

Understanding Heterogeneity in Additive Manufacturing with TitaniumPhil PrangnellLATEST2, School of materials, The university of manchester

Fig. 1 The development of a coarse-columnarprimary β- grain and strong texture intensityseen with Ti64 in thick sections for in theSEBM AM Processes.

Fig. 2 Examples of variability in primary β- grain structures with Ti64 in (a) athin section wall produced in an SEBM powder bed system and (b) evidenceof nucleation from the surrounding powder at the wall surface, (c) effect of achange in section thickness, and (d) effect of alternating the raster path withlayer height in a large scale arc based AM process (WAAM).

A parallel investigation has been performedon the homogeneity of the transformationstructure seen in different AM processeswith the alloy Ti-6Al-4-V. To obtainstatistically reliable results, this has involveddeveloping an automated tool for mappingthe main microstructure indicators, namelythe α lath width and the retained βspheroidicity, across different length scales.The tool involves automatically batchprocessing large arrays of high resolutionSEM images, either as stitched maps tostudy local heterogeneity, or regularly

spaced in grids to capture long rangeheterogeneity. This work has revealed thatthe transformation microstructure can varysignificantly, both across individual layers,and over long distances across wholesections (Figure 3a) in the build plane andvertically, well as in response to geometrychanges (Figure 3b). For example, in SEBMpowder bed systems the microstructure iscoarser and more spherdoidised near thebase of a build, because the materialconsolidated first spends a longer time at ahigh temperature. For components with

non-uniform sections, changes in sectionand build orientation can also affect thetransformation structure because thisinfluences the local heat flow (e.g. throughthe solid metal towards the base plate,relative to that into the lower conductivitysurrounding powder). In certain machinesthe control system also dynamically managesthe heat input to each layer, depending onthe local geometry, which can also affectthe transformation microstructure.

Acknowledgements:Dr Alphons Antonysamy (ex EADS-PhD Student now at GKN), Hao Zhao (PhD student) Sam Tamas-Williams (RRs- PhD student).

Collaborators: Airbus, UK, EADS, Innovation Works, Filton, UK, GKN Aeropsace, UK.

Publications:1. “Automated multi-scale microstructure heterogeneity analysis of selective electron beam melted TiAl6V4 components”,H. Zhao, A. A. Antonysamy, J. Meyer, O. Ciuca, S. W. Williams and P. B. Prangnell, TMS 2015, Additive ManufacturingSymposium, Supplementary Proceedings, 429-435, DOI: 10.1002/9781119093466.ch54 (2015).

2. “Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec, Quebec (2011).

3. “Influence of build geometry on beta grain structure and texture during additive layer manufacture (ALM) of Ti-6Al-4V by electron beam selective melting”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Titanium Conference (2011).

4. “Effect of wall thickness transitions on texture and grain structure in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A Antonysamy, P. B. Prangnell and J. Meyer, Materials Science Forum, 706 - 709, 205-2010, DOI: 10.4028/www.scientific.net/MSF.706-709.205 (2012).

Fig. 3 Statistical data obtained from automated batch processing of arrays of high resolution SEM images showing, (a) a progressive decrease in α lath width and reduction in circularity of the retained β with build height, for a 30 cmtall part, and (b) variation in α lath width with build height and sample orientation in a triangular cross section (Ti64 SEBM powder bed process).

Additive Manufacturing (AM) is a rapidlygrowing technology that is attracting greatinterest and large investments in theaerospace sector, because it allows near-net-shape manufacture of complex partswith a low buy-to-fly ratio. AM can alsofacilitate shorter product lead times andmore design freedom than traditionalmanufacturing processes, which can providesubstantial weight savings by allowing themanufacture of topographically optimisedcomponents. However, AM is based on thelayer-wise deposition of material throughmelting with a moving heat source and thiscan lead to quite different microstructuresand textures than are produced in moreconventional processes, as has beenpreviously demonstrated in a prior LATEST2project [1].

Of particular concern when manufacturinglarge scale AM components with titanium alloys, like Ti-6Al-4V, is that the solidification conditions promote homo-epitaxial re-growth within eachmelted layer, causing very coarse directionalgrain structures to develop (Figure 1a).Because of the preferred <001> growthdirection in cubic metals, these largecolumnar grains tend to have a strong β<001> fibre texture parallel to the averagesolidification direction within a particularAM process. On cooling, the finaltransformation texture is weakened by the12 possible variants of the α phase formedwithin each β grain (Figure 2a), as describedby the Burgers orientation relationship, butthis can still lead to anisotropy in theproperties of titanium AM

components. Disrupting this undesirableprimary columnar β structure bymetallurgical means is challenging as there are few options for grain refiningadditions in titanium.

Integration of In-Process Deformation with Additive Manufacture of Ti-6Al-4V Components - for improved β Grain Structure Refinement and Texture ControlP. B. PrangnellLATEST2, School of materialsThe university of manchester

Fig. 1 Examples of reconstructed IPF coloured EBSDmaps comparing the coarse columnar, strongly <001>textured, primary β grain structure, that is normally seenin AM parts, with the refinement that can be obtainedby an in-process deformation step: (a) wire arc AMwithout and with the application of a roller to eachdeposited layer, (b) laser blown powder AM without andwith the application of peening by UIT. Note; the redcolour denotes a strong <001> orientation aligned ~with the build direction (samples courtesy of CranfieldUniversity and BAE Systems).

Fig. 3 Examples from in-situ EBSD heating studiesshowing the reconstructed prior β phase at roomtemperature and direct indexing of the re-growth of βat close to the transus temperature; (a) for a lightlydeformed material (~2% strain) and (b) a higher pre-strain (~15%). Unreconstructed regions in the roomtemperature maps correspond to α phase twinning. In(a) new β orientations can be seen within the α twins,whereas many more new β orientations are found in (b).

In partnership with Airbus, BAE SYSTEMS,and Cranfield University, LATEST2 has beeninvestigating the potential for introducing adeformation step within AM, to reduceresidual stresses and improve the grainstructure and texture. Two methods havebeen studied, mechanical peening(ultrasonic impact treatment; UIT) andconstrained rolling of each layer after it isdeposited. The results have been excellent(Figs 1 & 2). For example, despite the smallstrains introduced into the layers in rolling(10 - 20%) the β grain size in wire arcadditive manufacturing (WAAM) wasreduced from several millimetres to lessthan 100 μm, which has led to a morefundamental study on why adding an ‘in-process’ deformation step in AM is so

effective at refining the β grain structure.This has involved simulating thedeformation step and rapid heating cyclesseen in AM, as well as observing, for thefirst time, the α -> β transition in a lightlydeformed AM material in-situ in an SEM byEBSD (Figure 3).

The results of this work have revealed thatthe β grain refinement mechanism involvesthe formation of new orientations withinthe thin retained β layers between the fineα lamellar by twinning, when the AMtransformation structure is deformed. Thesenew orientations then grow when re-heating above the β transus, on depositingthe next layer, which refines the grainstructure and randomises the texture in thesubstrate material on which each new melt

track solidifies. This prevents columnargrowth developing epitaxially over manylayers and thus disrupts the establishmentof the strong texture and coarse grainstructure normally found in AM parts. Themechanism for re-orientating the retained βdiscovered in this work has not beenobserved before and it is thought that itoccurs specifically in AM materials becauseof the fine nature of the transformationstructure, which promotes twinning duringcold deformation.

Fig. 2 The prior beta and final alpha textures seen in AMsamples produced by the blown powder method (a) a standardpart and (b) with the application of UIT (peening) to each layer.

Acknowledgements:Jack Donoghue - project PhD Student; Dr Ali Gholinia – Experimental Officer

Collaborators: Gatan, developmental high temperature heating stage; Airbus, student support; BAE Systems, blown powder direct metal deposition andultrasonic impact treatment; Cranfield University, wire arc AM; WAAM-rolling.

Publications:1. "The effectiveness of combining rolling deformation with wire-arc additive manufacture on ß grain refinement and texture modification in Ti-6Al-4V materials characterization", J. Donoghue, A. A. Antonysamy, F. Martina, P. A. Colegrove, S.W. Williams and P.B. Prangnell,Materials Characterization, DOI: 10.1016/j.matchar.2016.02.001 (2016).

2. “In-situ high temperature EBSD analysis of the effect of a deformation step on the alpha to beta transition in additive manufacturedTi6Al4V”, J. M. Donoghue, J. Quinta Da Fonseca and P. B. Prangnell, Ti-2015: The 13th World Conference on Titanium, On CD (2015).

3. “Integration of deformation processing with additive manufacture of Ti-6Al-4V components for improved ß grain structure and texture,additive manufacturing”, J. Donoghue, J. Sidhu, A. Wescott and P. B. Prangnell, TMS 2015, Additive Manufacturing SymposiumSupplementary Proceedings, 437-444, DOI: 10.1002/9781119093466.ch55 (2015).

4. "EBSD analysis to understand Additive Manufacturing (3D Printing) in titanium", P. B. Prangnell, J. Donoghue, A. Gholinia, O. Ciuca, A. A. Antonysamy, Opening address at RMS-EBSD Meeting, London (2014).

I really enjoyed being part of and contributing to theLATEST2 research Team.

Teruo Hashimoto, LATEST2 Technical Support Staff

ThEmE 3

The aim of Theme 3 was to develop thescientific understanding required to underpinand explore creative, new, environmentally-compliant and economically viable solutionsto i) enhance surface properties andperformance, including reduced corrosionsusceptibility, ii) facilitate joining of dissimilarmaterials (e.g. metals to composites) and themanufacture of hybrid materials and iii)protect multi-material structures, thusfacilitating the introduction of moreefficient designs.

For light alloys, corrosion control is a vitalaspect of many surface treatments where,for example, local variations in microstructureimpact significantly on both the corrosionsusceptibility and the uniformity ofprotective coating development. Importantly,microgalvanic effects are also decisive indetermining the performance in service.Consequently, major topics in this themeinclude understanding of the roles ofmicrostructure at all length scales on surfaceengineering, including advancement of 3D electron imaging of corrosion andprotection systems, and local subsurfacemicrostructures, textures and surfaceroughening, developed through formingand joining.

Such understanding has provided improvedsurface appearance and performance offormed materials from knowledge of theimpact of near-surface deformed layers onoptical appearance and surface integrity. Forsurface treatments, a more detailedknowledge of conventional anodizing andplasma electrolytic oxidation of light alloyshas enhanced practical applications. Inaddition, other treatments, including sol gelprocesses and conversion coating are also ofimportance for effective use of light alloys.

SurFAcE EngInEErIng For LowEnVIronmEnTAL ImPAcT And InTErFAcE dESIgn

The research has been aimed at supporting the following application areas:

Development of environmentally-friendly, economic coating routes for advanced light alloys across the transport sector.

Prevention of cosmetic corrosion in automotive closure panels by control of process-surface activated corrosion.

Prevention of stress corrosion cracking of light alloys for applications in the transport sector.

Development of self-healing and ‘smart’ coating technologies and new system assessment procedures, for example, image assistedelectrochemical noise analysis to replace accelerated corrosion testing.

Designing versatile surface treatment and finishing procedures tosupport the use of advanced forming and joining approaches foradvanced light alloys.

Development of targeted surface treatments for protecting weldedjoints between dissimilar materials.

Surface engineering for enhanced bonding of metals in hybridmaterials/ laminates and to polymer matrix composites.

From Theme 3, to date, LATEST2 has generated significant industrial andacademic interest in the following areas, which have high potential forlonger term impact:

Nanoscale 3D characterization has provided new insights into alloydegradation mechanisms through precise determination of corrosionpropagation paths and locations of local anodes and cathodes. For the first time, intergranular corrosion has been correlated with thequantitatively determined distribution of defects within grains.Knowledge created will be exploited by industry for alloy development.

The development of a fast screening technique, based on thequantification of the influence of near-surface deformed layers on theoptical appearance of aluminium alloys, for production line qualitycontrol of rolled products.

Tailored REACH compliant anodizing and surface pretreatments foraluminium and magnesium alloys in aerospace and automotive industries.

Development of surface treatments for protecting welded jointsbetween dissimilar light metals.

3D characterization of the degradation process of corrosion protectioncoatings. Knowledge created has been exploited by AkzoNobel fordeveloping new coating formulations.

THEME 3: KEy OUTPUTS WITH POTENTIAL FOR HIGH IMPACT

Increasing payload and fuel efficiency aredrivers for the aerospace industry to striveto improve lightweight materials forapplication in aircraft structures. Lithium-containing aluminum alloys are attractivedue to their low density and high stiffnesscompared with conventional aluminumalloys. For service performance, anadequate, economic, and environmentally-friendly corrosion protection scheme isnecessary. Traditionally, the anticorrosionperformance of aerospace aluminum alloyshas been achieved through chromic acidanodizing (CAA), followed by painting.However, the increasing environmentalconcerns and strict legislation on the use ofchromic acid require the development of low-cost and environmentally-friendlyanodizing electrolytes.

In this work, the anodizing behavior of acommercial Al-Li-Cu alloy in anenvironmentally-friendly electrolyte, namelytartaric-sulfuric acid (TSA), has beeninvestigated. Attention is focused onoptimizing the process parameters to tailorthe morphology, composition and structureof the resultant porous anodic films toachieve desirable performance.

A relatively fine porous anodic film, withwell-defined cells, was observed at relativelylow voltages, with copper-rich nanoparticlesoccluded in the film material (Figure 1).Pores of increased dimensions, with lateralporosity, were observed at increasedvoltages (Figure 2). The oxidation of copperis responsible for the additional lateralporosity in the anodic film. It is also revealedthat copper in the alloy matrix can beoccluded in the anodic film material ascopper-rich nanoparticles (Figure 3) or it canbe oxidized and incorporated into the filmmaterial as copper ions, depending on theanodizing voltage. Further, lattice images ofcopper-rich nanoparticles indicate that theyhave structures consistent with either the Ө, Ө' or Ө"phases, regardless of theirlocations in the anodic films.

Environmentally Friendly Surface Treatment for NewGeneration Aluminium-LithiumAerospace Alloys x. Zhou, g. E. Thompson, y. ma LATEST2, School of materialsThe university of manchester

Fig. 1 Transmission electron micrographs of anultramicrotomed cross section of AA 2099-T8 aluminumalloy after anodizing from the OCP to 3 V (SCE) at asweep rate of 0.03 V/min: (a) bright field image; (b)HAADF image.

Fig. 2 Transmission electron micrographs of anultramicrotomed section of AA 2099-T8 aluminum alloyafter anodizing at a constant voltage of 14 V: (a) brightfield image; (b) HAADF image.

Fig.3 Lattice images ofcopper-rich nanoparticles:(a-d) in different regions ofthe anodic film.

(a) 100nm

200nm(b)

(a)

(c)

(a)

(b)

(b)

(d)

Acknowledgements: This LATEST2 project was performed with support from Airbus Publication

Publications:1. Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, P. Skeldon P. Thomson and E. Koroleva. Single-stepFabrication of Metal Nanoparticle Loaded Mesoporous Alumina Through Anodizing of a CommercialAluminum Alloy, Electrochemical and Solid-State Letters, 15, E4-E6, 2012.

2. Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, X. Zhong, E. Koroleva, P. Skeldon P. Thomson and M. Fowles. Discontinuities in the Porous Anodic Film Formed on AA 2099-T8 Aluminium Alloy, Corrosion Science, 53, 4141-4151, 2011.

3. “Microstructural modification arising from alkaline etching and their effect on anodizing behaviour of Al-Li-Cu alloy”, J. Electrochemical Society, 160, C111-118, 2013 (Y. Ma, X. Zhou, G.E. Thompson, X Zhang, C Luo, M. Curioni and H. Liu).

1. “Anodic Film Growth on Al-Li-Cu Alloy AA2099-T8”, Electrochimica Acta, 80,148-159, 2012, (Y. Ma, X. Zhou, G.E. Thompson, M. Curioni, P. Skeldon, X. Zhang, Z. Sun, C. Luo, Z. Tang and F. Lu).

Fig. 3 The elemental depth profiles for magnesiumand zinc which contribute significantly to thecorrosion behaviour of the alloy. A sputtering rate of 66 nm/s was achieved. Magnesium oxides arepresent at the surface after rolling.

It is known that the thermomechanicalprocessing of aluminium alloys by rollingand extrusion significantly alters theirmicrostructures. These microstructures canbe beneficial to the mechanical behaviourof the material, but they can also bedetrimental to the corrosion properties inreal-life situations. In particular, an alteredmicrostructure is developed in the near-surface regions duringthermomechanical processing.

The understanding of the corrosionbehaviour of a commercially producedaluminium alloy is important for materialdurability. Employing a technique recentlydeveloped at The University of Manchester,nanoscale in-SEM tomography allows theobservation of the nanoscale structuresdeveloped within the near-surface region ofcommercially produced alloys. Examples ofresults are presented in Figures 1 and 2 Theinformation that can be acquired from thistechnique can quantify changes in the size,shape and distribution of the relevantmicrostructural features.

During rolling, the altered near-surfacemicrostructure is distributed across thesurface by the rolls in a manner that canresult in inconsistent distributions of suchmicrostructures. The varying microstructureacross the surface can have significantlydifferent corrosion behaviour whencompared to the bulk alloy.

Further, it is often difficult to assess thecorrosion properties of the commerciallyproduced alloys due to the complex natureof altered near-surface microstructures,which also have altered phase distributions.In particular, contact with the rolls can leadto the incorporation of various hot-formedoxides into the near-surface region.Microalloying of various types of oxides,including those of magnesium, zinc andaluminium, have been witnessed beneaththe surface.

Elemental depth profiles of the samecommercially produced alloy are providedby radio frequency glow discharge opticalemission spectroscopy. Analysis of the firstfew microns of the rolled surface canprovide accurate readings relating toelemental concentrations present within the near-surface region, as shown in Figure3. Such analysis helps to correlate thecorrosion behaviour of the alloy to thedistribution of the chemical species in thenear-surface region of the alloy.

Nanotomography Coupled with RF-GDOES for Evaluation of the Corrosion Performanceof Processed Aluminium AlloysA. cassell, g. E. Thompson, x. ZhouLATEST2, School of materials, The university of manchester

Acknowledgements: This LATEST2 project was performed with support from Constellium.

Publications:1. A. Cassell, G. E. Thompson, X. Zhou, T. Hashimoto and G. Scamans. Relating Grain Misorientation to the Corrosion Behaviour of Low Copper 7xxx Aluminium Alloys, Mater. Sci. Forum, 765, 623-628, 2013.

GDOES Element-time Profile of 7021 T4As-rolled and As-polished (dash-dotted line) surfaces

Times (s)

0 5 10 15 20 25 30

Elem

ent Count

8

6

4

2

0

Fig. 1 3D rendering of the volume of themicrostructure associated with the near-surfaceregion of a commercially produced AA7xxx alloy,revealing three zones: namely a, b and c, withsignificantly different microstructures comparedwith the bulk.

Fig. 2 HAADF micrograph of the cross section ofthe same near-surface region rendered in 3D inFig. 1. Features within the zones are readily compared.

Anodizing processes are widely used forprotecting aluminium alloys againstcorrosion. The resultant films are composedof amorphous alumina and consist of aporous, outer region and a thinner, non-porous, inner region. The films are mostcommonly formed in chromic, oxalic,phosphoric and sulphuric acids. The filmsformed in the last three acids containelectrolyte anions. In contrast, those formedin chromic acid contain comparatively fewchromate ions and the pore walls arefeathered. The latter films are industriallyimportant, especially for protection ofaerospace alloys. However, the use ofchromates will be restricted by impendingREACH (Registration, Evaluation,Authorisation and Restriction of Chemicals)legislation. Alternative anodizing processeshave been developed but not yet widelyadopted. Hence, interest remains in thechromic acid process.

In the present work, the effects of chromicoxide purity on the anodizing of aluminiumand AA2024-T3 aluminium alloy have beenexamined. Anodizing was carried out at 100V in 0.4 mol dm-3 chromic acid at 313 K,using reagent grade chemicals supplied byFisher Chemical and Acros Organics. The respective electrolytes, designatedHSCA and LSCA, contained 12.6 and ≤0.5 ppm sulphur.

Figure 1 shows that the steady currentdensity was reduced by a factor of ~1.8during anodizing in HSCA. Cross-sections offilms formed in HSCA from 15 to 360 sreveal the film development (Figure 2).Elemental maps reveal sulphur distributedpart way through the pore walls and to adepth of ~70% of the barrier layerthickness (Figure 3), where the atomic ratioof S:Al was ~0.02. Similar filmmorphologies and elemental maps wereobtained for LSCA films, but no sulphur wasdetected. Figure 4 compares cross-sections

of specimens that were anodized in LSCAand HSCA. The respective film thicknessesand the charges passed during anodizingindicated that the volume expansions onconverting the aluminium to oxide are~0.99 and 1.23 respectively. Figure 5 showsscanning electron micrographs of specimensafter chemical stripping of the films formedfor 360 s in LSCA and HSCA. Both surfacesreveal irregularly ordered cells of varioussizes and shapes. The average cell diametersare 137 and 214 nm respectively,corresponding to ratios of ~1.4 and 2.1 nmV-1. The ratio for the HSCA specimen issignificantly lower than the usual value forporous anodic alumina, namely ~2.5 nm V-1. Further, the efficiencies of growth film,calculated from the oxygen contents of thefilms, determined by nuclear reactionanalysis, and the charge passed through the cell, were ~0.6 and 0.5 in HSCA andLSCA respectively.

Effects of Sulphur Impurity in Chromic Acid Anodizing of AluminiumP. SkeldonLATEST2, School of materialsThe university of manchester

Fig. 1 The dependence of the current density on timeduring anodizing of aluminium at 100 V in 0.4 mol dm-3 chromic acid electrolyte at 313 K. Curve (1) lowsulphur electrolyte (LSCA). Curve (2) high sulphurelectrolyte (HSCA).

Fig. 2 Bright field transmission electron micrographs of cross-sectionsof aluminium anodized for (a) 15 s, (b) 30 s, (c) 90 s, (d) 180 s and (e)360 s at 100 V in 0.4 mol dm-3 high sulphur chromic acid electrolyte(HSCA) at 313 K.

The principal findings of the study are thatthe incorporation of sulphur species into thefilms decreases the current density duringfilm growth and reduces the pore size.Further, the volume expansion factor andthe efficiency of film growth are increased.The contrasts between the film growth inLSCA and HSCA indicate an altered growthmechanism, possibly involving influences ofthe sulphur on the transport numbers of

Al3+ and O2-, the magnitude and distributionof stress, the density of the film materialand the sites of new oxide growth. Inprevious work, the displacement of anarsenic tracer suggested that major poresmay develop by inward transport of filmmaterial, which fills the volume created bythe oxidation of the aluminium. Further,stress measurements on films have revealeda high compressive stress at the

film/electrolyte interface, which has beenattributed to incorporated electrolyteanions. The stress has been proposed to cause oxide flow in the film. Sulphateions may possibly generate increasedcompressive stress and promote oxide flowin the present films. From a practical pointof view, the sulphur impurity clearly has asignificant on the film morphology, which isan important factor in adhesion of paint.

Fig. 3 (a) High angle annular dark field transmission electron micrographand EDX elemental maps of (b) aluminium, (c) oxygen and (d) sulphur fora cross-section of aluminium anodized for 180 s at 100 V in 0.4 mol dm-3

high sulphur chromic acid electrolyte (HSCA) at 313 K.

Fig. 5 Scanning electron micrographs (secondary electrons) of the surfacesof aluminium anodized for 360 s at 100 V in (a) 0.4 mol dm-3 low sulphurchromic acid electrolyte (LSCA) and (b) 0.4 mol dm-3 high sulphur chromicacid electrolyte (HSCA) at 313 K and finally immersed inchromic/phosphoric acid to remove the anodic film.

Fig. 4 Scanning electron micrographs (backscattered electrons) of aluminiumanodized for 900 s at 100 V in 0.4 mol dm-3 chromic acid at 313 K. (a) Lowsulphur electrolyte (LSCA). (b) High sulphur electrolyte (HSCA). The insetshows the films at increased magnification.

Acknowledgements: D. Elabar - project PhD studentDr A. Baron-Wiecheć, Dr A. Němcová – PDRAs

Publications:

1. “18O tracer study of porous film growth on aluminium in phosphoric acid”, A. Baron-Wiechec, J. J. Ganem, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompsonand I. C. Vickridge, Journal of the Electrochemical Society, 157, 399-407, DOI: 10.1179/136217109X12590746472616 (2010).

2. “Role of oxide stress in the initial growth of self-organized porous aluminumoxide”, Ö. Çapraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert,Electrochimica Acta, 167, 404-411, DOI: 10.1016/j.electacta.2015.03.017 (2015).

3. “Factors controlling stress generation during the initial growth of porous anodic aluminium oxide”, O. Capraz, P. Shrotriya, P. Skeldon, G. E. Thompsonand K. R. Hebert, Electrochimica Acta,159, 16-22, DOI: 10.1016/j.electacta.2015.01.183 (2015).

Shot peen forming is a dieless processperformed at room temperature which hasbeen widely used to form various aircraftcomponents. Shot peening usually producesspherically-shaped dents (Figure 1) on thepeened component after small, round steelshots impact the surface of the work piece,resulting in stretching of the material in thenear-surface region and local plasticdeformation that result in residualcompressive stress. The compressive stressinduces a convex curvature on the peenedside. In order to achieve weight reductionand improved service life, integratedconstruction panels are employed as mainlyload-bearing components in wings or thefuselage of large aircraft. Due to the overallsize and the complex curves of the largepanels, large size shots are used to improvethe efficiency of shot peen forming.

In the present study, the microstructureevolution in the near-surface layer inducedby a shot peen forming process isinvestigated. Due to the use of large shots,deep dents are generated on the surface ofthe alloy and defects, such as microcracks,may develop around the dents. The fatiguelife of the formed panels may be influencedby such defects. Thus, it is essential todetermine the defect distribution aroundthe dents. The objective of the investigationis to understand the effect of processingparameters on the microstructure in thenear-surface layer and, therefore, tooptimize shot peen forming forimprovement of the mechanical propertiesof the components.

It was revealed that severe plasticdeformation and, consequently, a modifiedmicrostructure, including ultrafine grains,microcracks and redistribution ofintermetallic particles, were introduced tothe near-surface layer (Figure 2). The coarseintermetallic particles in the near-surfacelayer beneath the dents were broken upinto finer ones and redistributed during shot peen forming, which retards thepropagation of cracks and, hence, improvesthe fatigue properties of the alloy. Further,an ultrafine grained structure was producedin the near-surface layer of the dent regionon the aluminium alloy subjected to shotpeen forming (Figure 3). The co-action ofdislocation activities and dynamicrecrystallization was considered to be themain mechanism responsible for grainrefinement. The thicknesses of the refinedgrain layers increased with the increasing air pressure.

Impact of Shot Peening Forming on SurfaceIntegrity of Aluminum Alloys x. Zhou, g. E. Thompson, P. gai LATEST2, School of materialsThe university of manchester

Fig. 1 Optical image of the alloy surface after shotpeen forming.

Fig. 3 Transmission electron micrograph of a crosssection of the near-surface region at the centre ofa dent, revealing an altered microstructurecharacterized by ultrafine grains.

Fig. 2 3D X-ray volume reconstruction of a denton the surface of the alloy peened at 0.5 MPa.

A

B

Acknowledgements: This LATEST2 project was performed with support from BAMTRI

Publications:P. Gai, Y. Zeng, X. Zhou, G. E. Thompson. Microstructure Evolution in theNear-Surface Layer of AA2024 Aluminum Alloy during Shot Peen Forming,submitted to Acta Materialia.

Porous anodic films are of great importanceto the protection of aluminium alloysagainst corrosion and wear. The films arecomposed of amorphous aluminapermeated by fine, cylindrical pores thatextend from the film surface almost to themetal substrate. A much thinner, non-porous barrier layer separates the poresfrom the metal, as shown in the example ofa transmission electron micrograph of aporous film that was formed in aphosphoric acid electrolyte, presented inFigure 1. Over the last fifty years, thegrowth of the films and the formation ofthe pores have usually been explained by afield-assisted dissolution model. In thismodel, the anodic alumina is formed at themetal/film interface due to migration of O2-

ions across the barrier layer. The migrationtakes place under a high electric field at thebarrier layer, which is established by theexternal power supply in the electrolytic cell.At the same time that the oxide is formed,dissolution occurs at the pore base, suchthat the barrier layer remains of constantthickness. The dissolution is vastly

accelerated in comparison with the usualchemical dissolution of the film in theelectrolyte, which is attributed to the effectof the electric field at the pore base.

There has been a resurgence of interest inporous anodic films, partly due to theinterest in potential applications innanotechnology, but also for thedevelopment of new processes that caneliminate the need for anodizing in chromicacid, which is an often favoured process foraerospace applications, but which is nowunder legislative pressure due toenvironmental and health reasons. Withinthe LATEST Portfolio Partnership andLATEST2 programmes, alternative anodizingprocesses have been investigated in detail,coupled with fundamental research into thegrowth mechanism of the films. The latterhas led to a re-evaluation of the mechanismof pore formation. Firstly, using tungstentracers, it was shown that the pore growthinvolves flow of oxide within the barrierlayer, with field-assisted dissolution having a minor or negligible role under manyconditions of film growth. Thus, as newoxide is added at the base of the barrierlayer, oxide within the barrier layer ispushed toward the pore walls due to thestresses associated with the film growth.The oxide is made plastic due to the ionictransport processes within the barrier layerthat involve migration of both Al3+ and O2- ions.

In more recent work, attention has beendirected toward the initiation of pores andfor this purpose a new tracer approach wasdeveloped using arsenic species, which donot migrate during the film growth. Thearsenic is introduced into the film by a firststage of anodizing in sodium arsenateelectrolyte. The aluminium is then furtheranodized in a phosphoric acid electrolyte.Figure 2(a) shows transmission electronmicrographs and elemental maps of the filmat an early stage of re-anodizing, before thepores have initiated. The arsenic is revealedto be buried slightly below the film surface,and phosphorus species are also present inthe outer region of the film. Figure 2(b)shows the film at later stage, when themain pores of the film have begun to form.The arsenic map discloses a thin band ofarsenic within the barrier layer at the baseof the pore. The distribution of the arseniccan be explained by the flow of oxideinward from the original surface of the film.Figure 3 shows schematically the progressof pore development in the anodic aluminafilm, and the displacement of the arsenic bythe flow of oxide. This is the first time thatsuch a process has been demonstratedexperimentally. The new tracer approach iscurrently being further applied to examinepore formation under a range of conditionsof film growth, including anodizing inchromic acid which results in a differentpore morphology. It also has a potential forapplication to studies of pore formation inoxides other than porous alumina.

New Insights into Pore Initiationin Anodic AluminaA. Baron-wiecheć, m.g. Burke, T. hashimoto, h. Liu, P. Skeldon, g. E. ThompsonLATEST2, School of materials, The university of manchester

Fig. 1 Transmission electron micrographs of aporous film formed in phosphoric acid on athin layer of sputtering-deposited aluminium.(a) The original aluminium layer on top of an amorphous layer of anodic alumina. (b) The porous film.

Fig. 3 Schematic diagrams of the formation of anodicfilms on aluminium. (a) Barrier film formed to 60 V at 5mA cm-2 in 0.1 mol dm-3 sodium arsenate at 296 K,showing incorporation of arsenic species. (b) Barrier filmformed after re-anodizing the specimen depicted in (a)for ~15 s at 110 V in 0.4 mol dm-3 phosphoric acid at296 K, showing the burial of the arsenic. (c) Nucleationand growth of incipient pores and nucleation of a majorpore in the film of (b) following further anodizing in thephosphoric acid. (d) Growth of the major pore. Arsenicspecies are retained in the film and transported inwardby plasticized film.

Fig. 2 High angle annular dark field scanning transmissionelectron micrographs and energy-dispersive X-ray SDD spectrumimages of arsenic and phosphorus obtained from a cross-sectioned specimen of aluminium following anodizing to 60 V at5 mA cm-2 in 0.1 mol. dm-3 sodium arsenate electrolyte at 296 Kand re-anodizing at 110 V in 0.4 mol dm-3 phosphoric acidelectrolyte at 296 K for (a) 15 s and (b) 180 s.

Publications:1. “Volume expansion factor and growth efficiency of anodic alumina formed in sulphuric acid”, F. Zhou, A. K. M. Al-Zenati, A. Baron-Wiechec, M. Curioni, S. Garcia-Vergara, H. Habazaki, P. Skeldon, G. E. Thompson, Journal of the Electrochemical Society, 158 (6), C202-C214, DOI: 10.1149/1.3578028 (2011).

2. “Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in afluoride/glycerol/water electrolyte”, A. Nemcová, I. Kubena, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid State Electrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

3. “Tracer study of pore initiation in anodic alumina formed in phosphoric acid”, A. Baron-Wiechec, M. G. Burke,T. Hashimoto, H. Liu, P. Skeldon, G. E. Thompson, H. Habazaki, J. Ganem, and I. C. Vickridge, Electrochimica Acta, 113, 302-312, DOI: 10.1016/j.electacta.2013.09.060 (2013).

The use of multi-material components israpidly increasing in modern designs inorder to optimize performance and reduceweight. If these are subject to corrosiveenvironments, protection schemes may berequired to ensure durability of the product.In the case of light metals, protectionusually requires application of conversioncoatings, anodic coatings and paints as partof a coating system. However, conversionand anodic treatments are usually metal-specific, i.e. designed for application toaluminium, magnesium or titanium parts,and hence are not suited individually totreatment of a mixed-metal component in asingle treatment process. However, plasmaelectrolytic oxidation offers a potential toovercome this difficulty. Plasma electrolyticoxidation involves polarization of a metal ata high potential in an aqueous electrolyte,usually under AC or pulsed DC conditions.The high potential results in numerous,short-lived discharges on the treatedsurface, where coating material is formedthrough a combination of anodic oxidation,thermal oxidation, thermolysis and plasma-chemical processes. The mechanism of

coating growth is not well-understood,since the discharges are small and havelifetimes often of the order ofmicroseconds, making it difficult to probethe formation mechanism by conventionalapproaches. Nevertheless, coatings of up toseveral hundred microns thickness arereadily formed in suitable electrolytes thatare regarded as environmentally-friendlyand safe to handle. Further, the coatingscan provide excellent wear resistance due to the formation of high-temperature,crystalline oxide phases, and can alsoprovide corrosion protection; for the lastcase, this may require a sealing treatment orpaint top-coat since the coatings containporosity. Many studies are available in theliterature on the formation of coatings onaluminium, magnesium and titanium andtheir respective alloys, usually usingdifferent compositions of the electrolyte anddifferent electrical regimes. However, onlyone study has addressed the applicability ofthe process to treatment of mixed-metalsystems. Thus, within the LATEST2programme, investigations have beencarried out on the treatment of mixed-metalsystems consisting of a combination ofeither aluminium and AA 7075-T6aluminium alloy or of ZE41 magnesium alloyand AA 7075-T6 aluminium. These haveshown the possibility of successfully formingthick coating on both combinations ofmetals. The work utilized an alkaline

electrolyte and an AC electrical regime, withvarious RMS current densities applied. A keyobservation was the requirement to selectan appropriate current density to achievesimilar thicknesses of coating on the metalcombination. Clearly, due to the dissimilarcompositions of the metals, the details ofthe discharge conditions and the coatingcompositions differ between the twometals. Consequently, the current flow tothe two parts is not stable during thecoating formation as each of the coupledmetals presents a different and varyingresistance as the coating builds in thickness,as shown in Figure 1. If an inappropriatecurrent density is employed the currentsmay diverge, such that large differences inthe coating thickness result on the treatedmetals. However, with proper selection ofthe current, the current flow to each metalcan be maintained at a similar level, suchthat coatings can be formed of similarmorphology and thickness to those on theindividually treated metals, as shown inFigure 2. Thus, the work has demonstratedthe potential suitability of plasmaelectrolytic oxidation for the treatment ofmixed light alloys. However, furtherinvestigation is required to ascertain thegeneral applicability of the approach, forinstance to combinations with titanium, totreatments under voltage rather thancurrent control and to combined metalswith different area ratios.

Plasma Electrolytic Oxidation of Coupled Light MetalsA. Baron-wiecheć, P. Skeldon, m. curioni, g. E. Thompson LATEST2, School of materials, The university of manchester

Fig. 1 Current density responses of AA7075 alloy/ZE41alloy couples oxidized in sodium phosphate/sodiumsilicate electrolyte at 150, 525 and 780 mA cm-2.

Fig. 2 Cross-sections of coatings formed on the coupled AA7075/ZE41 substrates at(a,b) 150 mA cm-2 and (c,d) 525 mA cm-2. (e,f) Coatings formed on the respectiveindividually-oxidized alloys.

Acknowledgements: The authors are grateful to the European Community for financial assistance within the Integrating Activity“Support of Public and Industrial Research Using Ion Beam Technology (SPIRIT)”, under EC contract no.227012. In addition, they wish to acknowledge the support of the European Community's SeventhFramework Programme FP7/2007-2013 through the award of a Marie Curie Fellowship to ABW under grant agreement No PIEF-GA-2008-219913.

Publications:1. “Plasma electrolytic oxidation of coupled light metals”, A. Baron-Wiechec, M. Curioni, R. Arrabal, E. Matykina, P. Skeldon and G. E. Thompson, Transactions of the Institute of Metal Finishing, 91 (2), 107-112,DOI: 10.1179/0020296712Z.00000000083 (2013).

There is general agreement that industrialaccelerated corrosion tests such as SaltSpray Test (SST) and others are not alwaysadequate to evaluate real-life performance.Electrochemical tests, more common inAcademia, rely on measuring the responsedue to an externally applied voltage orcurrent of an immersed corroding surface.They are fast and provide fundamentalinformation on the corrosion processes butit is debated if they are representative of thereal-life behaviour due to the electricalperturbation of the corroding surface.Further, they are generally not standardizedand difficult to standardize, since theoptimum test parameters depend on the material-environment combination;optimization and interpretation requires a well-trained operator.

Electrochemical Noise Analysis is uniqueamong the electrochemical techniquesbecause it does not require the applicationof probing signal to the corroding surfaces.In practice, two nominally identicalspecimens are immersed in a test solutionand electrically connected through anexternal circuit. As a result of corrosion on the surfaces, current and potentialfluctuations are detected and recorded. The theory behind the interpretation of the electrochemical noise signal is wellestablished, but relatively complex. For thisreason, a specific software package hasbeen recently developed and distributedonline (Figure 1). The package requiresminimal user knowledge and estimateselectrode impedance (inversely proportionalto corrosion rate), average charge(proportional to volume of materialcorroded) and frequency of corrosionevents, as a function of exposure time.

Data obtained from electrochemical noisemeasurements are intrinsicallyrepresentative of a freely corroding systembecause no probing signal is applied.Further, the use of ready-made software toextract relevant, time-dependent, corrosion-related quantities, does not require detailedunderstanding of the underlying theory (Figure 2). For these reasons, the method isan ideal candidate to be standardized (bystandardizing the test environment) and to provide simultaneously quantitative fundamental and practical performance data.

Being an immersion test, as an addedbenefit, the surface of the specimens can be imaged in real time and image-analysis techniques and acceleratedfootages can be used to highlight thedetails of corrosion initiation andpropagation (Figure 3). The two combinedapproaches, automated electrochemicalnoise analysis and associated surfaceimaging provide a new intuitive, low costand robust tool for the comparativeevaluation of the corrosion performance ofprotective treatments, inhibitors and paints.A stand alone cabinet, capable ofsimultaneously recording and analysing theelectrochemical noise signal and the surfaceappearance of the corroding specimens hasbeen recently developed. Direct comparisonof images and time-lapse video allows arapid identification of the best candidatetreatment between competing solutions.Consideration of the values of low-frequency noise impedance providesquantitative estimation of the anticorrosionperformance. Once finalized andcommercially available, it will be a powerfultool for both fundamental and appliedcorrosion studies, enabling reliableinformation to be obtained withoutrequiring a highly trained operator.

Electrochemical TestingCoupled with Real Time ImagingProvides a New Tool forPractical Assessment ofAnticorrosion Performancem. curioni and g. E. ThompsonLATEST2, School of materials The university of manchester

Fig. 3 Images acquired during corrosion of ZE41 magnesium alloy supportingoxide coatings obtained by plasma electrolytic oxidation; a) 10 mA and b)20 mA for 10 min. Red arrows indicate the first sign of coating failure (4hand 12h respectively), corrosive electrolyte: 3.5% NaCl.

Fig. 2 Time evolution of the low-frequency noiseimpedance for two ZE41 magnesium alloy specimenssupporting oxide coatings obtained by plasmaelectrolytic oxidation; a) 10 mA and b) 20 mA for 10min, corrosive electrolyte: 3.5% NaCl. High values ofimpedance indicate low corrosion rates, low values ofimpedance indicate that corrosion is propagating, rapiddecrease indicates corrosion initiation. Lines are intendedas a guide to the eye.

Fig. 1 Homepage of the websitewhere the electrochemical noiseanalysis software can be downloaded(www.electrochemicalnoise.com)

Publications:1. “Interpretation of electrochemical noise generated by multiple electrodes”, M. Curioni, R.A. Cottis and G. E. Thompson, Corrosion, 69, 158, DOI: 10.5006/0701 (2013).

2. “An alternative to the use of a zeroresistance ammeter for electrochemicalnoise measurement: Theoretical analysis,experimental validation and evaluationof electrodes asymmetry”, M. Curioni, A. C. Balaskas and G. E. Thompson,Corrosion Science, 77, 281-291,DOI:10.1016/j.corsci.2013.08.014 (2013).

3. "Application of electrochemical noise analysis to corroding aluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, In press, Surface andInterface Analysis, 45 (10), 1564-1569,DOI: 10.1002/sia.5173 (2013).

4. “Reliability of the estimation ofpolarization resistance of corrodingelectrodes by electrochemical noiseanalysis: Effects of electrode asymmetry”,M. Curioni, P. Skeldon and G. E. Thompson, Electrochimica Acta, 105, 642-653, DOI: 10.1016/j.electacta.2013.04.119(2013).

Magnesium alloys are of great value forengineering applications due to their lowdensity and high strength-to-weight ratio. A major deficiency is their low corrosionresistance when exposed to aqueous andhumid environments. A thoroughunderstanding of the influence of alloyingelements/impurity on the corrosionbehaviour of magnesium alloys would allowtailoring the microstructure to achievebetter corrosion resistance and, would alsohelp in the development of recyclablemagnesium alloys, to cut the high cost forthe primary magnesium production.

The distribution of iron impurities, has been successfully detected in corrosionproducts surrounding Fe-rich particlesduring short immersion in distilled water(Figure 1). It is found that before theinitiation of localized corrosion, the Fe-richparticles are the main sites for the cathodicreaction; during the corrosion propagation,the Fe-rich particles can act as cathodesonly when they are still attached to the Mgmatrix. However, they are oxidized oncethey are detached from Mg matrix and,consequently, lose their cathodic activity.

The in situ monitoring of corrosionpropagation has been successfully achievedusing SVET to determine the currentdistribution on Mg surfaces followingimmersion in 3.5wt.% NaCl solution.Generally, the local breakdown of thesurface film occurred after 5-10 minimmersion. When the anodic activity swept across almost the entire surface,strong localized corrosion occurred at some sites where a strong anodic currentwas detected.

Understanding the Influence of Alloying Elements/Impurity on Corrosion Property of Magnesium Alloysx. ZhouLATEST2, School of materialsThe university of manchester

Fig. 1 Scanning electron micrographsof Mg after immersion in distilledwater, showing the distribution of Fe-rich particles in Mg.

Fig. 2 Distribution of currentdensity on Mg surface duringimmersion in 3.5wt.% NaClsolution. The blue and red coloursrepresent the anodic and cathodiccurrents respectively.

From the local initiation sites, the corrosionpropagated radially and laterally over thesurface, leaving a grey network of filamentsbehind (propagation stage I). Once thesurface has been consumed in this firststage, the corrosion propagation changedto a more localised attack (propagationstage II).

Microscopic examination of the twocorrosion propagation stages is presented inFigure 3. The filaments developed duringstage I are several microns in width and areconfined within the near-surface region,with a maximum depth of less than 10 µm.During stage II, however, severe localisedcorrosion developed into the bulk materialup to hundreds of micrometres.

TEM was employed to investigate cathodicsurface activation phenomenon duringcorrosion propagation. The transmissionelectron micrograph in Figure 4 clearlyshows the presence of an enriched layerwhich is located between the corrosionproduct and the intact alloy. CorrespondingEDX maps reveal that this layer is enrichedin zinc. As zinc is cathodic, with respect tothe matrix, the zinc-enriched layer canenhance cathodic activity when in contactwith the electrolyte. The findings explainspecific corrosion phenomena ofmagnesium, such as the so called negative difference effect and the cathodic surface activation.

Acknowledgements:Heike M. Krebs, Juliawati Alias – project PhD Students; Teruo Hashimoto – Experimental OfficerDr Sergiu P. Albu, Dr L Yang, Dr S Pawar – PDRA.

Collaborators: Magnesium Elektron, Brunel University

Publications:1. “Corrosion behaviour of pure magnesium with low impurity content but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou, M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

2. “Investigation of the microstructure and the influence of iron on the formation of Al8Mn5 particles in twin roll cast AZ31 magnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson and T. Hashimoto, Journal of Alloys and Compounds, 628, 195-198, DOI: 10.1016/j.jallcom.2014.12.028 (2015).

3. “Effect of traces of silicon on the formation of Fe-rich particles in pure magnesium and the corrosion susceptibility of magnesium”, L. Yang, X. Zhou, S. M Liang, R. Schmid-Fetzer, Z. Fan and G. Scamans, Journal of Alloys and Compounds, 619, 396-400, DOI: 10.1016/j.jallcom.2014.09.040 (2015).

4. “Corrosion behaviour of pure magnesium with low impurity content but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou,M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

Fig. 3 Secondary electron micrographs of AZ31 alloy after corrosion: (a) the alloy surface after removal ofcorrosion product, the regions of the two different corrosion propagation stages are separated by the white,dashed line; (b) cross section showing grain boundary attack and preferred crystallographic pitting, taking placesimultaneously; (c) a cross section revealing the corrosion propagation under the Mg(OH)2 outer layer.

Fig. 4 Transmission electron micrographs of AZ31 alloy after corrosion: (a) BF image showing the presence of alayer at the corrosion product/alloy interface; (b) HAADF image of a representative region; (c) corresponding EDX maps showing a interfacial layer enriched with zinc.

The use of magnesium alloys is potentiallyattractive for many applications owing totheir light weight. However, surfacetreatment is often required in order toprovide the requisite corrosion protection.Electrolytic processes, such as anodizing andplasma electrolytic oxidation, are commonlyemployed, and a variety of processes isavailable that produce relatively thick,porous coatings under dielectricbreakdown, which are generally used aspart of a coating system. Films formed inthe absence of dielectric breakdown arealso being investigated. However, despitethe significant research into the anodizingof magnesium, the understanding of thefilm growth mechanisms is much lessdeveloped in comparison with other lightmetals. Mechanistic investigations of filmgrowth are made easier when the films areof uniform thickness and relativelyunreactive in the electrolyte. Such films haverecently been formed using afluoride/glycol/water electrolyte.

In the present study, the formation of thefilms on a cast Mg-Zn-RE alloy, supplied byMagnesium Elektron Ltd, with composition3.2 % Nd, 0.8 % Zr, 0.7 % Zn, 0.2 % Gd,bal. Mg was investigated. The alloy wasanodized using a glycerol-based electrolytecontaining 0.35 M ammonium fluoride and 5 vol.% of water at 293 K. Themicrostructure of the alloy, shown in Figure1, reveals a discontinuous Mg-Zn-RE phase at grain boundaries and clusters ofzirconium-rich particles.

Figure 2 shows a bright field transmissionelectron micrograph of an anodic filmformed above the alloy matrix and the Mg-Zn-RE phase. The light band arrowed is due to the incorporation of theoxide/hydroxide film formed on the alloybefore the start of anodizing that acts as animmobile marker. The film is thicker abovethe Mg-Zn-RE phase than above the matrix, with respective formation ratios of ~2.0 nm V-1 and ~1.2 nm V-1. Further,the light band is located at a depth of ~0.1of the film thickness, compared with ~0.5 inthe film above the matrix, indicating agreater contribution of cation transport tofilm growth above the matrix. A thinnerlight band is also present near the centre ofthe film formed above the second phase.Ion beam analysis revealed that the band

separates an outer region, where bothfluorine and oxygen are present, and aninner region, where oxygen is depleted,indicating that oxygen migrates inwardmore slowly than fluorine. Neodymium and zinc are distributed throughout thethickness of the film, and zinc is enriched in the alloy at the alloy/film interface.Electron diffraction showed that the films are nanocrystalline and contain MgO and MgF2.

Anodic Film Formation on a Magnesium Alloy Using a Glycerol-based ElectrolyteP. SkeldonLATEST2, School of materialsThe university of manchester

Fig. 2 Transmission electronmicrograph (bright field) and EDXelemental maps for the Mg-Zn-RE

alloy following anodizing in aglycerol-fluoride electrolyte.

Fig. 1 Scanning electron micrograph (backscatteredelectrons) of the microstructure of the Mg-Zn-RE alloy.

The anodizing process oxidizes secondphase particles, locally modifying the filmcomposition. Figure 3 shows a bright fieldimage of the matrix, where two needle-likeparticles, which possibly consist of theZr2Zn3 phase, have been partly oxidized.Figure 4 shows oxidation of plate-like zinc- and zirconium-rich particles, resultingin zinc- and zirconium-rich material in theinner and outer regions of the film.

The efficiency of anodizing is close to 100 %, as calculated from the ratio of thecharges due to the cations in the films andthe charges passed though the anodizing

cell, which indicates negligible loss ofspecies to the electrolyte. Studies ofcrystalline anodic oxide films have generallyindicated that ionic transport occurs mostlyby migration of oxygen species along short-circuit paths. The present films arestrikingly different, since cations and anionshave significant mobility in the films. Theenrichment of zinc in a thin alloy layerimmediately beneath the anodic film is alsofound in Al-Zn alloys and has been relatedto the less negative Gibbs free energy perequivalent for formation of zinc oxide incomparison with that for formation of

aluminium oxide. Future work willinvestigate further the present type of filmsin order to develop a deeper understandingof the enrichment of alloying elements inthe alloy and the ionic transport processesin the film, as well as their corrosionprotection properties.

Fig. 3 Transmission electronmicrograph (bright field) andEDX elemental maps for theMg-Zn-RE alloy followinganodizing in a glycerol-fluorideelectrolyte.

Fig. 4 Transmission electron micrograph (bright field) of the Mg-Zn-RE alloy following anodizing in a glycerol-fluoride electrolyte.

Acknowledgements: Dr A. Němcová – PDRADr I. Kuběna – CEITEC IPM, Czech RepublicDr M. Šmíd – Institute of Physics of Materials, AS CR, Czech Republic

Publications:1. “Formation of barrier-type anodic films on sputteringdeposited Al-Ti alloys”, V.C. Nettikaden, A. Baron-Wiechec, P. Bailey, T. C. Q. Noakes, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3717-3721, DOI: 10.1016/j.corsci.2010.07.022 (2010).

2.“Effect of current density and behaviour of second phases in anodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/water electrolyte”, A. Nemcová, I. Kubena, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid State Electrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

3. “Growth of barrier-type anodic films on magnesium in ethylene glycol electrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, K. Shazad, E. Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, Electrochimica Acta, 179, 402 - 410, DOI: 10.1016/j.electacta.2015.02.168 (2015).

Due to a low density and high strength-to-weight ratio, magnesium alloys havebecome a commonly preferred choice forweight reduction in applications such asautomobile and computer parts, aerospacecomponents, mobile phones, sportinggoods, handheld tools and householdequipment. However, poor corrosion andwear resistance are challenges to thesuccessful use of magnesium alloys. Variouscoatings, which provide a means to avoiddirect contact of the alloy with theenvironment, are being investigated toprovide corrosion protection. Recently,electroless nickel–boron has attractedresearch interest due to its ability to providea hard, wear and corrosion resistant surface.The most difficult aspect of the electrolessprocess is often the selection of anappropriate pre-treatment, which shouldpromote a rapid initiation of the electrolesscoating and minimize corrosion of thesubstrate. Some plating technologies usehydrofluoric acid (HF) or chromiccompounds in order to protect themagnesium surface or to generate asuitably rough surface to enhance coatingadhesion. However, such chemicals arehazardous to health. Notably, little work hasbeen reported on the formation ofelectroless Ni–B on magnesium alloyswithout the use of these compounds.

Within the LATEST2 programme, incollaboration with the University ofAntioquia, procedures have been developedto coat commercial purity magnesium andthe general purpose casting alloy AZ91 by means of an electroless Ni–B process that provides a uniform, adherent andcontinuous layer without employing HF orchromic compounds. The substrates weremechanically polished with wet 100 grit SiCpaper, then grit-blasted with alumina (150μm). A final cleaning was carried out in 37g/l NaOH and 10 g/l Na3PO4 for 10 min at65 °C, followed by activation in 200 g/lNH4HF2 at room temperature for 10 min,and finally immersion in an electroless bathcontaining various additives, listed in Table1, including NH4HF2, which is easier tohandle, less volatile and cheaper than HF.

Figure 1 shows the typical nodularmorphology of the coatings, which can begrown to various thicknesses by selection of the time of immersion in the electrolessbath. Control of the fluoride concentrationin the electroless bath is important tominimize the corrosion rate of the coatedalloy, as demonstrated in Figure 2, whichdisplays the amount of hydrogen gasgenerated due to corrosion of the coatedmagnesium in sodium chloride solution. Thecoatings were formed in baths with a rangeof fluoride contents, with the resultsshowing that corrosion is accelerated by anexcess of fluoride, which is related togeneration of porosity in the coating. Withan optimized bath composition, corrosionof coated coupons following immersion insodium chloride solution is limited to theedges and corners, as shown in figure 3.Further testing has revealed an excellentwear resistance of the coatings, with agreatly reduced wear rate compared withthat of the uncoated alloy.

Formation of Electroless Nickel-Boron on Magnesium and AZ91D AlloyE. correa1, A. A. Zuleta1, L. guerra1, J. g. castaño1, F. Echeverría1, A. Baron-wiecheć2, P. Skeldon2

and g. E. Thompson2

2LATEST2, School of materials, The university of manchester

Table 1. Chemical composition of the electroless nickelplating bath and coating conditions.

Chemical composition

NiCl2·6H2O 20 g/l

NaBH4 8 g/l

CH4N2S 1 mg/l

C2H8N2 35 ml/l

NaOH 110 g/l

NH4HF2 Variable

Operating conditions

pH > 12

Temperature 80 °C

Plating time 120 min

Fig. 1 Scanning electron micrographs (backscatteredelectrons) of magnesium in (a) plan and (b) cross-sectionafter 120 min immersion in an alkaline Ni–B electrolessbath containing 5 g/l NH4HF2.

Fig. 2 Dependence of the amount of hydrogen evolvedand average weight loss rate on time of immersion in3.5 wt.% sodium chloride solution for magnesium withelectroless Ni–B coatings formed in baths containingdifferent concentrations of NH4HF2.

Fig. 3 The appearances of specimens treated in anelectroless bath containing 5 g/l before (a, b) and after(c, d) immersion in 3.5 wt.% sodium chloride solutionfor 60 minutes. Arrows point to locations of corrosion.

Acknowledgements:1Centro de Investigación, Innovación y Desarrollode Materiales—CIDEMAT, Universidad de AntioquiaUdeA, Calle 70 No. 52-21, Medellín, Colombia

The authors are grateful to “DepartamentoAdministrativo de Ciencia, Tecnología eInnovación, COLCIENCIAS”, Universidad deAntioquia for financial assistance (project111545221131 and Estrategia de Sostenibilidad2013–2014 de la Universidad de Antioquia).

Publications:1.“Effect of NH4HF2on deposition of alkalineelectroless Ni-P coatings as chromium-freepretreatments for magnesium”, A. A. Zuleta, E. Correa, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon and E. Koroleva,Corrosion Science, (55), 194-200,DOI:10.1016/j.corsci.2011.10.028 (2012).

2."Nickel–boron plating on magnesium and AZ91D alloy by a chromium-free electrolessprocess", E. Correa, A.A. Zuleta, M. Sepúlveda, L. Guerra, J.G. Castañoa, F. Echeverría, H. Liub, P. Skeldon, G.E. Thompson, Surface and Coatings Technology, 206, 13, 3088 - 3093, DOI: 10.1016/j.surfcoat.2011.12.023 (2012).

3.“Tribological behaviour of electroless Ni-Bcoatings on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L.Guerra, M. Goméz Botero, J. G. Castaño, F. Echeverría, H. Liu, P. Skeldon and G. E. Thompson, Wear 305, 115-123, DOI: 10.1016/j.wear.2013.06.004 (2013).

4.“Formation of electroless Ni-B on bifluoride-activated magnesium and AZ91Dalloy”, E. Correa, A. A. Zuleta, L. Guerra, J. G. Castaño, F. Echeverría, A. Baron-Wiechec, P. Skeldon and G. E. Thompson, Journal of the Electrochemical Society, 232, 784-794, DOI: 10.1149/2.012309jes (2013).

5. “Coating development during electroless Ni-B plating on magnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, M. A. Gómez,J. G. Castaño, F. Echeverría, H. Lui, A. Baron-Wiechec, T. Hashimoto, P. Skeldon and G. E. Thompson, Surface and CoatingsTechnology, 232, 784-794, DOI: 10.1016/j.surfcoat.2013.06.100 (2013).

I enjoyed the creative aspects of undertaking academic research.

Heike Krebs, PhD Student

Plasma electrolytic oxidation (PEO) processesare considered to be amongst the mostenvironmental-friendly surface treatmentsof aluminium, magnesium and titaniumalloys, providing good wear, thermal andcorrosion resistance. The coatings havepotential for applications in a range ofindustry sectors, including aerospace,automotive, textile processing, electroniccomponents, energy, oil and gas, leisureand sports products. Porous ceramiccoatings are formed during PEO underdielectric breakdown at the sites of micro-discharges. However, porosity in the coatings affects the coating hardness,wear resistance, corrosion resistance andthe thermal conductivity. Few studies areavailable that provide detailed, quantitative

information on the porosity. The presentstudy examines the potential of X-ray CT for characterizing a coating formed ontitanium. A Zeiss Xradia Versa 520 lab-based X-ray CT scanner, operated at an accelerating energy of 120 kV, was used to collect the results.

A rough surface, with nodular features andpores, can be seen in the X-ray CT image ofthe coating (Figure 1). Three regions in asub-volume (see red box) were selected fordetailed investigations: labelled 1, 2 and 3in Figure 2: (i) a nodule that contains anapproximately central pore (1), a nodule-free region (2), and a nodule that appearspore free (3) The physical cross-sections ofthe regions created in the FIB-SEM were

compared to the virtual cross-sectionsobserved by X-ray CT as shown in Figure 3. The locations of large pores at the coatingsurface, associated with the nodules, arevisualized in Figure 4 (a). The porosity withinthe coating is also shown in Figure 4 (b).The pores are mapped onto a map of theroughness of the titanium/coating interface.The images show a correlation between thelocations of the nodules, large pores anddepressions in the substrate. Figure 5reveals the shape of a pore in 3D; the pore within the coating connects to thecoating surface, but also exhibits a number of branches.

X-ray Computed Tomographic Investigation of the Porosity of Plasma Electrolytic Oxidation Coatingsx. Zhang, S. Aliasghari, A. němcová, T. L. Burnett, g. E. Thompson, P. Skeldon and P. J. withersLATEST2, School of materialsThe university of manchester

Fig. 1 X-ray CT data of the PEO coating rendered in3D giving an overview of the total sample imaged.

(a1) (a2) (b1) (b2) (c2)(c1)

Fig. 3 Comparison of X-ray CT virtual slices and FIB/SEM cross-sections of (a) the nodule with acentral pore, (b) the finely-porous region and (c) the nodule without a central pore.

Fig. 2 (a) X-ray CT data rendering of the chosen 3D sub-volume with distinctive regionshighlighted: 1) nodule with central pore; 2) finely porous region; 3) nodule without central pore.(b) Secondary electron SEM image showing the same region with the same features highlighted.

The study showed that X-ray CT is capableof resolving and quantifying of volumes ofat least 6 µm3. For larger pores, a goodcorrelation is obtained with the size andshape of pores observed by scanningelectron microscopy. The larger poresconstituted ~5.7% of the coating volume.The numerous cross-sections available fromvirtual slicing of the coating enable a moreaccurate assessment of the variations incoating thickness to be obtained incomparison with conventional cross-sectioning. Furthermore, the connectivity ofpores beneath nodules is revealed enablingidentification of pores that open directly tothe coating surface and ones that terminate

in the coating. A model was proposed toexplain the development of the pores byflow of molten coating due to the pressureof generated oxygen gas. The ability of X-ray CT to examine and quantify theporosity non-destructively, including itsvolume, location and interconnected nature, complements conventional electronmicroscopy of investigation. The techniqueis unique among those currently available in its ability to quantify the distribution ofporosity and its relation to the local coating morphology.

Fig. 4 X-ray CT images of (a) the coating surface with poreshighlighted and (b) additionally showing pores within the coating.

Fig. 5 (a) Contour plot showing the titanium/coating interface. The colour scaleshows the height of the substrate/coating interface, measured with respect to thelowest point of the interface. Pores have been rendered (in blue). (b) A zoom-insideshows the volcano-like pore in the black circle.

Acknowledgements:The authors thank the Engineering and Physical SciencesResearch Council for support of this work through theLATEST 2 Programme Grant (EP/H020047/1) and forfunding of the Henry Moseley X-ray Imaging Facility(EP/F007906/1 and EP/F028431/1). This work was partlyrealized in CEITEC – Central European Institute ofTechnology – with research infrastructure supported bythe project CZ.1.05/1.1.00/02.0068 financed from theEuropean Regional Development Fund.

Collaborators: I. Kuběna, Institute of Physics of Materials, AS CR, Žižkova 22, Brno, 616 62, Czech RepublicM. Šmíd, CEITEC IPM, Žižkova 22, Brno, 616 62, Czech Republic

Publications:1."X-ray computed tomographic investigation of theporosity and morphology of plasma electrolyticoxidation coatings", X. Zhang, S. Aliasghari, A. Nemcová, T. L. Burnett, I. Kubena, M. Šmíd, G. E. Thompson, P. Skeldon and P. J. Withers, ACS Applied Materials and Interfaces, in press.

2."Effects of reagent purity on plasma electrolyticoxidation of titanium in an aluminate–phosphateelectrolyte", S. Aliasghari, A. Němcová, J. Čížek, A. Gholinia, P. Skeldon, G. E. Thompson, Transactions of the IMF: The International Journal of SurfaceEngineering and Coatings, 94, 1, 32-42, DOI: 10.1080/00202967.2015.1121692 (2016).

3. "Influence of coating morphology on adhesivebonding of titanium pre-treated by plasma electrolyticoxidation", S. Aliasghari, A. Němcová, P. Skeldon, G. E. Thompson, Surface and Coatings Technology, 289, 101-109, DOI: 10.1016/j.surfcoat.2016.01.042(2016).

rESEArch ProJEcT LIST

Postdoctoral Research ProjectsAdvanced Electrochemical Methods for Evaluation of Corrosion Performance of Light Alloys

Alloy Composition/Forming and Performance

Anodic Treatments of Light Alloys (Plasma Electrolytic Oxidation/Anodizing)

Chromate Replacement in Surface Treatment of Aerospace Alloys (REACH)

Development of a Distributable Software Package for Electrochemical Noise Analysis

Development of DIC Formability Assessment Methodology and Formability of Mg Alloy Sheets

Environmentally-Friendly Anodizing/Corrosion Testing

Feasibility Study on Applicability of Advanced Electrochemical Methods for Fast Corrosion Testing of Aerosol Cans

Grain Boundary Structure of New Generation Aerospace Alloys

Improving the Performance of Extruded Aluminium

Interfacial Reaction – Modelling and Control In Friction Joining and Fusion Welds

Modelling Twin Clustering and Its Effect on Formability

Nanotomography for Understanding Sensitisation of AA5xxx Aluminium Alloys

New chrome-free coatings and inhibitors for protection of aluminium alloys

Novel Friction Joining Processes for Dissimilar Metals

Novel Friction Joining Processes for Light Alloys

Particle/Twin Interactions in Magnesium Alloys

Post Anodizing Surface Treatment for Aerospace Applications

Process Modelling of Laser Welding and Additive Manufacture

Replacement of Copper Conductors with Aluminium

Texture and Microstructure Evolution in New Generation Two-Phase Ti Alloys

Understanding the Performance of 7xxx Aluminium Alloy Forgings

Use of Selected Ionic Fluids for Finishing of Light Alloys

Electron Optics Specialist ProjectsUse of Advanced Electron optical approaches for understanding the performance of light alloys

Research Assistant ProjectsLaser welding of aluminium-lithium alloys and performing validation of such models

Repair of Armoured Vehicles - Weld Re-Processing

PhD Research ProjectsAlkali Resistant Anodic Films for Automotive Applications

Alloy Design for Large-Scale Additive Manufacturing of Aluminium Aerospace Components

A Novel Refill Friction Stir Spot Welding Approach to Joining Automotive Sheets

Anodic Films on Titanium

Anodizing of Aluminium Alloys with Rare Earth Additions

Characterisation and Simulation on Interface in Metallic Matrix Composites

Control of Cosmetic Corrosion in Aluminium Automotive Alloys

Controlling Interfacial Reaction in Aluminium to Steel Dissimilar Metal Welding

Controlling Interfacial Reaction in Titanium to Aluminium for Aerospace Applications

Conversion Coatings of Aluminium

Corrosion Control of Dissimilar Metals

Corrosion Control of Heat Exchange Alloys

Corrosion Protection by Encapsulated Inhibitors

Deformation Mechanisms in Polycrystalline Materials Studied By Diffraction Contrast Tomography

Development of Near-Surface Microstructure and Its Influence on Performance of AA3104 Aluminium Alloy

Dynamic Deformation of Magnesium Alloys

Effect of Microstructure on Corrosion Resistance and Anodizing Behaviour of AA2099T8 Alloys

Environmentally-Friendly Novel Coatings for Aerospace Alloys

Excessive Grain Coarsening In IN718 Engine Disc Forgings

Friction Joining of Aluminium to Magnesium for Light Weight Automotive Applications

Friction Stir Welding of Aluminium AA5xxx Alloys

Galvanic Corrosion of Magnesium Alloys

Hard Anodising of Aluminium Alloys

High Performance Magnesium Alloys for Aerospace Applications

High Resolution, Low Voltage Electron Imaging

Hybrid Additive Manufacture with Deformation for Large Scale Near Net Shape Manufacture of Titanium Aerospace Components

Impact of Fabrication Process on the Performance of Aerospace Aluminium Alloys

PhD Research Projects (continued)Impact of Near Surface Microstructure on the Performance of Metallic Materials

Improving Aluminium-To-Magnesium Dissimilar Welding For Lightweight Automobile Applications

Influence of Forming On Corrosion of Lean 7000 Alloys

Influences of New Electrolyte Formulations on the Anodizing Behaviour and Corrosion Protection

of Aerospace and Automotive Aluminium Alloys

Interaction of Solute and Second Phase Particle Evolution with Deformation Mechanisms in Commercial Aluminium AlloysJoint Performance and Interface Reactions in Dissimilar Aluminium to Steel Ultrasonic Spot Welding

Laser Spot Welding Dissimilar Materials

Laser Surface Processing

Laser Surface Treatment of Magnesium Alloys

Local Electrochemistry/Microstructural Revelation

Localised Corrosion of High Strength Aluminium Alloys

Mechanism of Pore Formation in Anodic Alumina

Metallurgical Performance of Hyper-Joint Pins in Composite to Metal Joining

Micro-Galvanic Control of Early Stage Etching of Flat-Rolled Aluminium Products

Microstructural Descriptors and Deformation Heterogeneity in Titanium Alloys

Microstructure Characterisation and Corrosion Properties of the Heat Affected Zones of the Automotive AA6111 Alloy

Microstructure Formability Relationships in New Generation High Strength Aluminium Automotive Alloys

Microstructure Modelling For FSW

Microstructure, Texture and Mechanical Property Evolution during Additive Manufacturing of Ti6Al4V Alloy for Aerospace Applications

Modelling of Friction Welding Processes

Modelling of the Friction Spot Welding Process

Nanotube Formation on Zirconium

Near-Surface Microstructures and their Influence on Performances of 8xxx and AA5182 Aluminium Alloys

Novel Environmental Friendly Surface Treatment for Al-Cu-Li Alloys

Optimisation of Stationary Shoulder FSW

Optimising Precipitate Shape and Habit for Strengthening in Magnesium Alloys

Particle Effects on Local Deformation, Recovery and Stored Energy in Aluminium Alloys By Measurement and Simulation

Particle Stimulated Nucleation: Deformation around Particles

Performance of Recycled Aluminium Alloys

Performance of Recycled Magnesium Alloys

Plasma Electrolytic Oxidation of Titanium

Predicting Performance of Al Armour Alloy Welds under Blast Conditions

Prediction of the Role of Defects in Fatigue Failure in Additive Manufactured SEBM Titanium Components

Process Quality Relationships in Material Addition Repair of High Value Aerospace Components

Qualification of the EBM Wire Fed Process for Manufacture with Ti6Al4V

Quantifying Microstructure Heterogeneity and its Effect on Additive Manufactured Ti6Al4V Parts

REACH Compliant Strategies for Aerospace Corrosion Prevention

Steel to Aluminium Laser Seam Welding

Stress Corrosion Cracking of Marine Alloys

Surface Integrity of Aerospace Aluminium Alloys

Surface Integrity through Tomographic Reconstruction

Surface Treatment of Titanium and its Alloys for Adhesion Promotion

Synthesis, Characterization and Corrosion Protection Performance of Hybrid Nanocomposite Coatings

The Application of Taper Rolling to the Near-Net Shape Manufacture of Aluminium

The Effect of Alloying Elements on Deformation by Twinning in Alpha Titanium

The Effect of Chromium Content on the Microstructure and Recrystallisation Behaviour of Al-Mg-Si Aluminium Alloys

The Effect of Intermetallic Precipitation on the Corrosion Resistance of Ultra High Strength Stainless Aerospace Steels

The Effect of Macrozones in Crack Initiation and Propagation in Titanium Alloys

The Impact of Warm Forming on the Microstructure and Corrosion Behaviour of Recycled Aluminium Alloys

The Origins of Reverse Loading Effects in Aero Engine Alloys

Thermo-Mechanical Processing of Advanced RE-Magnesium Alloys

Thermo-Mechanical Processing of Magnesium Alloy Elektron 43

Understanding Improved Formability in Mg Alloys Caused by Rare Earth Alloying Additions

Understanding the Effect of Microstructure on Strain Localization and Failure in 7xxx Aluminium Alloys

Understanding the Formability of Titanium

EngD Research ProjectsCharacterisation of Magnesium Castings Using X-Ray Tomography and Ultrasonic Inspection

Industrial Application of USW Aluminium Car Body Panels

Interrogation of the Manufacturing Route of Aluminium AA 1050 Alloy Used for Lithographic Application

Sol-Gel Coatings for Aerospace Alloys

MPhil Research ProjectsPEO of Magnesium

MEng Research ProjectsDissimilar Refill Spot Welding of Al to Mg

Effect of Aluminium on Quasi Static Compression Behaviour of Cross-Rolled Alpha Titanium

Effect of Paint Bake Cycle on Friction Stir Spot Welding Of Aluminium Automotive Sheet

Effect of Tin and Zirconium on Twinning in Alpha Titanium

Fatigue in the Microstructure of Titanium

Interpretation of the Effect and Thermodynamics of Copper Interfacial Enrichments on A6111 Alloys

Strain Homogeneity of Titanium Alloy With and Without Macrozones

The Effect of Zirconium on Twinning in Alpha Titanium

Visitor Research Projects3-D Imaging of Rheocast Aluminium Alloy

Anodic Oxidation of Titanium for Energy Application

Anodizing of Titanium and Titanium Alloys

Antibacterial Properties of Coatings of Silanols

Characterisation of porous anodic films formed on aluminium

Coatings on Aerospace Alloys

Collaboration of Friction Stir Welding

Comparison of Ultrasonic Welding Variants for Al/Ti-Joints by Mechanical and Microstructural Analysis

Corrosion and Protection of Mg-RE Alloy Corrosion Performance of Dissimilar Material Joints

Development, Optimization and Characterization of Environmentally Friendly Anodic Oxides and Sealing Processes for Corrosion Protection of Aerospace Alloys

Electroless Ni-P Coatings on Magnesium

Electroless Ni-B Coatings on Magnesium

Fatigue of PEO Coated Magnesium Alloy

Formation of Porous Films on Iron

Laser Shock Peening of Titanium Alloys

Low-Density Smart Polymers for Packaging Food

Nanoparticle Characterisation for Inhibition/Biocide Activity

Nanotube Film Formation on Titanium Alloy

Plasma Electrolytic Oxidation of Titanium for Photocatalysis and Energy Conversion Applications

Preparation of Electroless Nickel, Electroless Boron Nitride Particle-Reinforced Composite Coating for Improvement of the Wear and Corrosion Resistance of Aluminium Alloys

Shock Peening of Aluminium Alloys

Sol-Gel Films

Suppression of the Formation of Fayalite (Fe2SiO4) By Antioxidant Composed of Refractory Powders for High Si Steel

TEM Observation of TiO2 Films

Texture evaluation of Mg-based alloys during thermomechanical processing

The Effects of Impurities on Chromic Acid Anodizing

The Effect of Aluminium on Stress Corrosion Cracking of Mg Alloys

Training on Electrochemical Techniques for Corrosion Studies on Light

Understanding the Strength of Sharply Textured Magnesium Extrusions

PuBLIcATIonS

1. “Flow modulated ionic migration during porous oxide growthon aluminium”, M. Curioni, E. Koroleva, P. Skeldon and G. E. Thompson, Electrochemica Acta, 55, 23, 7044-7049, DOI: 10.1016/j.electacta.2010.06.088 (2010).

2. “Enrichment, incorporation and oxidation of copper duringanodizing of aluminium - copper alloys”, Surface andInterface Analysis, M. Curioni, F. Roeth, S. Garcia-Vergara, T. Hashimoto, P. Skeldon, G. E. Thompson and J. Ferguson.42, 4, 234-240, DOI: 10.1002/sia.3139 (2010).

3. “Degradation of the corrosion resistance of anodic oxide films through immersion in the anodizing electrolyte”, M. Garca-Rubio, P. Ocon, M. Curioni, G. E. Thompson, P. Skeldon, A. Lavia and I. Garca, Corrosion Science, 52, 7, 2219-2227, DOI: 10.1016/j.corsci.2010.03.004 (2010).

4. “Preferential anodic oxidation of second-phase constituentsduring anodizing of AA2024-T3 and AA7075-T6 alloys”, M. Saenz De Miera, M. Curioni, P. Skeldon and G. E. Thompson,Surface and Interface Analysis, 42, 4, 241 - 246, DOI: 10.1002/sia.3191 (2010).

5. “The behaviour of second phase particles during anodizing ofaluminium alloys”, M. Saenz de Miera, M. Curioni, P. Skeldonand G. E. Thompson, Corrosion Science, 52, 7, 2489-2497,10.1016/j.corsci.2010.03.029 (2010).

6. “Influence of applied potential on titanium oxide nanotubegrowth”, A. Valota, M. Curioni, D. Leclere, P. Skeldon, P.Falaras and G. E. Thompson, Journal of the ElectrochemicalSociety, 157, 12, 243-247, DOI: 10.1149/1.3494155 (2010).

7. “The formation of nano grain structures and accelerated room temperature theta precipitation in a severely deformed Al-4wt%Cu alloy”, Y. Huang and P. B. Prangnell,Acta Materialia, 58, 14, DOI: 10.1016/j.actamat.2009.11.008(2010).

8. “Analysis of the homogeneity of particle refinement in frictionstir processing Al-Si alloys”, C. Y. Chan, P. B. Prangnell, and S. J. Barnes, Advanced Materials Research, 6, 85-90, DOI:10.4028/www.scientific.net/AMR.89-91.85 (2010).

9. “Effects of combined Zr and Mn additions on dispersoidformation and recrystallization behaviour of AA2198 alloysheet”, D. Tsivoulas, P. B. Prangnell, C. Sigli, B. Bès, Advanced Materials Research, 89-91, 569-273, DOI: 10.4028/www.scientific.net/AMR.89-91.568 (2010).

10. “Room temperature instability of an Al-4%Cu super saturatedsolid solution in a nano-crystalline alloy produced by SPD”, Y. Huang and P. B. Prangnell, Journal of Materials Science, 45, 17, 4851, DOI: 10.1007/s10853-010-4318-6 (2010).

11. “Novel approaches to friction spot welding thin aluminiumautomotive sheet”, P. B. Prangnell, and D. Bakavos, Materials Science Forum, 638-642, 1237-1242, DOI: 10.4028/www.scientific.net/MSF.638-642.1237 (2010).

12. “Mechanisms of joint and microstructure formation in highpower ultrasonic spot welding 6111 aluminium automotivesheet”, D. Bakavos and P. B. Prangnell, Materials Science andEngineering, 527A, 15, DOI: 10.1002/9781118062111.ch85(2010).

13. “Control of weld composition when arc welding high strength aluminium alloys using multiple filler wires”, C. G. Pickin, S. W. Williams, P. B. Prangnell, C. Derry and M. Lunt, Science and Technology of Welding and Joining, 15, 6, 491-496, DOI: 10.1179/136217110X12785889549660(2010).

14. “Efficacy of active cooling for controlling residual stresses in friction stir welds”, D. G. Richards, P. B. Prangnell, P. J. Withers, S. W. Williams, T. Nagy and S. Morgan, Science and Technology of Welding and Joining, 15, 2, 156-165, DOI: 10.1179/136217109X12590746472490 (2010).

15. “Deformation twinning in Ti-6Al-4 V during low strain ratedeformation to moderate strains at room temperature”, D. G. Leo Prakash, R. Ding, R. J. Moat, I. Jones, P. J. Withers, J. Quinta da Fonseca, M. Preuss, Materials Science andEngineering: A, 527, 21-22, 5734-5744, DOI: 10.1016/j.msea.2010.05.039 (2010).

16. “Twinning in structural material with a hexagonal close-packed crystal structure”, M. Preuss, J. da Fonseca, V. Allen, D. Prakash and M. Daymond, Journal of Strain Analysis for Engineering Design, 45, 5, 377-389, DOI: 10.1243/03093247JSA624 (2010).

17. “A model relating tool torque and its associated power andspecific energy to rotation and forward speeds during frictionstir welding/processing”, S. Cui, Z. W. Chen, J. D. Robson,International Journal of Machine Tools and Manufacture, 50, 7, DOI: 10.1016/j.ijmachtools.2010.09.005 (2010).

18. “Incipient melting during friction stir processing of AZ91magnesium castings”, J. D. Robson, S. Cui, Z. W. Chen,Materials Science and Engineering: A, 527, 7299-7304, DOI: 10.1016/j.msea.2010.07.093 (2010).

19. “Modelling microstructural evolution during multiple pass friction stir welding”, J. D. Robson, P. Upadhyay and A. P. Reynolds, Science and Technology of Welding and Joining, 15, 7, 6, DOI: 10.1179/136217110X12813393169651 (2010).

20. “Model for grain evolution during friction stir welding of aluminium alloys”, J. D. Robson and L. Campbell, Science and Technology of Welding and Joining, 15, 2, 6, DOI: 10.1179/136217109X12590746472616 (2010).

21. “18O tracer study of porous film growth on aluminium in phosphoric acid”, A. Baron-Wiecheć, J. J. Ganem, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompson and I. C. Vickridge, Journal of the Electrochemical Society, 157,399-407, DOI: 10.1179/136217109X12590746472616 (2010).

22. “Anodic oxides on InAlP formed in sodium tungstateelectrolyte”, A. Suleiman, P. Skeldon, G. E. Thompson, F. Echeverria, M. J. Graham, G. I. Sproule, S. Moisa, T. Quance and H. Habazaki, Corrosion Science, 52, 595-601,DOI: 10.1016/j.corsci.2009.10.019 (2010).

23. “Effect of excimer laser surface melting on the microstructureand corrosion performance of the die cast AZ91D magnesiumalloy”, A. E. Coy, F. Viejo, F. J. Garcia-Garcia, Z. Liu, P. Skeldonand G. E. Thompson, Corrosion Science, 52, 387-397, DOI: 10.1016/j.corsci.2009.09.025 (2010).

24. “Susceptibility of rare-earth magnesium alloys tomicrogalvanic corrosion”, A. E. Coy, F. Viejo, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3896-3906, DOI: 10.1016/j.corsci.2010.08.006 (2010).

25. “Investigation of the mechanism of plasma electrolyticoxidation of aluminium using 18O tracer”, E. Matykina, A. Baron-Wiecheć., R. Arrabal, D. J. Scurr, P. Skeldon and G. E. Thompson, Corrosion Science, 52, 1070-1076, DOI: 10.1016/j.corsci.2009.11.038 (2010).

26. “Optimization of the plasma electrolytic oxidation processefficency on aluminium”, E. Matykina, R. Arrabal, P. Skeldon,G. E. Thompson, Surface and Interface Analysis, 42, 221-226,DOI: 10.1002/sia.3140 (2010).

27. “AC PEO of aluminium with porous alumina precursor films”, E. Matykina, R. Arrabal, P. Skeldon, G. E. Thompson and P. Belenguer, Surface and Coatings Technology, 205, 1668-1678, DOI: 10.1016/j.surfcoat.2010.05.014 (2010).

28. “Plasma electrolytic oxidation of a zirconium alloy under AC conditions”, E. Matykina, R. Arrabal, P. Skeldon, G. E. Thompson, P. Wang and P. Wood, Surface and Coatings Technology, 204, 2142-2151, DOI: 10.1016/j.surfcoat.2009.11.042 (2010).

29. “Anodic zirconia nanotubes: composition and growth mechanism”, F. Muratore, A. Baron-Wiecheć, T. Hashimoto, P. Skeldon and G. E. Thompson,Electrochemistry Communications, 12, 1727-1730, DOI: 10.1016/j.elecom.2010.10.007 (2010).

30. “Relationship between microstructure and corrosionperformance of the AA2050-T8 aluminium alloy after excimerlaser surface melting”, F. Viejo, A. E. Coy, Z. Liu, P. Skeldonand G. E. Thompson, Corrosion Science, 52, 2179-2187, DOI: 10.1016/j.corsci.2010.03.003 (2010).

31. “Performance of Al alloys following excimer LSM-anodizingapproaches”, F. Viejo, Z. Aburas, A. E. Coy, F. J. Garcia-Garcia,T. Hashimoto, Z. Liu, P. Skeldon and G. E. Thompson, Surfaceand Interface Analysis, 42, 252-257, DOI: 10.1002/sia.3144(2010).

32. “Influence of current density on the distribution of tungstentracers in porous anodic films”, F. Zhou, D. J. LeClere, S. J. Garcia-Vergara, P. Skeldon, G. E. Thompson and H. Habazaki, Surface and Interface Analysis, 42, 247-251, DOI: 10.1002/sia.3179 (2010).

33. “Incorporation and migration of phosphorus in anodicalumina films containing tungsten tracer layers”, F. Zhou, D. J. LeClere, S. J. Garcia-Vergara, T. Hashimoto, I. S. Molchan,H. Habazaki, P. Skeldon, and G. E. Thompson, Journal of the Electrochemical Society, 157, 437-443, DOI: 10.1149/1.3499218 (2010).

34. “Formation of porous anodic titanium oxide films in hotphosphate/glycerol electrolyte”, H. Habazaki, M. Teraoka, Y. Aoki, P. Skeldon and G. E. Thompson, Electrochimica Acta,55, 3939-3943, DOI: 10.1007/s11665-014-1262-7 (2010).

35. “Differentiation of 180- and 160-rich layers in anodic aluminafilms by glow discharge time-of-flight mass spectroscopy“, I. S. Molchan, G. E. Thompson, P. Skeldon, N. Trigoulet, A. Tempez, P. Chapon, N. Tuccitto and A. Licciardello, Surfaceand Interface Alaysis, 211-214, DOI: 10.1002/sia.3227 (2010).

36. “Impurity-driven defect generation in porous anodicalumina”, I. S. Molchan, T. V. Molchan, N. V. Gaponeneko. P. Skeldon and G. E. Thompson, ElectrochemistryCommunications, 12, 693-696, DOI: 10.1016/j.elecom.2010.03.008 (2010).

37. “Influence of pre-treatment on the surface composition of Al-Zn alloys.” M. Gentile, E. V. Koroleva, P. Skeldon, G. E. Thompson, P. Bailey and T. C. Q. Noakes, Corrosion Science, 52, 688-694, DOI: 10.1016/j.corsci.2009.10.023 (2010).

38. “Influence of grain orientation on zinc enrichment andsurface morphology of an Al-Zn alloy”, M. Gentile, E. V. Koroleva, P. Skeldon, G. E. Thompson, P. Bailey and T. C. Q. Noakes, Surface and Interface Analysis, 42, 287-292, DOI: 10.1002/sia.3147 (2010).

39. “Surface topography effects on glow discharge depthprofiling analysis.” N. Trigoulet, T. Hashimoto, I. S. Molchan, P. Skeldon, G. E. Thompson, A. Tempez and P. Chapon,Surface and Interface Analysis, 42, 328-333, DOI: 10.1002/sia.3165 (2010).

40. “Influence of water content on the growth of anodic TiO2

nanotubes in fluoride containing ethylene glycol electrolytes.”P. Schmuki, S. Berger, J. Kunze, A. Valota, D. LeClere, P. Skeldon and G. E. Thompson, Journal of the ElectrochemicalSociety, 157, C18-C23, DOI: 10.1149/1.3251338 (2010).

41. “In-vitro evaluation of cell proliferation and collagen synthesison titanium following plasma electrolytic oxidation”, P. Whiteside, E. Matykina, J. E. Gough, P. Skeldon and G. E. Thompson, Journal of Biomedical Materials Research,94A, 38-46, DOI: 10.1002/jbm.a.32664 (2010).

42. “Corrosion behaviour of a magnesium matrix composite withsilicate plasma electrolytic oxidation coating”, R. Arrabal, A. Pardo, M. C. Merino, M. Mohedano, P. Casajús, E. Matykina,P. Skeldon and G. E. Thompson, Corrosion Science, 52, 3738-3749, DOI: 10.1016/j.corsci.2010.07.024 (2010).

43. “Tracer studies relating to alloying element behaviour inporous anodic alumina formed in phosphoric acid”, S. J. Garcia-Vergara, H. Habazaki, P. Skeldon and G. E. Thompson, Electrochimica Acta, 55, 3175-3184, DOI: 10.1016/j.electacta.2010.01.038 (2010).

44. “Formation of barrier-type anodic films on sputtering-deposited Al-Ti alloys”, V.C. Nettikaden, A. Baron-Wiecheć, P. Bailey, T. C. Q. Noakes, P. Skeldon and G. E. Thompson,Corrosion Science, 52, 3717-3721, DOI: 10.1016/j.corsci.2010.07.022 (2010).

45. “Calcium and titanium release in simulated body fluid fromplasma electrolytically oxidized titanium”, Y. Zhang, E.Matykina, P. Skeldon and G. E. Thompson, Journal ofMaterials Science: Materials for Medicine, 21, 81-88, DOI: 10.1007/s10856-009-3850-x (2010).

46. “Crack-free sol-gel coatings for protection of AA1050aluminium alloy. Surface and Interface Analysis”, Z. Feng, Y. Liu, G. E. Thompson and P. Skeldon, Electrochemica Acta42, 306-310, DOI: 10.1002/sia.3162 (2010).

47. “Detection of negative ions in glow discharge massspectrometry for analysis of solid specimens.” S. Canulescu, I. Molchan, C. Tauziede, A. Tempez, J. Whitby, G. E. Thompson,P. Skeldon, P. Chapon and J. Michler, Analytical andBioanalytical Chemistry, 396 (8) 2871-2879, DOI: 10.1007/s00216-009-3366-8 (2010).

48. “Anodic film formation on binary al-mg and Al-Ti alloys innitric acid", F. Garcia-Garcia, E. Koroleva, G. E. Thompson and G. Smith, Surface and Interface Alaysis, 258-263, DOI: 10.1016/j.corsci.2011.12.035 (2010).

49. “Galvanostatic growth of nanoporous anodic films on iron inammonium fluoride-ethylene glycol electrolytes with differentwater contents”, H. Habazaki, Y. Konno, Y. Aoki, P. Skeldon,and G. E. Thompson, Journal of Physical Chemistry C, 114(44), 18853-18859, DOI: 10.1021/jp1078136 (2010).

50. “Investigation of the mechanism of plasma electrolyticoxidation of aluminium using O-18 tracer”, E. Matykina, R. Arrabal, D. Scurr, A. Baron, P. Skeldon, and G. E. Thompson, Corrosion Science, 52 (3), 1070-1076, DOI: 10.1016/j.corsci.2009.11.038 (2010).

51. “Analysis of thin impurity doped layers in anodic alumina andanodic tantala films by glow discharge time-of-flight massspectrometry”, I. Molchan, G. E. Thompson, P. Skeldon, N. Trigoulet, A. Tempez and P. Chapon, Transactions of the Institute of Metal Finishing, 88 (3), 154-157, DOI: 10.1179/174591910X12692576434617 (2010).

52. “Electrochemical techniques for practical evaluation ofcorrosion inhibitor effectiveness Performance of cerium nitrate as corrosion inhibitor for AA2024T3 alloy”, N. Rosero-Navarro, M. Curioni, R. Bingham, A. Duran, M. Aparicio, R. Cottis and G. E. Thompson, Corrosion Science,52 (10), 3356-3366, DOI: 10.1016/j.corsci.2010.06.012(2010).

53. “Performance of Al alloys following excimer LSM - anodizingapproaches”, F. Viejo, Z. Aburas, A. Coy, F. Garcia-Garcia, Z. Liu, P. Skeldon and G. E. Thompson, Surface and InterfaceAnalysis, 42 (4), 252-257, DOI: 10.1002/sia.3144 (2010).

54. “Enhanced performance of the AA2050-T8 aluminium alloyfollowing excimer laser surface melting and anodizingprocesses.” F. Viejo, A. Coy, F. Garcia-Garcia, M. Merino, Z. Liu, P. Skeldon and G. E. Thompson, Thin Solid Films, 518(10), 2722-2731, DOI: 10.1016/j.corsci.2009.09.025 (2010).

55. “Stress-enhanced growth rate of alumina scale formed onFeCrAlY alloy”, X. Zhao, F. Yang, A. Shinmi, P. Xiao, I. Molchan and G. E. Thompson, Scripta Materialia, 63 (1),117-120, DOI: 10.1016/j.scriptamat.2010.03.031 (2010).

56. “Co-operative corrosion phenomena”, A. Hughes, T.H. Muster, A. Boag, A. M. Glenn, C. Luo, X. Zhou, G. E. Thompson and D. McCulloch, Corrosion Science, 52, 665-668, DOI: 10.1016/j.corsci.2009.10.021 (2010).

57. “The ubiquitous beilby layer on aluminium surfaces”, G. M. Scamans, M. F. Frolish, W. M. Rainforth, Z. Zhou, Y. Liu,X. Zhou and G. E. Thompson, Surface and Interface Analysis, 42, 175-179, DOI: 10.1002/sia.3204 (2010).

58. “Surface structure”, G. E. Thompson, X. Zhou, MaterialsWorld, 18, 26-27, DOI: 10.1016/j.matlet.2011.06.088 (2010).

59. “Nanotomography for understanding materials degradation”,T. Hashimoto, X Zhou, C. Luo, K. Kawano, G. E. Thompson,A. E. Hughes, P. Skeldon, P. J. Withers, T. J. Marrow and A. H. Sherry, Scripta Materialia, 63, 835-838,10.1016/j.scriptamat.2010.06.031(2010).

60. “Corrosion behaviour of mechanically polished AA7075-T6aluminium alloy”,Y. Liu, A. Laurino, T. Hashimoto, X. Zhou, P. Skeldon, G. E. Thompson, G. M. Scamans, C. Blanc, W. M. Rainforth and M. F. Frolish, Surface and InterfaceAnalysis, 42, 185-188, DOI: 10.1002/sia.3136 (2010).

61. “Evolution of near-surface deformed layers during hot rolling of AA3104 aluminium alloy”, Y. Liu, M. F. Frolish, W. M. Rainforth, X. Zhou, G. E. Thompson, G. M. Scamansand J. A. Hunter, Surface and Interface Analysis, 42, 180-184,DOI: 10.4028/www.scientific.net/MSF.765.358 (2010).

62. “Effect of Al8Mn5 intermetallic particles on grain size of as-cast Mg-Al-Zn AZ91D alloy”, Y. Wang, M. Xia, Z. Fang, X Zhou and G. E. Thompson, Intermetallics,18, 1683-1689,DOI: 10.1016/j.intermet.2010.05.004 (2010).

63. “Electron and photon based spatially resolved techniques”, X. Zhou and G. E. Thompson, In B. Cottis et al (Ed.), Shreir`s Corrosion, 1405-1429 (2010)

64. “Solid-state welding of aeroengine materials”, M. Preuss andP. Threadgill, In R. Blockley and W. Shyy (Ed.), Encyclopedia onAerospace Engineering ,2355-2368 (2010)

65. “Simulation of joining operations A: Rotational welding”, P. J. Withers and M. Preuss, In D. U. Furrer and S. L. Semiatin(Ed.), ASM International Handbook, 22,432-455 (2010)

66. “New metallic materials for aeroengines - or understandingwhat we use today”, M. Preuss, Engine Yearbook. (2010)

67. “Sol-gel coatings for corrosion protection of 1050 aluminiumalloy”, Y. Liu, G. E. Thompson, P. Skeldon, ElectrochimicaActa, 55 (10), 3518-3527, DOI:10.1016/j.electacta.2010.01.074 (2010).

68. “Influence of applied potential on titanium oxide nanotubegrowth”, M. Curioni, D. J. Leclere, P. Skeldon, P. Falaras, G. E. Thompson , Journal of The Electrochemical Society, 157, 12, DOI: 10.1149/1.3494155 (2010).

69. “Material interactions in a novel pinless tool approach tofriction stir spot welding thin aluminium sheet”, Y. Chen, B. Laurent, P. B. Prangnell, Metallurgical and MaterialsTransactions A, 42, 5, 1266-1282, DOI: 10.1007/s11661-010-0514-x (2010).

70. “Simulation of rotational welding operations”, P. J. Withers,M. Preuss, ASM Handbook, Volume 22B - Metals ProcessSimulation, 432-455, (2010).

71. “Corrosion of dissimilar alloys: electrochemical noise”, M. Curioni, R. Cottis, M. Di Natale and G. E Thompson,Electrochimica Acta, 56 (18), 6318-6329, DOI:10.1016/j.electacta.2011.05.034 (2011).

72. “Electrochemical noise analysis on multiple dissimilarelectrodes: theoretical analysis”, M. Curioni, R. Cottis, M. Di Natale and G. E. Thompson, Electrochimica Acta, 56(27), 10270-10275, DOI: 10.1007/s10800-011-0295-y (2011).

73. “Reducing the energy cost of protective anodizing”, M. Curioni, P. Skeldon, J. Ferguson and G. E. Thompson,Journal of Applied Electrochemistry, 41 (7), 773-785, DOI: 10.1007/s10800-011-0295-y (2011).

74. “Glass-like CexOy sol-gel coatings for corrosion protection of aluminium and magnesium alloys” N. Rosero-Navarro, M. Curioni, Y. Castro, M. Aparicio, G. E. Thompson, A Surface and Coatings Technology, 206 (2-3), 257-264, DOI: 10.1016/j.surfcoat.2011.07.006 (2011).

75. “Volume expansion factor and growth efficiency of anodicalumina formed in sulphuric acid”, F. Zhou, A. K. M. Al-Zenati,A. Baron-Wiecheć, M. Curioni, S. Garcia-Vergara, H. Habazaki, P. Skeldon, G. E. Thompson, Journal of theElectrochemical Society, 158 (6), C202-C214, DOI: 10.1149/1.3578028 (2011).

76. “A combined approach to microstructure mapping of an Al-Li AA2199 Friction Stir Weld”, A. Steuwer, M. Dumont, J. Altenkirch, S. Birosca, A. Deschamps, P. B. Prangnell, P. J. Withers, Acta Materialia, 59 (8), 3002-3011, DOI: 10.1016/j.actamat.2011.01.040 (2011).

77. “Microstructure simulation and ballistic behaviour of weldzones in friction stir welds in high strength aluminium 7xxxplate”, A. Sullivan, C. Derry, J. D. Robson, I. Horsfall, P. B. Prangnell, Materials Science and Engineering: A, 528 (9),3409-3422, DOI: 10.1016/j.msea.2011.01.019 (2011).

78. “Material interactions in a novel pinless tool approach tofriction stir spot welding thin aluminium sheet”, D. Bakavos,Y. C. Chen, L. Babout and P. B. Prangnell, Metallurgical andMaterials Transactions A, 42A (5), 1266-1282, DOI:10.1007/s11661-010-0514-x (2011).

79. “Ultrasonic spot welding of aluminium to steel for automotiveapplications”, F. Haddadi, Y. C. Chen, and P. B. Prangnell,microstructure and optimisation, Materials Science andTechnology, 27 (3), 617-624, DOI:10.1179/026708310X520484 (2011).

80. “Effect of zinc coatings on joint properties and interfacereaction in aluminium to steel ultrasonic spot welding”,F. Haddadi, D. Strong and P. B. Prangnell, The Minerals, Metals and Materials Society (JOM), 64 (3), 407-413, DOI: 10.1007/s11837-012-0265-9 (2011).

81. “Solid state joining of metals by linear friction welding: aliterature review”, I. Bhamji, M. Preuss, P. L. Threadgill, A. C. Addison, Materials Science and Technology, 27 (1), 2-12,DOI: 10.1179/026708310X520510 (2011).

82. “Effect of precipitate shape on slip and twinning in magnesium alloys” J. D. Robson, N. Stanford, M. R. Barnett, Acta Materialia, 56 (5), 11, DOI: 10.1016/j.actamat.2010.11.060 (2011).

83. “Effect of extrusion conditions on microstructure, texture, and yield asymmetry in Mg-6Y-7Gd-0.5 wt%Zr alloy”, J. D. Robson, A. M. Twier, G. W. Lorimer, P. Rogers, Materials Science and Engineering A, 528 (24), 7247-7256,DOI: 10.1016/j.msea.2011.05.075 (2011).

84. “Application of X-ray microtomography to analysis ofcavitation in AZ61 magnesium alloy during hot deformation”,H. M. M. A. Rashed, J. D. Robson, P. S. Bate, B. Davis,Materials Science and Engineering A, 528 (6), 9, DOI: 10.1016/j.msea.2010.11.083 (2011).

85. “Particle effects on recrystallization in magnesium–manganesealloys: Particle pinning”, J. D. Robson, D. T. Henry, B. Davis.Materials Science and Engineering: A, 528 (12), 8, DOI: 10.1016/j.msea.2011.02.030 (2011).

86. “Surface topography evolution through production ofaluminium offset lithographic plates”, B. Rivett, E. V. Koroleva, F. J. Garcia-Garcia, J. Armstrong, G. E. Thompson and P. Skeldon, Wear, 270, 204-217, DOI: 10.1016/j.wear.2010.10.061 (2011).

87. “Comparison of nanotube formation on zirconium influoride/glycerol electrolytes at different anodizing potentials”F. Muratore, A. Baron-Wiecheć, A. Gholinia, T. Hashimoto, P. Skeldon and G. E. Thompson, Electrochimica Acta, 58, 389-398, DOI: 10.1016/j.electacta.2011.09.062 (2011).

88. “Growth of nanotubes on zirconium in glycerol/fluorideelectrolytes”, F. Muratore, A. Baron-Wiechéc, T. Hashimoto, A. Gholinia, P. Skeldon and G. E. Thompson, Electrochimica Acta, 56, 10500-10506, DOI: 10.1016/j.electacta.2010.12.089 (2011).

89. “Effect of ageing in the electrolyte and water on porous filmson zirconium”, F. Muratore, T. Hashimoto, P. Skeldon, G. E. Thompson, Corrosion Science, 53, 2299-2305,10.1016/j.corsci.2011.03.014 (2011).

90. “Volume expansion factor and growth efficiency of anodicalumina formed in sulphuric acid”, F. Zhou, A. K. MohamedAl-Zenati, A. Baron-Wiecheć, M. Curioni, S. J. Garcia-Vergara,H. Habazaki, P. Skeldon and G. E. Thompson, Journal of theElectrochemical Society, 158, C202-C214,10.1149/1.3578028 (2011).

91. “Depth profiling analysis of barrier-type anodic aluminiumoxide films formed on substrates of controlled roughness”, N. Trigoulet, N. Tuccitto, I. Delfanti, A. Licciardello, I. S. Molchan, P. Skeldon, G. E. Thompson, A. Tempez and P. Chapon, Surface and Interface Analysis, 43, 183-186,DOI: 10.1016/j.msea.2010.11.083 (2011).

92. “Effect of microplasma modes and electrolyte composition on micro-arc oxidation coatings on titanium for medicalapplications”, O.P. Terleeva, P. Sharkeev, A. I. Slonova, I. V. Mironov, E. V. Legostaeva, I. A. Khlusov, E. Matykina, P. Skeldon, and G. E. Thompson, Surface and CoatingsTechnology, 205, 1723-1729, DOI:10.1016/j.msea.2011.02.030 (2011).

93. “Control of morphology and surface wettability of anodicniobium oxide microcones formed in hot phosphate-glycerolelectrolytes”, S. Yang, H. Habazaki, T. Fujii, Y. Aoki, P. Skeldonand G. E. Thompson, Electrochimica Acta, 56, 7446-7453,10.1016/j.electacta.2011.07.005 (2011).

94. “Growth of porous anodic alumina films in hot

phosphate-glycerol electrolyte”, S. Yang, Y. Aoki, P. Skeldon,

G. E. Thompson and H. Habazaki, Journal of Solid-State

Electrochemistry, 15, 689-696, 10.1007/s10008-010-1141-6

(2011).

95. “Incorporation and migration of phosphorus species within

anodic films on an Al-W alloy”, S. J. Garcia-Vergara,

I. S. Molchan, F. Zhou, H. Habazaki, D. Kowalski, P. Skeldon

and G. E. Thompson, Surface and Interface Analysis, 43,

893-902, 10.1149/1.3499218 (2011).

96. “Anodic film formation on AA 2099-T8 aluminum alloy in

tartaric-sulfuric acid”, X. Zhou, Y. Ma, G. E. Thompson, M.

Curioni, T. Hashimoto, P. Skeldon, P. Thomson and M. Fowles,

Journal of the Electrochemical Society, 158, C17-C22, DOI:

10.1149/1.3523262 (2011).

97. “Discontinuities in the porous anodic film formed on

AA2099-T8 aluminium alloy”, Y. Ma, X. Zhou,

G. E. Thompson, M. Curioni, X. Zhong, E. Koroleva,

P. Skeldon, P. Thomson, M. Fowles, Corrosion Science,

53, 4141-4151, DOI: 10.1016/j.corsci.2011.08.023 (2011).

98. “Formation and composition of nanoporous films on

316L stainless steel by pulsed polarization”, J. Doff,

P. E. Archibong, G. Jones, E. V. Koroleva, P. Skeldon,

G. E. Thompson, Electrochimica Acta, 56,

DOI: 10.1016/j.electacta.2011.01.038 (2011).

99. “Effect of cooling rate and substrate thickness on

spallation of alumina scale on Fe Cr alloy”, C. Zhu, X. Zhao,

I. S. Molchan, G. E. Thompson and P. Xiao, Materials Science

and Engineering A, 528, 8687-8693,

DOI: 10.1016/j.msea.2011.08.044 (2011).

100. “Corrosion of AA2024-T3 Part III: Propagation”, A. Glenn,

T. Muster, C. Luo, X. Zhou, G. E Thompson, A. Boag, and

A. Hughes, Corrosion Science, 53 (1), 40-50,

DOI: 10.1016/j.corsci.2010.09.035 (2011).

101. “Characterisation of plasma electrolytic oxidation coatings on

Zircaloy-4 formed in different electrolytes with AC current

regime”, Y. Cheng, E. Matykina, P. Skeldon and

G. E. Thompson, Electrochimica Acta, 56, 8467-8476.

DOI: 10.1016/j.electacta.2011.07.034 (2011).

102. “Corrosion of AA2024-T3 part II: co-operative corrosion”,

A. Boag, A. M. Glenn, D. McCulloch, T. H. Muster, C. Ryan,

C. Luo, X. Zhou, G. E. Thompson and A. E. Hughes, Corrosion

Science, 53, 27-39. DOI:10.1016/j.corsci.2010.09.030 (2011).

103. “A silanol-based nanocomposite coating for protection of AA2024 aluminium alloy”, E. Gonzalez, J. Pavez, I. Azocar, J. H. Zagal, F. Melo, X. Zhou, G. E. Thompson and M. A. Páez, Electrochimica Acta, 56, 7586-7595.DOI:10.1016/j.electacta.2011.06.082 (2011).

104. “The characterisation and performance of Ce(dbp)3-inhibitedepoxy coatings”, J. Mardel, S. J. Garcia, P. A. Corrigan, T. Markley, A. E. Hughes, T. H. Muster, D. Lau, T. G. Harvey, A .M. Glenn, P. A. White, S. G. Hardin, J. M. C. Mol, C. Luo,X. Zhou, G. E. Thompson, Progress in Organic Coatings, 70,91-101, DOI:10.1016/j.porgcoat.2010.10.009 (2011).

105. “Near-surface deformed layers on rolled aluminium alloys”,X. Zhou, Y. Liu, G. E. Thompson, G. M. Scamans, P. Skeldonand J. A. Hunter, Metallurgical and Materials Transactions A,42, 1373-1385, DOI:10.1007/s11661-010-0538-2 (2011).

106. “Distribution of intermetallics in an AA2099-T8 aluminiumalloy extrusion”, Y. Ma, X. Zhou, G. E. Thompson, T. Hashimoto,P. Thomson and M. Fowles, Materials Chemistry and Physics,126, 46-53, DOI:10.1016/j.matchemphys.2010.12.014 (2011).

107. “Characterisation of magnesium oxide and its interface withα-Mg in Mg-Al based alloys”, Y. Wang, Z. Fan, X. Zhou andG. E. Thompson, Philosophical Magazine Letters, 91, 516-529,DOI:10.1080/09500839.2011.591744 (2011).

108. “On the impact of second phase particles on twinning inmagnesium alloys”, N. Stanford, J. Geng, J. D. Robson, M. R. Barnett, Magnesium Technology 2011, 289-293, DOI: 10.1002/9781118062029.ch55 (2011).

109. “Mechanisms of joint formation in ultrasonic spot weldingaluminium automotive sheet” Y. C. Chen, P. B. Prangnell, D. Bakavos, Supplemental Proceedings: Materials Processingand Energy Materials, Volume 1, 735 – 742, DOI: 10.1002/9781118062111.ch85 (2011).

110. “Control of morphology and surface wettability of anodicniobium oxide microcones formed in hot phosphate-glycerolelectrolytes”, H. Habazaki, F. Takashi, A. Yoshitaka, P. Skeldon,G. E. Thompson, S. Yang, Electrochimica Acta, 56, 22, 7446-7453, DOI: 10.1016/j.electacta.2011.07.005 (2011).

111. “In-Situ observation and modelling of intergranular cracking in polycrystalline alumina”, D. Gonzalez, M. Aswad, J. Quinta Da Fonseca, P. J. Withers, J. T. Marrow, Key Engineering Material, 465, 560-563, DOI: 10.4028/www.scientific.net/KEM.465.560 (2011).

112. “Inertia friction welding (IFW) for aerospace applications”,M.M. Attallah, M. Preuss, Welding and Joining of AerospaceMaterials, 25-74, DOI: 10.1533/9780857095169.1.25 (2011).

113. “High strength aluminium alloys: microstructure, corrosionand principles of protection”, A. E. Hughes, N. Birbilis, J. C. M. Mol, S. J. Garcia, X. Zhou and G. E. Thompson,InTech Publications, In Z. Ahmad (Ed.), 223-262 (1), DOI: 10.5772/18766 (2012).

114. “Single-step fabrication of metal nanoparticle loadedmesoporous alumina through anodizing of a commercialaluminum alloy”, Y. Ma, X. Zhou, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon, and E. Koroleva,Electrochemical and Solid-State Letters, 15 (1), E4-E6, DOI: 10.1149/2.019201esl (2012).

115. “Effect of wall thickness transitions on texture and grain structure in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A Antonysamy, P. B. Prangnell and J. Meyer, Materials Science Forum, 706 - 709, 205-2010, DOI: 10.4028/www.scientific.net/MSF.706-709.205 (2012).

116. “The effect of high strain rate deformation on intermetallicreaction during ultrasonic welding a luminium to magnesium”,A. Panteli, J. D. Robson, I Brough and P. B. Prangnell, Materials Science and Engineering A, 556, 31-42;DOI:10.1016/j.msea.2012.06.055 (2012).

117. “Interactions between zirconium and manganese dispersoid-Forming elements on their combined addition in Al-Cu-Li alloys”, D. Tsivoulas, J. D. Robson, C. Sigli, P. B. Prangnell, Acta Materialia, 60, 5245–5259. DOI:10.1016/j.actamat.2012.06.012 (2012).

118. “Microstructure and performance of a biodegradable Mg–1Ca–2Zn–1TCP composite fabricated by combinedsolidification and deformation processing”, D.-B. Liu, Y. Huang, P. B. Prangnell, Materials Letters, 82, 7-9, DOI: 10.1016/j.matlet.2012.05.035 (2012).

119. “Modelling intermetallic phase formation in dissimilar metalultrasonic welding of aluminium and magnesium alloys”, J. D. Robson, A. Panteli, P. B. Prangnell, Science andTechnology of Welding and Joining, 17, 447-453, DOI: 10.1179/1362171812Y.0000000032 (2012).

120. “Interface structure and bonding in abrasion circle friction stirspot welding: A novel approach for rapid welding aluminiumalloy to steel automotive sheet”, Y. C. Chen, A. Gholinia, P. B. Prangnell, Materials Chemistry and Physics, 134, 459-463. DOI:10.1016/j.matchemphys.2012.03.017 (2012).

121. “Optimisation of aluminium to magnesium ultrasonic spotwelding”, A. Panteli, Y. C. Chen, D. Strong, X. Zhang and P. B. Prangnell, Journal of Materials, 64 (3), 414-420,DOI:10.1007/s11837-012-0268-6 (2012).

122. “HAZ development and accelerated post-weld natural ageingultrasonic spot welding aluminium 6111-T4 automotivesheet,” Y. C. Chen, D. Bakavos, A. Gholinia, P. B. Prangnell,Acta Materialia, 60, 2816-2828. DOI:10.1016/j.actamat.2012.01.047 (2012).

123. “Influence of temperature upon the texture evolution andmechanical behaviour of Zircaloy-4”, P. Honniball, M. Preuss,J. Quinta da Fonseca, Materials Science Forum, 702-703, 834-837. DOI:10.4028/www.scientific.net/MSF.702-703.834(2012).

124. “In situ observation on the influence of β grain growth ontexture evolution during phase transformation in Ti-6A-4V”,G. C. Obasi, R. J. Moat, D. G. Leo Prakash, W. Kockelmann, J. Quinta da Fonseca and M. Preuss, Materials Science Forum,702-703, 854-857, DOI:10.4028/www.scientific.net/MSF.702-703.854 (2012).

125. “Effect of β grain growth on variant selection and texturememory effect during α → β → α phase transformation in Ti–6Al–4V”, G.C. Obasi, S. Birosca, J. Quinta da Fonseca, andM. Preuss, Acta Materialia, 60(3), 1048-1058.DOI:doi:10.1016/j.actamat.2011.10.038 (2012)

126. “Influence of lead on the microstructure and corrosionbehavior of melt-conditioned, twin-roll-cast AZ91Dmagnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson, J .D. Robson, I. Bayandorian, G. Scamans and Z. Fan,Corrosion, 68 (6), 548-556, DOI: 10.5006/i0010-9312-68-6-548 (2012).

127. “Effect of NH4HF2 on deposition of alkaline electroless Ni-Pcoatings as chromium-free pretreatments for magnesium”, A. A. Zuleta, E. Correa, G. E. Thompson, M. Curioni, T. Hashimoto, P. Skeldon and E. Koroleva, Corrosion Science,(55), 194-200, DOI:10.1016/j.corsci.2011.10.028 (2012).

128. “Effects of density and electrolyte temperature on poregeneration in anodic alumina formed in oxalic acid.” F. Zhou, A. Baron-Wiecheć, S. J. Garcia-Vergara, M. Curioni,H. Habazaki, P. Skeldon and G. E. Thompson, ElectrochimicaActa, (59), 186-195, DOI:10.1016/j.electacta.2011.10.052(2012).

129. “The impact of melt-conditioned twin roll casting on thedownstream processing of an AZ31 magnesium alloy”, I. Bayandorian, Y. Huang, Z. Fan, S. Pawar, X. Zhou and G. E. Thompson, Metallurgical and Materials Transactions, A, 43, 1035-1047, DOI:10.1007/s11661-011-1006-3 (2012).

130. “Study of localized corrosion in AA2024-T3 aluminium alloyusing electron tomography”, X. Zhou, C. Luo, T. Hashimoto,A. E. Hughes, G. E. Thompson, Corrosion Science, 58, 299-306, DOI:10.1016/j.corsci.2012.02.001 (2012).

131. “Analysis of thin and thick films”, Members of the EC EMPDASTREP Consortium, M.S. Lee (Ed.), Applied Handbook of Mass Spectrometry, Chapter 41, 943-959, DOI: 10.1002/9781118180730.ch41 (2012).

132. “Inertia friction welding for aerospace applications”, M. Attallah and M. Preuss. In M.C. Chaturvedi (Ed.), Welding and Joining of Aerospace Materials, 25-108,Cambridge: Woodhead Publishing, 25-74, DOI: 10.1533/9780857095169.1.25 (2012).

133. “Linear Friction Welding in Aerospace Engineering”, I. Bhamji, A. C. Addison, P. L Threadgill and M. Preuss, In M.C.Chaturvedi (Ed.), Welding and Joining of Aerospace Materials,384-415, Cambridge: Woodhead Publishing (2012).

134. “Characterization of MEA degradation for an open air cathodePEM fuel cell”, R. Silva, T. Hashimoto, G. E. Thompson, and C. Rangel, International Journal of Hydrogen Energy,DOI:10.1016/j.ijhydene.2011.12.110 (2012).

135. “Enrichment of alloying elements in aluminum: A scanningkelvin probe approach”, S. Garcia-Vergara, P. Skeldon, G. E. Thompson, G. Williams, and H. McMurray, Journal ofThe Electrochemical Society, 159(9), C428-C433.DOI:10.1149/2.057209jes (2012).

136. “Contamination of stainless steel in an electrospray ionizationsource”, J. Doff, D. Douce, G. Jones, E. Koroleva, P. Skeldon,and G. E. Thompson, Applied Surface Science,DOI:10.1016/j.apsusc.2012.02.014 (2012).

137. “18O distributions in porous anodic alumina by plasmaprofiling time-of-flight mass spectrometry and nuclearreaction analysis”, A. Baron Wiechec, A. Tempez, P. Skeldon,P. Chapon, and G. E. Thompson, Surface and InterfaceAnalysis, DOI:10.1002/sia.5032 (2012).

138. “Oxidation states of molybdenum in oxide films formed insulphuric acid and sodium hydroxide”, I. Okonkwo, J. Doff, A. Baron-Wieche, G. Jones, E. Koroleva, P. Skeldon, and G. E. Thompson, Thin Solid Films,DOI:10.1016/j.tsf.2012.05.031 (2012).

139. “Observations of intergranular corrosion in AA2024-T351:The influence of grain stored energy”, C. Luo, X. Zhou, G. E. Thompson, and A. Hughes, Corrosion Science,DOI:10.1016/j.corsci.2012.04.005 (2012).

140. “Ion migration and film morphologies in anodic alumina filmsformed in selenate electrolyte”, A. Baron-Wiecheć, O. Ekundayo,S. Garcia-Vergara, H. Habazaki, H. Liu, P. Skeldon, and G. E. Thompson, Journal of The Electrochemical Society,159(7), C312-C317, DOI:10.1149/2.044207jes (2012).

141. “The effect of nickel on alloy microstructure andelectrochemical behaviour of AA1050 aluminium alloy in acid and alkaline solutions”, F. Garcia-Garcia, P. Skeldon, G. E. Thompson, G. C. Smith, Electrochimica Acta,DOI:10.1016/j.electacta.2012.04.106 (2012).

142. “Plasma electrolytic oxidation and corrosion protection ofZircaloy-4”, Y. Cheng, E. Matykina, R. Arrabal, P. Skeldon, and G. E. Thompson, Surface and Coatings Technology,DOI:10.1016/j.surfcoat.2012.01.011 (2012).

143. “The influences of microdischarge types and silicate on themorphologies and phase compositions of plasma electrolyticoxidation coatings on Zircaloy-2”, Y. Cheng, F. Wu, E. Matykina, P. Skeldon, and G. E. Thompson, CorrosionScience, DOI:10.1016/j.corsci.2012.03.017 (2012).

144. “Porous anodic film formation on Al-Ti alloys in sulphuricacid”, V. Nettikaden, H. Liu, P. Skeldon, and G. E. Thompson,Corrosion Science, DOI:10.1016/j.corsci.2011.12.035 (2012).

145. “Porous anodic film growth on a Zr-W Alloy”, F. Muratore, A. Baron-Wieche, T. Hashimoto, A. Gholinia, H. Habazaki, P. Skeldon, and G. E. Thompson, Electrochemical and Solid-StateLetters, 15(5), C8-C11. DOI:10.1149/2.005206esl (2012).

146. “Simulating the galvanic coupling between S-Al2CuMg phaseparticles and the matrix of 2024 aerospace aluminium alloy”,L. Lacroix, C. Blanc, N. Pébère, G. E. Thompson, B. Tribollet,and V. Vivier, Corrosion Science, 64, 213-221, DOI: 10.1016/j.corsci.2012.07.020 (2012).

147. “Growth and field crystallisation of anodic oxide films on Ta-Nb alloys”, S. Komiyama, E. Tsuji, Y. Aoki, H. Habazaki, M. Santamaria, F. Di Quarto, P. Skeldon and G. E. Thompson.Journal of Solid State Electrochemistry, (16), 1595-1604.DOI:10.1007/s10008-011-1565-7 (2012).

148. “Formation of self-organised nanoporous anodic films on type 304 stainless steel”, K. Kure, Y. Konno, E. Tsuji, H. Shoji, P. Skeldon, G. E. Thompson and H. Habazaki,Electrochemistry Communications, (21), 1-4,DOI:10.1016/j.elecom.2012.05.003 (2012).

149. “Inhomogeneous mesoscopic honeycomb optical media for enhanced cathode- and under-X-ray luminescence”, N. V. Gaponenko, M. V. Rudeko, V. S. Pustovarov, S. V. Zvonarev,A. I. Slesarev, I. S. Mochan, G. E. Thompson and E. A. Stepanova, Journal of Applied Physics, (111), DOI: 10.1063/1.4717740 (2012).

150. “The influence of rolling temperature on texture evolutionand variant selection during α → β → α phase transformationin Ti–6Al–4V”, G.C. Obasi, S. Birosca, D.G. Leo Prakash, J. Quinta da Fonseca, M. Preuss. Acta Materialia, 60, 6013-6024, DOI: 10.1016/j.actamat.2012.07.025 (2012).

151. “Linear friction welding of aluminum to copper”, I. Bhamji,R.J. Moat, M. Preuss, P.L Threadgill, A.C. Addison and M.J. Peel, Science and Technology of Welding and Joining, 17 (4), 314-320, DOI: 10.1179/1362171812Y.0000000010(2012).

152. “Linear friction welding of aluminum to magnesium”, I. Bhamji, M. Preuss, R. J. Moat, P. L Threadgill and A. C. Addison, Science and Technology of Welding and Joining, 17 (5), 368-374 DOI: 10.1016/j.mechmat.2014.12.001 (2012).

153. “Microstructural and residual stress development due toinertia friction welding in Ti-6246”, M. M. Attallah, M. Preuss, C. Boonchareon, A. Steuwer, J. E. Daniels, D. J. Hughes, C. Dungey and G. J. Baxter, Metallurgical andMaterials Transactions A, 43 (9), 3149-3161, DOI: 10.1007/s11661-012-1116-6 (2012).

154. “In situ neutron diffraction study of texture evolution andvariant selection during the α → β → α phase transformationin Ti–6Al–4V”, G. C. Obasi, R. J. Moat, D. G. Leo Prakash, W. Kockelmann, J. Quinta da Fonseca, M. Preuss, Acta Materialia, 60 (20), 7169-7182, DOI: 10.1016/j.actamat.2012.09.026 (2012).

155. “Observations of intergranular corrosion in AA2024-T3: The influence of grain stored energy”, C. Luo, X. Zhou, A. E. Hughes, G. E. Thompson, Corrosion Science, 61, 35-44, DOI: 10.1016/j.corsci.2012.04.005 (2012).

156. “Microstructural modelling for friction stir welding of highstrength aluminum alloys”, J. D. Robson, and L. Campbell,Materials Science Forum, 706, 1008-1013, DOI: 10.4028/www.scientific.net/MSF.706-709.1008 (2012).

157. “Anodic film growth on Al-Li-Cu alloy AA2099-T8”, Y. Ma, X. Zhou, G. E Thompson, M. Curioni, P. Skeldon, X. Zhang, Z. Sun, C. Luo, Z. Tang and F. Lu, Electrochimica Acta, 80, 148-159, DOI: 10.1016/j.electacta.2012.06.126 (2012).

158. “Anodic growth of titanium oxide: Electrochemical behaviourand morphological evolution”, A. Mazzarolo, M. Curioni, A. Vicenzo, P. Skeldon and G. E. Thompson, ElectrochimicaActa, 75, 288-295, DOI: 10.1016/j.electacta.2012.04.114(2012).

159. “Formation of protective anodic oxides on aluminium by lowvoltage anodizing in sulphuric acid with cerium nitrate andtartaric acid additions”, M. Curioni, A. Zuleta, E. Correa, X. Pan, A. Baron-Wiecheć, P. Skeldon, J. Castao, F. Echeverra and G. E. Thompson, Transactions of the Institute of Metal Finishing, 90 (6), 290-297, DOI: 10.1179/0020296712Z.00000000059 (2012).

160. Effect of surface morphology changes of Ti-6Al-4V alloymodified by laser treatment on GDOES elemental depthprofiles”, I. S. Molchan, S. Marimuthu, A.Mhich, Z. Liu, T. Hashimoto, G. E. Thompson, D. Whitehead, Z. B. Wang, P. Mativenga, L. Li, C. Grafton-Reed, I. H. Leaver, S. Cheetham, and S. Dilworth, Journal of Analytical AtomicSpectrometry, 28, 150-155, DOI: 10.1039/c2ja30186e (2012).

161. “Durability and corrosion of aluminium and its alloys:overview, property space, techniques and developments”, N. L. Suliman, X. Zhou, N. Birbilis, A. E. Hughes, J. M. C. Mol,S. J. Garcia, X. Zhou, and G. E. Thompson, Aluminium Alloys,New Trends in Fabrication and Applications (ed. Z. Ahmad),Chapter 2, INTECH Publications, ISBN 980-953-307-512-4December (2012).

162. “Interfacial reaction during dissimilar joining of aluminumalloy to magnesium and titanium alloys”, A. Panteli, C. Q.Zhang, D. Baptiste, E. Cai, P. B. Prangnell, J. D. Robson,ICAA13: 13th International Conference on Aluminum Alloys,761-770, DOI: 10.1002/9781118495292.ch112 (2012).

163. “Plastic strain mapping with sub-micron resolution using digital image correlation”, J. Quinta da Fonseca, F. Di Gioacchino, Experimental Mechanics, 53, 5, 743-754,DOI: 10.1007/s11340-012-9685-2 (2012).

164. “Formation of self-organized nanoporous anodic films on type 304 stainless steel”, Y. Konno, E. Tsuji, P. Skeldon, G. E. Thompson, H. Habazaki, ElectrochemistryCommunications, 21, 04, DOI: 10.1016/j.elecom.2012.05.003(2012).

165. “Origin of streaks on anodized aluminium alloy extrusions”, Y. Ma, X. Zhou, G. E. Thompson, J-O. Nilsson, M. Gustavssonand A. Crispin, Transactions of the Institute of Metal Finishing,91, 11-16, DOI: 10.1179/0020296712Z.00000000075 (2013).

166. “Advances in X-ray diffraction contrast tomography: flexibility in the setup geometry and application to multiphasematerials”, P. Reischig, A. King, L. Nervo, N. Viganó, Y. Guilhem, W. J. Palenstijn, K. J. Batenburg, M. Preuss and W. Ludwig, Journal of Applied Crystallography, 46, 297-311, DOI: 10.1107/S0021889813002604 (2013).

167. “The effect of a paint bake treatment on joint performance infriction stir spot welding AA6111-T4 sheet using a pinlesstool”, Y. C. Chen, S.F. Liu, D. Bakavos, and P. B. Prangnell,Materials Chemistry and Physics, 141 (2-3), 768-775, DOI: 10.1016/j.matchemphys.2013.05.073 (2013).

168. “In situ observation of texture and microstructure evolution during rolling and globularization of Ti–6Al–4V”, J. L. W. Warwick, N.G. Jones, I. Bantounas, M. Preuss, D. Dye, Acta Materialia, 61 (5), 1603-1615, DOI: 10.1016/j.actamat.2012.11.037 (2013).

169. “The effect of beta grain coarsening on variant selection and texture evolution in a near-beta Ti alloy”, G. C Obasi, J. Quinta da Fonseca, D. Rugg and M. Preuss, MaterialsScience and Engineering A, 576, 272-279, DOI: 10.1016/j.msea.2013.04.018 (2013).

170. “Surface texture formed on AA2099 Al–Li–Cu alloy duringalkaline etching”, Y. Ma, X. Zhou, G. E. Thompson, P. Skeldon. (2013). Corrosion Science, 66, 292-299, DOI: 10.1016/j.corsci.2012.09.032 (2013).

171. “Reducing mechanical asymmetry in wrought magnesiumalloys”, J. D. Robson, Materials Science Forum, 765, 580-584,DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

172. “Visualisation of carbon nanoparticle distributions in polymercomposites using voltage contrast and energy contrastimaging in SEM”, Y. Liu, X. Zhou, J. Carr, C. Butler, S. Mills, J. O`Connor, E. McAlpine, T. Hashimoto, G. E. Thompson, G. Scamans, P. Howe, M. A. McCool and N. S. Malone, Polymer, 54, 330-340, DOI: 10.4028/www.scientific.net/MSF.765.580 (2013).

173. “New evidence on the role of catalase in Escherichia coli-mediated biocorrosion”, S .Baeza, N .Vejar, M. Gulppi, M. Azocar, F. Melo, A. Monsalve, J. Pinto, C. Vasquez, J. Pavez, J. H .Zagal, X. Zhou, G. E. Thompson and M. A. Páez, Corrosion Science, 67, 32-41, DOI: 10.1016/j.corsci.2012.09.047 (2013).

174. “The effectiveness of surface coatings on preventinginterfacial reaction during ultrasonic welding of aluminum to magnesium”, A. Panteli, J. D. Robson, Y. C. Chen and P. B. Prangnell, Metallurgical and Materials Transactions A, DOI: 10.1007/s11661-013-1928-z (2013).

175. “Constituent particles and dispersoids in an Al-Mn-Fe-Si alloystudied in three-dimensions by serial sectioning”, J. D. Robson,J. da Fonseca, L. Dwyer, T. Hashimoto, G. E. Thompson and N. Kamp, Materials Science Forum, 765, 451-455, DOI: 10.4028/www.scientific.net/MSF.765.451 (2013).

176. “Anodizing of aluminum in sulfuric acid/boric acid mixedelectrolyte”, L. Zhang, G. E. Thompson, M. Curioni and P. Skeldon, Journal of the Electrochemical Society, 160 (4),DOI: 10.1149/2.032306jes (2013).

177. “Plasma electrolytic oxidation of coupled light metals”, A. Baron-Wiecheć, M. Curioni, R. Arrabal, E. Matykina, P. Skeldon and G. E. Thompson, Transactions of the Instituteof Metal Finishing, 91 (2), 107-112, DOI:10.1179/0020296712Z.00000000083 (2013).

178. “Microstructural modification arising from alkaline etchingand its effect on anodizing behavior of Al-Li-Cu alloy”, Y. Ma,X. Zhou, G. E. Thompson, X Zhang, C. Luo, M. Curioni and H. Liu, Journal of the Electrochemical Society, 160 (3), C111-C118, DOI: 10.1149/2.043303jes (2013).

179. “Interpretation of electrochemical noise generated by multipleelectrodes”, M. Curioni, R.A. Cottis and G. E. Thompson,Corrosion, 69, 158, DOI: 10.5006/0701 (2013).

180. “Near-surface deformed layer and its evolution on AA3104aluminium alloy”, K. Li, X. Zhou, G. E. Thompson, J. A. Hunterand Y. Yuan, Materials Science Forum, 765, 358-362, DOI: 10.4028/www.scientific.net/MSF.765.358 (2013).

181. “Novel environmentally-friendly coatings for aerospacealloys”, J. M. Harris, X. Zhou, G. E. Thompson, P. P. Scott, X. Zhang, Z. Shi and Z. Sun, Materials Science Forum, 765,693-697, 10.4028/www.scientific.net/MSF.765.693 (2013).

182. “Analysis of molecular monolayers adsorbed on metalsurfaces by glow discharge optical emission spectrometry”, I. S. Molchan, G. E. Thompson, P. Skeldon, A. Licciardello, N. Tuccitto and A. Tempez, Journal of Analytical AtomicSpectrometry, 28, 121-126, DOI: 10.1039/c2ja30247k (2013).

183. “Microstructure and microgalvanic corrosion of an extrudedMg-Gd-Y-Zr magnesium alloy”, J. P. Li, P. Wang, Y. C. Guo, G. E. Thompson, X. Zhou, S. Zhong and T. Hashimoto,Materials Science Forum, 765, 683-687, DOI: 10.4028/www.scientific.net/MSF.765.683 (2013).

184. “Galvanic corrosion between magnesium alloys and steel”, J. Janiec-Anwar, G. E. Thompson, X. Zhou, M. Curioni, M. Turski and T. Wilks, Materials Science Forum, 765, 648-653, DOI: 10.4028/www.scientific.net/MSF.765.648 (2013).

185. “Reliability of the estimation of polarization resistance of corroding electrodes by electrochemical noise analysis:Effects of electrode asymmetry”, M. Curioni, P. Skeldon and G. E. Thompson, Electrochimica Acta, 105, 642-653, DOI: 10.1016/j.electacta.2013.04.119 (2013).

186. “3-D tomography by automated in-situ block faceultramicrotome imaging using an FEG-SEM to study complexcorrosion protective paint coatings”, A. Trueman, S. Knight, J. M. Colwell, T. Hashimoto, J. Carr, P. Skeldon and G. E. Thompson, Corrosion Science, 75, 376-385, DOI: 10.1016/j.corsci.2013.06.021 (2013).

187. “Relating grain misorientation to the corrosion behaviour of low copper 7xxx aluminium alloys”, A. Cassell, G. E. Thompson, X. Zhou, T. Hashimoto and G. Scamans,Materials Science Forum, 765, 623-628, DOI: 10.4028/www.scientific.net/MSF.765.623 (2013).

188. “Microstructure, corrosion and wear performance of plasmaelectrolytic oxidation coatings formed on Ti-6Al-4V alloy insilicate-hexametaphosphate electrolyte”, Ying-liang Cheng,Xiang-Quan Wu, Zhi-gang Xue, E. Matykina, P. Skeldon, G. E. Thompson, Surface and Coatings Technology, 217, 129-139, DOI:10.1016/j.surfcoat.2012.12.003 (2013).

189. “Extending the life of light alloy components: microstructure,corrosion, inhibition and performance assessment”,M.Curioni, A. C. Balaskas, T.Hashiomoto, A. I. Egbeolu, and G.E.Thompson, Materials Science Forum, 765, 597, DOI: 10.4028/www.scientific.net/MSF.765.597 (2013).

190. “Three dimensional imaging of light metals using serial block face scanning electron microscopy (SBFSEM)”, T. Hashimoto, G. E. Thompson, M. Curioni, X. Zhou, P. Skeldon, Materials Science Forum, 765, 501, DOI: 10.4028/www.scientific.net/MSF.765.501 (2013).

191. “Tailoring of the solid state properties of Al-Nb mixed oxides:a photoelectrochemical study”, M. Santamaria, F. Di Franco, F. Di Quarto, P. Skeldon and G. E. Thompson, Journal ofPhysical Chemistry, 117, 4201-4210, DOI: 10.1021/jp312008m (2013).

192. “Tribological behaviour of electroless Ni-B coatings onmagnesium and AZ91D alloy”, E. Correa, A. A. Zuleta,L.Guerra, M. Goméz Botero, J. G. Castaño, F. Echeverría, H. Liu, P. Skeldon and G. E. Thompson, Wear 305, 115-123,DOI: 10.1016/j.wear.2013.06.004 (2013).

193. “Formation of electroless Ni-B on bifluoride-activatedmagnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, J. G. Castaño, F. Echeverría, A. Baron-Wiechec, P. Skeldon and G. E. Thompson, Journal of the ElectrochemicalSociety, 232, 784-794, DOI: 10.1149/2.012309jes (2013).

194. “Effect of fluoride ions on plasma electrolytic oxidation of AZ61magnesium alloy”, A. Nemcová, P. Skeldon, G. E. Thompson, B. Pacal, Surface and Coatings Technology, 232, 827-838, DOI: 10.1016/j.surfcoat.2013.06.107 (2013).

195. “Coating development during electroless Ni-B plating onmagnesium and AZ91D alloy”, E. Correa, A. A. Zuleta, L. Guerra, M. A. Gómez, J. G. Castaño, F. Echeverría, H. Lui, A. Baron-Wiechec, T. Hashimoto, P. Skeldon and G. E. Thompson, Surface and Coatings Technology, 232, 784-794, DOI: 10.1016/j.surfcoat.2013.06.100 (2013).

196. “Observation of self-assembled layers of alkyl phophonic acid on aluminium using low-voltage scanning electronmicroscopy”, H. Sato, T. Fujii, E. Tsuji, Y. Aoki, K. Shimizu, P. Skeldon, G. E. Thompson and H. Habazaki, SurfaceInterface Analysis, 45 (10), 1441-1445, DOI: 10.1002/sia.5217 (2013).

197. “An alternative to the use of a zero resistance ammeter forelectrochemical noise measurement: Theoretical analysis,experimental validation and evaluation of electrodesasymmetry”, M. Curioni, A. C. Balaskas and G. E. Thompson, Corrosion Science, 77, 281-291, DOI: 10.1016/j.corsci.2013.08.014 (2013).

198. “Application of electrochemical noise analysis to corroding aluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, In press, Surface and Interface Analysis, 45 (10), 1564-1569, DOI: 10.1002/sia.5173 (2013).

199. “Revealing the 3D internal structures of aluminium and itsalloys”, T. Hashimoto, X. L. Zhong, M. Curioni, X. Zhou, P. Skeldon, P. J. Withers and G. E. Thompson, Surface andInterface Analysis, 45 (10), 1536-1542, DOI: 10.1002/sia.5221 (2013).

200. “Optimization of anodizing cycles for enhancedperformance”, M. Curioni, T. Gionfini, A. Vicenzo ,P. Skeldon,and G. E. Thompson, Surface and Interface Analysis, 45 (10),1485-1489, DOI: 10.1002/sia.5222 (2013).

201. “Microstructure and corrosion behaviour of lean 7xxxaluminium alloy”, A. M. Cassell, G. E. Thompson, X. Zhou, A. Afseth, H. Dunlop and M-A. Kulas, Surface and InterfaceAnalysis, 45 (10), 1604-1609, DOI: 10.1002/sia.5226 (2013).

202. “Investigation of dealloying by ultra-high resolutionnanotomography”, T. Hashimoto, M. Curioni, X. Zhou, J. Mancuso, P. Skeldon and G. E. Thompson, Surface and Interface Analysis, 45 (10), 1548-1552, DOI: 10.1002/sia.5176 (2013).

203. “Comparison of the behaviours of chromate and sol–gelcoatings on aluminium”, Y. Liu, Z. Feng, J. Walton, G. E. Thompson, P. Skeldon and X. Zhou, Surface andInterface Analysis, 45 (10), 1446-1451, DOI: 10.1002/sia.5206(2013).

204. “Anodizing of AA6063 aluminium alloy profiles; generation ofregions of dark appearance”, Y. Ma, X. Zhou, G. E. Thompson,J-O. Nilsson, M. Gustavsson and A. Crispin, Surface andInterface Analysis, 45 (10), 4179-1484, DOI: 10.1002/sia.5219(2013).

205. “Grain stored energy and the propagation of IGC in AA2xxxaluminium alloys”, C. Luo, Y. Ma, T. Hashimoto, X. Zhou, G. E. Thompson, P. Skeldon and A. E. Hughes, Surface andInterface Analysis, 45 (10), 1543-1547, DOI: 10.1002/sia.5218(2013).

206. “Influence of near-surface deformed layers on filiformcorrosion of painted AA3104 aluminium alloy”, Y. Liu, T. Hashimoto, X. Zhou, G. E. Thompson, G. Scamans, W. M. Rainforth and J. A. Hunter, Surface and InterfaceAnalysis, 45 (10), 1553-1557, DOI: 10.1002/sia.5232 (2013).

207. “Assessment of surface reactivity of aluminium AA1050alloy”, M. Witkowska, G. E. Thompson, T. Hashimoto and E. Koroleva, Surface and Interface Analysis, 45 (10), 1585-1589, DOI: 10.1002/sia.5271 (2013).

208. “Surface treatment of aluminium automotive sheet:mythology and technology”, G. Scamans, P. R. Andrews, C. Butler, A. Hall, G. E. Thompson, Y. Ma and X. Zhou, Surface and Interface Analysis, 45 (10), 1430-1434, DOI: 10.1002/sia.5279 (2013).

209. “Tracer study of pore initiation in anodic alumina formed in phosphoric acid”, A. Baron-Wiecheć, M. G. Burke, T. Hashimoto, H. Liu, P. Skeldon, G. E. Thompson, H. Habazaki,J. Ganem, and I. C. Vickridge, Electrochimica Acta, 113, 302-312, DOI: 10.1016/j.electacta.2013.09.060 (2013).

210. “The effect of integrating rolling deformation with wire arcadditive manufacture of Ti-6Al-4V - on grain size and texturerefinement”, A. A. Antonysamy, F. Martina, P. A. Colegrove,S.W. Williams and P. B. Prangnell, Metallurgical and MaterialsTransactions A (2013).

211. “Comparison of the effect of individual and combined Zr and Mn additions on the fracture behaviour of Al-Cu-Li alloyAA2198 rolled sheet”, D. Tsivoulas, P. B. Prangnell,Metallurgical and Materials Transactions A, 45 (3), 1338-1351, DOI: 10.1007/s11661-013-2103-2 (2013).

212. “Effect of microstructure on the corrosion behaviour ofextruded heat exchanger aluminium alloys”, A. Laferrere, N. Parson, X. Zhou and G. E. Thompson, Surface andInterface Analysis, 45, 1597-1603, DOI: 10.1002/sia.5282(2013).

213. “Anodizing of aluminium in sulphuric acid/boric acid mixedelectrolyte”, P. Skeldon, G. E. Thompson, M. Curioni and L. Zhang, Journal of the Electrochemical Society, 160, C179-C184, DOI: 10.1149/2.032306jes (2013).

214. “New findings on properties of plasma electrolytic coatingsfrom study of an Al-Li alloy”, Y. Cheng, Z. Xue, Q. Wang, X. Q. Wu, P. Skeldon and G. E. Thompson, ElectrochimicaActa, 107, 358-376, DOI: 10.1016/j.electacta.2013.06.022(2013).

215. “Ion-ion interaction in two-dimensional nanoporous aluminafilled with cubic YAlO3:Tb3+ matrix”, A. Podhorodecki, N.V. Gaponenko, G. Zatryb, I. S. Molchan, M. Motyka, J. Scrafinczuk, I. W. Golacki, L. S. Khoroshko, J. Misiewicz andG. E. Thompson, Journal of Physics D: Applied Physics, 46,355302-355312, DOI: 10.1088/0022-3727/46/35/355302(2013).

216. “Antibiofouling properties of sol-gel type polymers foraluminium alloys: biocorrosion protection againstPseudomonas Aeruginosa”, N. D. Vejar, M. I. Azocar, L. A. Tamayo, E. Gonzalez, J. Pavez, J. H. Zagal, X. Zhou, F. Santibanez, G. E. Thompson and M. A. Paez, InternationalJournal of Electrochemical Science, 8, 12062-12077, ISSN:1452-3981 (2013).

217. “Modelling competitive continuous and discontinuousprecipitation”, J. D. Robson, Acta Materialia 61 (20), 7781-7790, DOI: 10.1016/j.actamat.2013.09.017 (2013).

218. “The effect of aluminium on deformation and twinning inAlpha Titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas and S. Y. Zhang, Materials Science Forum 765, 549-553, DOI: 10.1016/j.actamat.2015.09.048 (2013).

219. “Measurement of strain and lattice rotation in the particledeformation zone”, L. C. L. Ko and J. Quinta da Fonseca,Materials Science Forum 753, 21-24, DOI:10.4028/www.scientific.net/MSF.753.21 (2013).

220. “Evolution of near-surface deformed layers during hot rollingof AA3104 aluminium alloy”, Y. Liu, M. Frolish, W. Rainforth,X. Zhou, G. E. Thompson, G. Scamans, and J. Hunter, Surface and Interface Analysis, 180-184, DOI: 10.1002/sia.5232 (2013).

221. “Finite element modelling of the inertia friction welding ofdissimilar high-strength steels”, M. Attallah, M. Preuss, P. H.Shipway, T. H. Hyde, S. Bray, C. J. Bennett, Metallurgical andMaterials Transactions A, 44, 11, 5054 – 5064, DOI:10.1007/s11661-013-1852-2 (2013).

222. “The effect of β phase on microstructure and textureevolution during thermomechanical processing of α + βtitanium alloy”, D. G. Prakash, P. Honniball, D. Rugg, P. J. Withers, J. Quinta da Fonseca, M. Preuss, Acta Materialia,61, 9, 3200 – 3213, DOI: 10.1016/j.actamat.2013.02.008(2013).

223. “On the three-dimensional structure of wc grains in cementedcarbides”, I. Brough, P. Hedströma, J. Odqvist, A.Borgenstama, J. Ågrena, A. Gholiniab, B. Winiarski, P. J. Withers, G. E. Thompson, K. Mingard, M. G. Gee, Acta Materialia, 61, 13, 4726-4733, DOI: 10.1016/j.actamat.2013.05.008 (2013).

224. “Three-dimensional observation and image-based modellingof thermal strains in polycrystalline alumina”, A. King, M. Mostafavi, P. Reischig, S. Rolland du Roscoat, W. Ludwig, J. Quinta da Fonseca, P. J. Withers, T. J. Marrow, D. Gonzalez,Acta Materialia, 61, 20, 7521 – 7533, DOI: 10.1016/j.actamat.2013.06.005 (2013).

225. “Residual stresses and tetragonal phase fractioncharacterisation of corrosion tested zircaloy-4 using energydispersive synchrotron x-ray diffraction”, A. Ambard, S. Lyon,R. A. Cottis, M. Preuss, Journal of Nuclear Materials, 443, 03,436-443, DOI: 10.1016/j.jnucmat.2013.07.053 (2013).

226. “Effect of build geometry on the β-grain structure and texturein additive manufacture of Ti-6Al-4V by selective electronbeam melting”, P. B. Prangnell, A. A. Antonysamy, J. Meyer,Materials Characterization, 84, 153 – 168, DOI:10.1016/j.matchar.2013.07.012 (2013).

227. “The effect of γ′ size and alloy chemistry on dynamic strainageing in advanced polycrystalline nickel base superalloys”, J. Quinta Da Fonseca, B. Grant, E. M. Francis, M. Preuss,Materials Science and Engineering. A, Structural Materials:Properties, Microstructure and Processing, 54-61, DOI: 10.1016/j.msea.2013.02.027 (2013).

228. “Visualisation of conductive filler distributions in polymercomposites using voltage and energy contrast imaging inSEM”, X. Zhou, J. Carr, C. Butler, S. L. Mills, J. O'Connor, E. McAlpine, T. Hashimoto, G. E. Thompson, G. M. Scamans,P. Howe, M. A. McCool, Polymer, 54, 1, 330-340, DOI: 10.1016/j.polymer.2012.11.018 (2013).

229. “Microstructural characterisation and corrosion behaviour of electroless Ni-W-P deposits of mixed nanocrystalline/amorphous structures”, R. X. Guo, F. Veijo, G. E. Thompson,Z. Liu, H. Liu, Transactions of the IMF, 91, 2, 101-106, DOI: 10.1179/0020296712Z.00000000087 (2013).

230. “Evolution of near-surface deformed layers on AA3104aluminium alloy”, X. Zhou, G. E. Thompson, J. A. Hunter, Y. Y. Die, L. Kai, Materials Science Forum, 765, 358-362, DOI: 10.4028/www.scientific.net/MSF.765.358 (2013).

231. “Mechanical and microstructural characterization ofpercussive arc welded hyper-pins for titanium to composite metal joining”, D. Strong, C. Octav, J. Meyer, P. B. Prangnell, Materials Science Forum, 765, 771-775, DOI: 10.4028/www.scientific.net/MSF.765.771 (2013).

232. “Antibiofouling properties of sol-gel type polymers foraluminium alloys: bio corrosion protection againstpseudomonas aeruginosa”, M. Azocar, L. Tamayo, E. Gonzalez, J. Pavez, M. Gulppi, X. Zhou, G. E. Thompson,Vejar, N. D, International Journal of the ElectrochemicalSociety, 8, 12062-12077, 10.1016/j.msea.2013.05.021(2013).

233. “Crystallisation and performance characteristics of high-temperature annealed electroless Ni-W-P coatings”, Y. Liu, H. L. Yao, G. E. Thompson, Z. Liu, Crystal Research andTechnology, 49, 03, 178-189, DOI: 10.1002/crat.201300375(2013).

234. “Microstructural characterization and mechanical properties of high power ultrasonic spot welded aluminum alloyAA6111–TiAl6V4 dissimilar joints”, C. Q. Zhang, J. D. Robson,O. Ciuca and P. B. Prangnell, Materials Characterization, 97,83-91, DOI: 10.1016/j.matchar.2014.09.001 (2014).

235. “Influence of orientation on twin nucleation and growth atlow strains in a magnesium alloy”, M. R. Barnett, A. Ghaderi,J. Quinta da Fonseca and J. D. Robson, Acta Materialia, 80,380-391, DOI: 10.1016/j.actamat.2014.07.013 (2014).

236. “Anisotropy and asymmetry of yield in magnesium alloys at room temperature”, J. D. Robson, Metallurgical andMaterials Transactions A 45 (11), 5226-5235, DOI: 10.1007/s11661-014-2453-4 (2014).

237. “Evaluating the effect of yttrium as a solute strengthener inmagnesium using in situ neutron diffraction”, N. Stanford, R. Cottam, B. Davis and J. D. Robson, Acta Materialia 78, 1-13, DOI: 10.1016/j.actamat.2014.06.023 (2014).

238. “Controlling interfacial reaction during dissimilar metalwelding of aluminium alloys”, L. Wang, Y. Wang, C. Q. Zhang, L. Xu, J. D. Robson and P. B. Prangnell, Materials Science Forum 794, 416-421, DOI: 10.4028/www.scientific.net/MSF.794-796.416 (2014).

239. “The effect of hot deformation on dispersoid evolution in a model 3xxx alloy”, J. D. Robson, T. Hill, N. Kamp,Materials Science Forum 794, 697-703, DOI: 10.4028/www.scientific.net/MSF.794-796.697 (2014).

240. “Texture evolution during wire drawing of Mg-RE alloy”, M. Chatterton, J. D. Robson and D. Henry, Magnesium Technology, 251-256, DOI: 10.1002/9781118888179.ch48 (2014).

241. “A new model for discontinuous and continuous precipitation in AZ91 magnesium alloy”, J. D. Robson, Materials Science Forum 461-466, DOI: 10.4028/www.scientific.net/MSF.783-786.461 (2014).

242. “Effect of rare-earth additions on the texture of wroughtmagnesium alloys: the role of grain boundary segregation”, J. D. Robson, Metallurgical and Materials Transactions A 45 (8), 3205-3212, DOI: 10.1007/s11661-013-1950-1 (2014).

243. “Contribution of twinning to low strain deformation in a Mg alloy”, M. R. Barnett, A. Ghaderi and J. D. Robson,Metallurgical and Materials Transactions A 45 (8), 3213-3221,DOI: 10.1007/s11661-013-2029-8 (2014).

244. “Electrochemical characteristics of a carbon fibre compositeand the associated galvanic effects with aluminium alloys”, Z. Liu, M. Curioni, P. Jamshidi, A. Walker, P. B. Prangnell, G. E. Thompson and P. Skeldon, Applied Surface Science, 314, 233-244, DOI: 10.1016/j.apsusc.2014.06.072 (2014).

245. “The effect of Mn and Zr dispersoid-forming additions onrecrystallization resistance in Al–Cu–Li AA2198 sheet”, D. Tsivoulas and P. B. Prangnell, Acta Materialia 77, 1-6, DOI: 10.1016/j.actamat.2014.05.028 (2014).

246. “Dissimilar metal laser spot joining of steel to aluminium in conduction mode”, G. Pardal, S. Meco, S. Ganguly, S. Williams and P. B Prangnell, International Journal ofAdvanced Manufacturing Technology, 73, 365-373, DOI: 10.1007/s00170-014-5802-y (2014).

247. "Heterogeneous nucleation of α-Al grain on primary α-AlFeMnSi intermetallic investigated using 3D SEMultramicrotomy and HRTEM", W. Yang, S. Ji, X. Zhou, G. E. Thompson I. Stone, G. Scamans and Z. Fan,Metallurgical and Materials Transactions A45, 3971-3980, DOI: 10.1007/s11661-014-2346-6 (2014).

248. “The impact of machining on the corrosion behaviour of AA7150-T651 aluminium alloy”, B. Liu and X. Zhou,Materials Science Forum, 794-796, 217-222, DOI: 10.4028/www.scientific.net/MSF.794-796.217 (2014).

249. “The behaviour of magnesium during free corrosion andpotentiodynamic polarization investigated by real-timehydrogen measurement and optical imaging”, M. Curioni, Electrochimica Acta, 120, 284, DOI: 10.1016/j.electacta.2013.12.109 (2014).

250. “Evaluation of inhibitor performance by electrochemicalmethods: comparative study of nitrate salts”, A. C. Balaskas,M. Curioni and G. E. Thompson, Journal of ElectrochemicalSociety, 161, C389, DOI: 10.1149/2.0711409jes (2014).

251. “Development of cerium-rich layers on anodic films formed onhigh-purity aluminium and AA7075 T6 alloy”, I. Gordovskaya,T. Hashimoto, J. Walton, M. Curioni, G. E. Thompson and P. Skeldon, Journal of the Electrochemical Society, 161, 14,C601, DOI: 10.1149/2.0091501jes (2014).

252. “Influence of plasma electrolytic oxidation on fatigue performance of AZ61 magnesium alloy”, A. Nemcova, P. Skeldon, G. E. Thompson, S. Morse and B. Pacal, Corrosion Science, 82, 58-66, DOI: 10.1016/j.corsci.2013.12.019 (2014).

253. “Effect of chloride ions in plasma electrolytic oxidation oftitanium”, P. Skeldon, G. E. Thompson, T. Hashimoto and S. Aliasghari, ECS Electrochemistry Letters, 3, C17-C20, DOI: 10.1149/2.002405eel (2014).

254. “Morphological control of anodic crystalline TiO2 nanochannelfilms for use in size-selective photocatalytic decomposition of organic compounds”, E. Tsuji, Y. Taguchi, Y. Aoki, T. Hashimoto, P. Skeldon, G. E. Thompson and H. Habazaki,Applied Surface Science, 301, 500-507, DOI: 10.1016/j.apsusc.2014.02.113 (2014)

255. “Correlative tomography”, T. L. Burnett, S. A. McDonald, A. Gholinia, R. Geurts, M. Janus, T. Slater, S. Haigh, C. Ornek,F. Almuaili, D. Engelberg, G. E. Thompson and P. J. Withers,Nature Scientific Reports 4, Article Number 4711, DOI: 10.1038/srep04711 (2014).

256. “Quantitative 3D in-situ study of the opening of a shortfatigue crack in a magnesium alloy”, M. Mostafavi, T. Hashimoto, G. E. Thompson and T. J. Marrow, International Journal of Fatigue,66, 183-193, DOI: 10.1016/j.ijfatigue.2014.04.003 (2014).

257. “Revelation of intertwining organic and inorganic fractalstructures in polymer coatings”, A. E. Hughes, A. Trinchi, F. F. Chen, Y. S. Yang, I. S. Cole, S. Sellaiyan, J. Carr, P. D. Lee,G. E. Thompson and T. Q. Xiao, Advanced Materials, 26, 4504-4508, DOI: 10.1002/adma.201400561 (2014).

258. “Formation of barrier-type anodic films on ZE41 alloy in afluoride/glycerol electrolyte”, J. M. Hernández-López, A. Nemcova, X. L. Zhong, H. Liu, M. A. Arenas-Vara, S. Haigh,G. Burke, P. Skeldon and G. E. Thompson, ElectrochimicaActa, 130, 124-131, DOI: 10.1016/j.electacta.2014.05.147(2014).

259. “Discoloration of anodized AA6063 aluminium alloy”, Y. Ma,X. Zhou, J. Wang, G. E. Thompson, W. Huang, J. O Nilsson,M. Gustavsson and A. Crispin, Journal of the ElectrochemicalSociety, 161, C312-C320, DOI: 10.1149/2.065406jes (2014).

260. “Efficient growth of anodic films on magnesium in organicelectrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, E.i Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, Electrochemistry Communications, 46, 30-32, DOI: 10.1016/j.elecom.2014.06.011 (2014).

261. “Characterization of anodic oxide growth on commerciallypure titanium in NaTESI electrolyte”, Z. Liu, H. Liu, X. Zhong, T. Hashimoto, G. E. Thompson and P. Skeldon, Surface and Coatings Technology, 258, 1025-1031, DOI: 10.1016/j.porgcoat.2014.07.001 (2014).

262. “CO2 capture efficiency, corrosion properties and ecotoxicityevaluation of amine solutions involving newly synthesizedionic liquids”, X. L. Papatryfon, N. S. Heliopoulos, I. S. Molchan,L. F. Zubeir, N. D. Bezemer, M. K. Arfanis, A. G. Kontos, V. Likodimos, B. Iliev, G. Em. Romanos, P. Falaras, K. Stamatakis, K. G. Beltsios, M. C. Kroon, G. E. Thompson, J. Klöckner and T. J. S. Schubert, Industrial & EngineeringChemistry Research, 30, 12083-12102, DOI: 10.1021/ie501897d (2014).

263. “Plasma electrolytic oxidation of titanium in phosphate/silicateelectrolyte and tribological performance of the coatings”, S. Aliasghari, P. Skeldon and G. E. Thompson, Applied SurfaceScience, 316, 463-476, DOI: 10.1021/ie501897d (2014).

264. “Anodic oxide film growth on thin magnetron sputter-deposited titanium layer”, Z. Liu, H. Liu, T. Hashimoto, G. E. Thompson and P. Skeldon, Materials Characterisation,98, 102-106, DOI 10.1016/j.matchar.2014.10.012 (2014).

265. “Staining and embedding of human chromosomes for 3Dserial block face scanning electron microscopy”, M. Yusuf, B. Chen, T. Hashimoto, A. Estardarte G. E. Thompson and I. K. Robinson, Biotechniques International Journal of Life Science Methods, 57, 302-307, DOI: 10.2144/000114236(2014).

266. “3D characterization of trans- and inter-lamellar fatigue crack in (α + β) Ti alloy”, L. Babout, Ł. Jopek and M. Preuss, Materials Characterization, 98 (0), 130-139, DOI: 10.1016/j.matchar.2014.10.017 (2014).

267. “A method for accurate texture determination of thin oxidefilms by glancing-angle laboratory X-ray diffraction”, A. Garner, M. Preuss, P. Frankel, Journal of AppliedCrystallography, 47 (2), 575-583, DOI: 10.1107/S1600576714000569 (2014).

268. “In situ synchrotron studies of reversible and irreversible non-elastic strain in a two-phase TiAl alloy”, F. A. Garcia-Pastor, H. Jiang, D. Hu, X. Wu, P. J. Withers and M. Preuss,Metallurgical and Materials Transactions, 45 (2), 607-618,DOI: 10.1007/s11661-013-2024-0 (2014).

269. “Iron redistribution in a zirconium alloy after neutron andproton irradiation studied by energy-dispersive X-rayspectroscopy (EDX) using an aberration-corrected (scanning)transmission electron microscope”, E. M. Francis, A. Harte, P. Frankel, S. J. Haigh, D. Jädernäs, J. Romero, L. Hallstadiusand M. Preuss, Journal of Nuclear Materials, 454 (1-3), 387-397, DOI: 10.1016/j.jnucmat.2014.08.034 (2014).

270. “Influence of orientation on twin nucleation and growth atlow strains in a magnesium alloy”, M.R Barnett, A. Ghaderi,JQ da Fonseca and J. D. Robson, Acta Materialia, 80, 380-391, DOI: 10.1016/j.actamat.2014.07.013 (2014).

271. “Peak broadening anisotropy in deformed face-centred cubicand hexagonal close-packed alloys”, T. H Simm, P. J Withersand J. Quinta da Fonseca, Applied Crystallography, 47 (5),DOI: 10.1107/S1600576714015751 (2014).

272. “Comparison between a near-field and a far-field indexingapproach for characterization of a polycrystalline samplevolume containing more than 1500 grains”, L. Nervo, A. King,J. P Wright, W. Ludwig, P. Reischig and J. Quinta da Fonseca,Journal of Applied Crystallography, 47 (4), 1402-1416, DOI: 10.1107/S160057671401406X (2014).

273. “Modeling Twin Clustering and Strain Localization in HexagonalClose-Packed Metals”, G. Timár, and J. Quinta da Fonseca.Metallurgical and Materials Transactions, A, 1-8, DOI: 10.1007/s11661-014-2547-z (2014).

274. “A systematic study of antibacterial silver nanoparticles:efficiency, enhanced permeability, and cytotoxic effects”, H. Liu, H. L. Yao, Y. Liu, G. E. Thompson, Z. Liu, Journal ofNanoparticle Research, 49, 02, 178-189, DOI:10.1007/s11051-014-2465-4 (2014).

275. “The effect of cooling rate from solution on the lattice misfitduring isothermal aging of a Ni-base superalloy”, L. Tamayo,N. Vejar, G. Gomez, X. Zhou, G. E. Thompson, E. Cerda,Journal of Nanoparticle Research, 45, 5, 2436-2444, DOI:10.1007/s11661-014-2197-1 (2014).

276. “The effect of annealing on the corrosion behaviour of 444stainless steel for drinking water applications”, C. Bitondo, M. Curioni, A. Bossio, F. Bellucci, Corrosion Science, 87, 6-10,DOI: 10.1016/j.corsci.2014.06.025 (2014).

277. “Wear-resistant coatings formed on Zircaloy-2 by plasmaelectrolytic oxidation in sodium aluminate electrolytes”, J. Cao, Z. Peng, Q. Wang, E. Matykin, P. Skeldon, G. E.Thompson, Y. Cheng, Electrochimica Acta, 116, 453-466,DOI: 10.1016/j.electacta.2013.11.079 (2014).

278. “A quantitative three-dimensional in situ study of a shortfatigue crack in a magnesium alloy”, M. Mostafavi, T.Hashimoto, G. E. Thompson, T. J. Marrow, InternationalJournal of Fatigue, 66, 183-193, DOI:10.1016/j.ijfatigue.2014.04.003 (2014).

279. “Modelling the effect of elastic and plastic anisotropies onstresses at grain boundaries”, I. Simonovski, P. J. Withers, J. Quinta Da Fonseca, D. Gonzalez, International Journal ofPlasticity, 61, 49-63, DOI: 10.1016/j.ijplas.2014.03.012(2014).

280. “Release of silver and copper nanoparticles from polyethylenenanocomposites and their penetration into Listeriamonocytogenes”, P. A. Zapata, N. J. Vejar, M. A. Gulppi, X. Zhou, G. E. Thompson, F. M. Rabagliati, L. A. Tamayo,Materials Science and Engineering: C, 40, 24-31, DOI:10.1016/j.msec.2014.03.037 (2014).

281. “Three-dimensional analysis of the spatial distribution of iron oxide particles in a decorative coating by electronmicroscopic imaging”, T. Hashimoto , F. Vergeer , A. Burgess,G. E. Thompson, I. Robinson, Progress in Organic Coatings,77, 6, 1069-1072, DOI: 10.1016/j.porgcoat.2014.03.005(2014).

282. “The application of multiscale quasi 4D CT to the study ofSrCrO4 distributions and the development of porous networksin epoxy-based primer coatings”, A. Trinchi, F. F. Chen, Y. S. Yang, I. S. Cole, J. Carr, P. D. Lee, G. E. Thompson, A. E. Hughes, Progress in Organic Coatings, 77, 11, |1946-1956, DOI: 10.1016/j.porgcoat.2014.07.001 (2014).

283. “Corrosion behaviour of mild steel in 1-alkyl-3-methylimidazolium tricyanomethanide ionic liquids for CO2capture applications”, G. E. Thompson, P. Skeldon, R. Lindsay,L. Vlassis, G. Romanos, I. S. Molchan, RSC Advances, 4, 11,DOI: 10.1039/c3ra45872e (2014).

284. “Characterization of abnormal grain coarsening in Alloy 718”,M. Preuss, J. Quinta Da Fonseca, T. Witulski, T. Gregor, MATEC Web of Conferences, 14, DOI: 10.1051/matecconf/20141407004 (2014).

285. “Laser nanocrystallisation and corrosion behaviour ofelectroless Ni-W-P coating with high phosphorus content”, G. E. Thompson, H. L. Yao, F. Viejo, G. Harrison, Z. Liu, H. Liu,Transactions of the IMF, 92, 4, 212-217, DOI:10.1179/0020296714Z.000000000171 (2014).

286. “Influence of galvanized coatings on abrasion circle frictionstir spot welding aluminium to steel for automotiveapplications”, P. B. Prangnell, L. S. Fang, Y. C. Chen, MaterialsScience Forum, 783-786, 1741-1746, DOI:10.4028/www.scientific.net/MSF.783-786.1741 (2014).

287. “Texture formation in flow formed ferritic steel tubes and theinfluence of the process parameters”, G. Timar, M. Tuffs, J. Quinta Da Fonseca, M. Preuss, D. Tsivoulas, MaterialsScience Forum, 783-786, 2602-2607, DOI:10.4028/www.scientific.net/MSF.783-786.2602 (2014).

288. “Systematic evaluation of the advantages of static shoulderfsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong, P. B. Prangnell, Materials Science Forum, 794-796, 407-412,DOI: 10.4028/www.scientific.net/MSF.794-796.407 (2014).

289. “Heterogeneous Zr solute segregation and Al 3 Zr dispersoid distributions in Al–Cu–Li alloys”, D. Tsivoulas and J. D. Robson, Acta Materialia, 93, 73-86, DOI: 10.1016/j.actamat.2015.03.057 (2015)

290. “Characterisation and modelling of defect formation in direct-chill cast AZ80 alloy” D. Mackie, J. D. Robson, P. J. Withers and M. Turski, Materials Characterization, 104, 116-123, DOI: 10.1016/j.matchar.2015.03.033 (2015).

291. “Coating design for controlling b phase imc formation in dissimilar Al-Mg-metal welding”, Y. Wang, L. Wang,J. D. Robson, B. M. Al-Zubaidy and P. B. Prangnell, Friction Stir Welding and Processing VIII, 171, DOI: 10.1002/9781119093343.ch19 (2015).

292. “Critical assessment 9: wrought magnesium alloys”, J. D. Robson, Materials Science and Technology, 31 (3), 257-264, DOI: 10.1179/1743284714Y.0000000683(2015).

293. “Effect of traces of silicon on the formation of Fe-rich particlesin pure magnesium and the corrosion susceptibility ofmagnesium”, L. Yang, X. Zhou, S. M Liang, R. Schmid-Fetzer,Z. Fan and G. Scamans, Journal of Alloys and Compounds,619, 396-400, DOI: 10.1016/j.jallcom.2014.09.040 (2015).

294. “Stationary shoulder FSW for joining high strength aluminiumalloys”, H. Wu, Y-C, Chen, D. Strong and P. B. Prangnell, Journal of Materials Processing Technology, 221, 187-196, DOI: 10.1016/j.jmatprotec.2015.02.015 (2015).

295. “Modelling of the thermal field in dissimilar alloy ultrasonicwelding”, P. Jedrasiak, H. R. Shercliff, Y. C. Chen, L. Wang, P. B. Prangnell and J. D. Robson, Journal of MaterialsEngineering and Performance, 24, 799-807, DOI: 10.1007/s11665-014-1342-8 (2015).

296. “Delamination of near-surface layer on cold rolled AlFeSi alloyduring sheet forming”, J. Wang, X. Zhou, G. E. Thompson, J. A. Hunter and Y. Yuan, Materials Characterization, 99, 109-117, DOI: 10.1016/j.matchar.2014.11.011 (2015).

297. “Near-surface microstructure on twin-roll cast 8906 aluminiumalloy”, J. Wang, X. Zhou, G. E. Thompson, J. A. Hunter and Y. Yuan, Metallurgical and Materials Transactions A, 46, 2688-2695, DOI: 10.1007/s11661-015-2877-5 (2015).

298. “Corrosion behaviour of pure magnesium with low impuritycontent but high corrosion rate in 3.5 wt% NaCl solution”, L. Yang, X. Zhou, M. Curioni, S. Pawar, H. Liu, Z. Fan and G. E. Thompson, Journal of Electrochemical Society, 162, C362-368, DOI: 10.1149/2.1041507jes (2015).

299. “Study of the metallurgy of dissimilar Ti-6Al-4V – StainlessSteel linear fiction welded joints”, F. Impero, F. Scherillo, A. Astarita, K. A. Beamish, M. Curioni, A. Squillace and X. Zhou, Key Engineering Materials, 651-653, 1427-1432,DOI: 10.1002/maco.201307476 (2015).

300. “Investigation of the microstructure and the influence of ironon the formation of Al8Mn5 particles in twin roll cast AZ31magnesium alloy”, S. Pawar, X. Zhou, G. E. Thompson and T. Hashimoto, Journal of Alloys and Compounds, 628, 195-198, DOI: 10.1016/j.jallcom.2014.12.028 (2015).

301. “Effect of near-ambient temperature changes on the galvanic corrosion of an AA2024-T3 and mild steel couple”,U. Donatus, G. E. Thompson and X. Zhou, Journal ofElectrochemical Society, 161, C42-C46, DOI: 10.1149/2.0551501jes (2015).

302. “Grain refining mechanism in the Al/Al-Ti-B system”, Z. Fan, W. Yang, Y. Zhang, T. Qin, X. Zhou, G. E. Thompson, T. Pennycook and T. Hashimoto, Acta Materialia, 84, 292-304, DOI: 10.1016/j.actamat.2014.10.055 (2015).

303. “Corrosion behaviour of stainless steel-titanium alloy linearfriction welding joints: galvanic coupling”, M. Curioni, A. Astarita, A. Squillace, X. Zhou, F. Bellucci, G. E. Thompsonand K. Beamish, Materials and Corrosion, 66 (2), 111-117,DOI: 10.1002/maco.201307476 (2015).

304. “Efficiency of anodizing of an Al-Cu alloy in sulphuric acidunder low potentials”, B. Mingo, A. Nemcova, D. Hamad, R. Arrabal, E. Matykina, M. Curioni, P. Skeldon and G. E. Thompson, Transaction of the Institute of MetalFinishing, 93 (2), 18-23, DOI:10.1179/0020296714Z.000000000217 (2015).

305. “Correlation between electrochemical impedance spectroscopymeasurements and corrosion rate of magnesium investigatedby real-time hydrogen measurement and optical imaging”, M. Curioni, F. Scenini, T. Monetta and F. Bellucci,Electrochimica Acta, 166 (1), 372-384, DOI:10.1016/j.electacta.2015.03.050 (2015).

306. “Effect of magnesium and titanium on the cathodic behaviourof aluminium in nitric acid”, F. J. Garcia-Garcia, T. Y. Chiu, P. Skeldon and G. E. Thompson, Surface and InterfaceAnalysis, 47, 30-36, DOI: 10.1002/sia.5640 (2015).

307. “Formation of porous anodic oxide film on titanium inphosphoric acid electrolyte”, Z. Liu and G. E. Thompson,Journal of Materials Engineering and Performance, 24, 59-66,DOI: 10.1007/s11665-014-1262-7 (2015).

308. “High growth rate, wear-resistant coatings on an Al-Cu-Li alloyby plasma electrolytic oxidation in concentrated aluminateelectrolytes”, J. Cao, Y. Cheng, Z. Peng, M. Mao, P. Skeldonand G. E Thompson, Surface and Coatings Technology, 269,74-82, DOI: 10.1016/j.surfcoat.2014.12.078 (2015).

309. “Factors controlling stress generation during the initial growthof porous anodic aluminium oxide”, O. Capraz, P. Shrotriya, P. Skeldon, G. E. Thompson and K. R. Hebert, ElectrochimicaActa,159, 16-22, DOI: 10.1016/j.electacta.2015.01.183(2015).

310. “Scanning transmission electron microscopy for morphologyanalysis of anodic oxide film on titanium”, Z. Liu, T. Hashimoto, I-L. Tsai, G. E. Thompson, P. Skeldon and H. Liu,Vacuum, 115, 19-22, DOI: 10.1016/j.vacuum.2015.01.027(2015).

311. “Formation of grooved and porous coatings on titanium byplasma electrolytic oxidation in H2SO4 / H3PO4 electrolytesand effects of coating morphology on adhesive bonding”, O. A. Galvis, D. Quintero, J. G. Castano, H. Liu, G. E. Thompson, P. Skeldon and F. Echeverria, Surface and Coatings Technology, 269, 238-249, DOI: 10.1016/j.surfcoat.2015.02.036 (2015).

312. “Role of oxide stress in the initial growth of self-organizedporous aluminum oxide”, Ö. Çapraz, P. Shrotriya, P. Skeldon,G. E. Thompson and K. R. Hebert, Electrochimica Acta, 167, 404-411, DOI: 10.1016/j.electacta.2015.03.017 (2015).

313. “A comparison of plasma electrolytic oxidation of Ti-6Al-4Vand Zircaloy 2 alloys in a silicate-hexametaphosphateelectrolyte”, Y. Cheng, Z. Peng, X. Wu, Z. Cao, P. Skeldon andG. E. Thompson, Electrochimica Acta, 165, 303-313, DOI: 10.1016/j.electacta.2015.03.020 (2015).

314. “Study of the effect of cadmium on the bimetallic corrosion behaviour of AA2024T3 and mild steel couple”, U. Donatus, G. E.Thompson and Z. Liu, Journal of MaterialsEngineering and Performance, 24, 1897-1905, DOI: 10.1007/s11665-015-1472-7 (2015).

315. “Chemical etching behaviour of titanium in methanol-ethanolelectrolyte”, Z. Liu, I-L. Tsai, G. E. Thompson, H. Liu andU.Donatus, Materials Chemistry and Physics, 160, 329, DOI: 10.1016/j.matchemphys.2015.04.045 (2015).

316. “Growth of barrier-type anodic films on magnesium inethylene glycol electrolytes containing fluoride and water”, H. Habazaki, F. Kataoka, K. Shazad, E. Tsuji, Y. Aoki, S. Nagata, P. Skeldon and G. E. Thompson, ElectrochimicaActa, 179, 402 - 410, DOI: 10.1016/j.electacta.2015.02.168(2015).

317. “The corrosion protection of AA2024-T3 aluminium alloy byleaching of lithium-containing salts from organic coatings”, P. Visser, Y. Liu, X. Zhou, T. Hashimoto, G. E. Thompson, S. B. Lyon, L. G. J. Van der Ven, A. J. M. C. Mol and H. A. Terryn, Faraday Discussions (Royal Society of Chemistry),180, 511 (2015).

318. “Evolution of a laser shock peened residual stress field locallywith foreign object damage and subsequent fatigue crackgrowth”, S. Zabeen, M. Preuss and P. J. Withers, ActaMaterialia, 83, 216-226, DOI: 10.1039/C4FD00237G (2015).

319. “Grain breakup during elevated temperature deformation of an HCP metal”, P. Honniball, M. Preuss, D. Rugg, and J. Quinta Da Fonseca, Metallurgical and Materials TransactionsA, 46 (5), 2143-2156, DOI: 10.1016/j.actamat.2014.09.032(2015).

320. “Residual stresses due to foreign object damage in laser-shockpeened aerofoils: simulation and measurement”, B. Lin, S. Zabeen, J. Tong, M. Preuss and P. J. Withers, Mechanics of Materials, 67 (12), 2908-2913, DOI: 10.1007/s11837-015-1627-x (2015).

321. "Structure of the copper-enriched layer introduced by anodicoxidation of copper-containing aluminum alloy” T. Hashimoto,X. Zhou, G. E. Thompson and P. Skeldon, Electrochimica Acta,179, 394-401, DOI: 10.1016/j.electacta.2015.01.133 (2015).

322. "FIB-SEM investigation on corrosion propagation of Al-Li alloyin sodium chloride solution” Corrosion Engineering, Scienceand Technology, C. Luo, M. Gao, Z. Sun, X. Zhang, Z. Tang and X. Zhou, 50 (5), 390 - 396, DOI: 10.1179/1743278214Y.0000000235 (2015).

323. “Effect of current density and behaviour of second phases inanodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/waterelectrolyte”, A. Němcová, I. Kuběna, M. Šmíd, H. Habazaki, P. Skeldon and G. E. Thompson, Journal of Solid StateElectrochemistry, 179, 394-401, DOI: 10.1007/s10008-015-2864-1 (2015).

324. “XCT analysis of the influence of process parameters on defect population in Ti-6Al-4V components manufactured byselective electron beam melting”, S. Tammas-Williams, H. Zhao, F. Leonard, F. Derguti, I. Todd and P. B. Prangnell,Journal of Material Characterisation, 102, 47 - 61, DOI: 10.1007/s10008-015-2864-1 (2015).

325. “Crystallographic defects induced localised corrosion inAA2099-T8 aluminium alloy”, Y. Ma, X. Zhou, W. Huang, Y. Liao, X. Chen, X. Zhang and G. E. Thompson, CorrosionEngineering, Science and Technology, 50 (6), 420-424, DOI: 10.1179/1743278214Y.0000000237 (2015).

326. “Modelling data acquisition during electrochemical noisemeasurements for corrosion studies”, M. Curioni, T. Monetta,and F. Bellucci, Corrosion Reviews, 33 (4), 187-194, DOI: 10.1515/corrrev-2014-0047 (2015).

327. "Localized corrosion in AA2099-T83 aluminium-lithium alloy:the role of intermetallic particles”, Materials Chemistry andPhysics, Y. Ma , X. Zhou, W. Huang, G. E. Thompson, X. Zhang, C. Luo, Z. Sun, 161, 201-210, DOI: 10.1016/j.matchemphys.2015.05.037 (2015).

328. “Characterization of anodic oxide film growth on Ti6Al4V in NaTESi electrolyte with associated adhesive bondingbehaviour”, G. E. Thompson, Z. J. Liu, X. Zhong, H. Liu, I. L. Tsai, U. Donatus, Electrochemica Acta, 182, 482-492, DOI: 10.1016/j.electacta.2015.09.089 (2015).

329. “Modelling of intermetallic compounds growth betweendissimilar metals”, P. B. Prangnell, L. Wang, J. D. Robson,Metallurgical and Materials Transactions A, 4106-4114, DOI: 10.1007/s11661-015-3037-7 (2015).

330. “Effect of low temperature sensitization on the susceptibilityto intergranular corrosion in AA5083 aluminium alloy”, X. Zhou, W. Wei, S. Gonzalez, T. Hashimoto, P. B. R. Rajan, G. E. Thompson, Materials and Corrosion, DOI: 10.1002/maco.201508589 (2015).

331. “Correlation between localized plastic deformation andlocalized corrosion in AA2099 aluminum-lithium alloy”, Y. Ma, X. Meng, Y. Liao, L. Chai, Y. Yi, X. Zhang, X. Zhou,DOI: 10.1002/sia.5817 (2015).

332. “The influence of prolonged natural aging on the subsequentartificial aging response of the AA6111 automotive alloy”, A. Abouarkoub, X. Zhou, T. Hashimoto, G. Scamans, G. E. Thompson, Metallurgical and Materials Transactions A,46 (9), 4380-4393, DOI: 10.1007/s11661-015-3043-9 (2015).

333. “In-service sensitization of a microstructurally heterogeneousAA5083 alloy”, G. E. Thompson, W. Wei, S. Gonzalez, T. Hashimoto, X. Zhou, Materials and Corrosion, DOI: 10.1002/maco.201508507 (2015).

334. “Understanding the galvanic interactions between AA2024T3 and mild steel using the scanning vibratingelectrode technique”, U. Donatus, H. Liu, X. Zhou, Z. Liu, G. E. Thompson, Materials Chemistry and Physics, 161, 228-236, DOI: 10.1016/j.matchemphys.2015.05.040 (2015).

335. “Analyses of the sequential stages of corrosion on aa2024t3using the scanning vibrating electrode technique (SVET)”, G. E. Thompson, U. Donatus, H. Liu, D. Elabar, Journal ofMaterials Engineering and Performance, 24 (10), 3808-3814,DOI: 10.1007/s11665-015-1701-0 (2015).

336. “The effect of post-anodizing rinsing on the morphology and composition of porous and nanotubular anodic filmsgenerated on titanium”, P. Skeldon, G. E. Thompson, T. V. Molchan, X. Zhong, I. S. Molchan, Electrochimica Acta,176, 1233-1238, DOI: 10.1016/j.electacta.2015.07.061 (2015).

337. “Formation of a trivalent chromium conversion coating on AA2024-T351 alloy”, G. E. Thompson, P. Skeldon, J. Qi, T. Hashimoto, J. Walton, X. Zhou, T. Hashimoto, Journal of the Electrochemical Society, 163 (2), C25-C35, DOI: 10.1149/2.0771602jes (2015).

338. “Corrosion inhibition of aluminium and AA2014-T6 alloy bystrontium chromate”, P. Skeldon, Z. Liu, Z. Feng, X. Zhou, G. E. Thompson, S. B. Lyson, S. Gibbon, D. Graham, Surfaceand Interface Analysis, 122-1238, DOI: 10.1002/sia.5845(2015).

339. “The role of intermetallics on the corrosion initiation of twinroll cast AZ31 magnesium alloy”, G. E. Thompson, S. Pawar,X. Zhou, G. Scamans, Z. Fan, Journal of the ElectrochemicalSociety, 162, DOI: 10.1149/2.0291509jes (2015).

340. “Antibacterial and Non-cytotoxic Effect of NanocompositesBased in Polyethylene and Copper Nanoparticles”, X. Zhou, L. A. Tamayo, P. A. Zapata, M. Azocar, X. Zhou, G.E. Thompson,M. A. Paez, Journal of Materials Science: Materials in Medicine,26 (129), 1-5, DOI: 10.1007/s10856-015-5475-6 (2015).

341. “Corrosion susceptibility of dissimilar friction stir welds of AA5083 and AA6082 alloys”, X. Zhou, U. Donatus, G. E. Thompson, J. Wang, A. Cassell, K. Beamish, Materials Characterization, 107, 85-97, DOI: 10.1016/j.matchar.2015.07.002 (2015).

342. “Effect of sulphate impurity in chromic acid anodizing ofaluminium”, P. Skeldon, G. E. Thompson, A. Nemcova, T. Hashimoto, D. Elabar, Corrosion Science, 100, 377-385, DOI: 10.1016/j.corsci.2015.08.019 (2015).

343. “Features in aluminium alloy grains and their effects onanodizing and corrosion”, G. E. Thompson, U. Donatus, D. Elabar, T. Hashimoto, S. Morsch, Surface CoatingsTechnology, 277, 91-98, DOI: 10.1016/j.surfcoat.2015.07.034(2015).

344. “Trivalent chromium conversion coating formation onaluminium”, P. Skeldon, J. Qi, T. Hashimoto, T. Hashimoto, J. Walton, X. Zhou, G. E. Thompson, Surface and Coatings Technology, 280, 317-329, DOI: 10.1016/j.surfcoat.2015.09.024 (2015).

345. “Flow patterns in friction stir welds of AA5083 and AA6082alloys”, G. E. Thompson, X. Zhou, U. Donatus, J. Wang, K. Beamish, Materials and Design, 83, 203-213,10.1016/j.matdes.2015.06.006 (2015).

346. “Behaviour of alloying elements during anodizing of Mg-Cuand Mg-W in fluoride/glycerol electrolyte”, P. Skeldon, M. S. Palagonia, A. Němcová, I. Kuběna, M. Šmíd, S. Gao, H. Liu, X. L. Zhong, S. J. Haigh, M. Santamaria, F. Di Quarto, H. Habazaki, G. E. Thompson, Electrochemical Society Journal,162 (9), 487-494, DOI: 10.1149/2.0761509jes (2015).

347. “Microstructure and corrosion properties of the plasma MIG welded AA5754 automotive alloy”, A. Abouarkoub, G. E. Thompson, X. Zhou, G. Scamans, Journal of Mineralsand Materials Characterization and Engineering, 3, 318-325,DOI: 10.4236/jmmce.2015.34034 (2015).

348. “The role of crack branching in stress corrosion cracking of aluminium alloys”, G. E. Thompson, T. L. Burnett, N. J. H. Holyroyd, G. M. Scamans, X. Zhou, P. J. Withers,Surface and Interface Analysis, 47 (11), 1029-1039, DOI: 10.1515/corrrev-2015-0050 (2015).

349. “Effectiveness of 2-mercaptobenzothiazole,8-hydroxyquinoline and benzotriazole as corrosion inhibitorson AA 2024-T3 assessed by electrochemical methods”, A. C. Balaskas, M. Curioni, G. E. Thompson, Surface andInterface Analysis, 47 (11), 1029-1039, DOI: 10.1002/sia.5810 (2015).

350. “Modelling and visualisation of material flow in friction stirspot welding”, P. B. Prangnell, A. Reilly, H. R. Shercliffe, Y. C. Chen, Journal of Materials Processing Technology, 473-474, DOI: 10.1016/j.jmatprotec.2015.06.021 (2015).

351. “Novel use of glow discharge optical emission spectroscopy(GDOES) to study corrosion of AA2024-T3 in the presenceand absence of inhibitors”, G. E. Thompson, R. V. Bingham,Surface and Interface Analysis, 47 (12), 1098-1108, DOI: 10.1002/sia.5854 (2015).

352. “The mechanism of hydrogen evolution during anodic polarization of aluminium”, M. Curioni, F. Scenini, Electrochimica Acta, 180, 712-721, DOI: 10.1016/j.electacta.2015.08.076 (2015).

353. “Passivation behaviour of 304 stainless steel in an ionic liquidwith a fluorinated anion”, G. E. Thompson, I. S. Molchan, J. Walton, P. Skeldon, A. Tempez, S. Legendre, Applied Surface Science, 357 (Part A), 37-44, DOI: 10.1016/j.apsusc.2015.08.189 (2015).

354. “Anodizing behaviour of friction stir welded dissimilaraluminium alloys”, P. Skeldon, X. Zhou, U. Donatus, G. E. Thompson, Journal of The Electrochemical Society, 162 (2), C657-C665, DOI: 10.1149/2.0651512jes (2015).

355. “Quantitative characterization of porosity and determinationof elastic modulus for sintered micro-silver joints”, G. E. Thompson, J. Carr, X. Milhet, P. Gadaud, S. A. Boyer, P. Lee, Journal of Materials Processing Technology, 225, 19-23, DOI: 10.1016/j.jmatprotec.2015.03.037 (2015).

356. “Elevated temperature, in situ micromechanicalcharacterization of a high temperature ternary shape memoryalloy”, G. E. Thompson, J. M. Wheeler, C. Niederberger, R. Raghavan, M. Weaver, J. Michler, The Journal of TheMinerals, Metals & Materials Society, 67 (12), 2908-2913, DOI: 10.1007/s11837-015-1627-x (2015).

357. “The kinematics of deformation and the development ofsubstructure in the particle deformation zone”, J. Quinta daFonseca, L. Ko, Iop Conference Series: Materials Science andEngineering, 89 (1), DOI: 10.1088/1757-899X/89/1/012012(2015).

358. “Surface modifications of stainless steel to minimisecontamination in mass spectrometers”, G. E. Thompson, J. Abda, D. Douce, G. Jones, P. Skeldon, Applied SurfaceScience, 357 (Part A), 593-602, DOI: 10.1016/j.apsusc.2015.08.209 (2015).

359. “The interaction of grain refinement and ageing inmagnesium–zinc–zirconium (ZK) alloys”, J. D. Robson, C. Paa-Rai, Acta Materialia, 95, 010-019, DOI: 10.1016/j.actamat.2015.05.012 (2015).

360. “Coating design for controlling β phase IMC formation indissimilar Al-Mg metal welding”, Y. Wang, L. Wang, J. D. Robson, B. Al-Zubaidy, P. B. Prangnell, Friction StirWelding and Processing VIII, 352-358, DOI:10.1002/9781119093343.ch19 (2015).

361. “Automated multi-scale microstructure heterogeneity analysisof selective electron beam melted Ti-6Al-4V components”, H. Zhao, A. A. Antonysamy, J. Meyer, S. T. Williams, P. B.Prangnell, TMS2015 Supplemental Proceedings, 429-436,DOI: 10.1002/9781119093466.ch54 (2015).

362. “Integration of deformation processing with additivemanufacture of Ti-6Al-4V components for improved β grainstructure and texture”, TMS2015 Supplemental Proceedings,Sidhu, J, A. Wescott, P. B. Prangnell, J. Donoghue, 437-444,DOI: 10.1002/9781119093466.ch55 (2015).

363. “Microstructural origin of localized corrosion in anodizedAA2099-T8 aluminium-lithium alloy”, X. Chen, X. Zhou, Y. Yi, Y. Liao, W. Huang, Y. Ma, Surface and Interface Analysis,DOI: 10.1002/sia.5856 (2015).

364. “The propagation of localized corrosion in Al-Cu-Li alloy”, X. Zhou, Y. Ma, G. E. Thompson, C. Luo, Z. Sun, X. Zhang, Z. Tang, X. Zhang, Surface and Interface Analysis, DOI:10.1002/sia.5890 (2015).

365. “Effect of current density and behaviour of second phases inanodizing of a Mg-Zn-RE alloy in a fluoride/glycerol/waterelectrolyte” A. Němcová, I. Kuběna, M. Šmíd, H. Habazaki, P. Skeldon , G. E. Thompson, Journal of Solid StateElectrochemistry, 20, 4, 1155-1165, DOI: 10.1007/s10008-015-2864-1 (2015).

366. “Spallation behaviour of alumina scale formed on FeCrAlYalloy after isothermal oxidation”, X. Zhao, Y. C. Chen, Y. Zhao, P. Xiao, I. S. Molchan, G. E. Thompson, C. Zhu,Oxidation of Metals, DOI: 10.1007/s11085-015-9602-z(2015).

367. “Microstructure and texture evolution during thermomechanicalprocessing of β-quenched Zr”, D.G. L. Prakash, M. Preuss, M. Dahlbäck, J. Quinta da Fonseca, Acta Materialia, 88, 389-401, DOI: 10.1016/j.actamat.2014.12.033 (2015).

368. “Structure and transport in coatings from multiscalecomputed tomography of coatings - new perspectives for electrochemical impedance spectroscopy modelling?”, A. Trinchi, F. Chen, Y. Yang, S. Sellaiyan, J. Carr, P. Lee, G. E. Thompson, Electrochimica Acta, 1-8, DOI: 10.1016/j.electacta.2015.10.183 (2015).

369. “Identifying suboxide grains at the metal-oxide interface of acorroded Zr-1.0%Nb alloy using (S)TEM, transmission-EBSDand EELS”, H. Jing, A. Garner, N. Ni, A. Gholinia, R. J. Nicholls,S. Lozano-Perez, F. Frankel, M. Preuss, Micron, 69, 35-42, DOI: 10.1016/j.micron.2014.10.004 (2015).

370. “In situ synthesis of PbS nanocrystals in polymer thin filmsfrom lead (ii) xanthate and dithiocarbamate complexes:evidence for size and morphology control”, McNaughter, P. D, Y. Zhongjie, Y. Chen, J. R. Brent, J. Rafferty, P. O’Brien, S. J. Haigh, G. E. Thompson, Chemistry of Materials, 27, 6,2127-2136, DOI: 10.1021/cm504765z (2015).

371. “Microscopic study of the corrosion behaviour of mild steel inionic liquids for CO2 capture applications”, G. E. Thompson,R. Lindsay, P. Skeldon, T. Schubert, J. Walton, G. Romanos, I. S. Molchan, RSC Advances, 5, 4, 35181-35194, DOI:10.1039/C5RA01097G (2015).

372. “Corrosion resistance of graphene directly and locally grownon bulk nickel substrate by laser irradiation”, F. Yu, M.Curioni, X. H. Ye, Z. Lin, H. J. Zhang, Z. Liu, M. L. Zong, RSCAdvances, 5, 45, 35384-35390, DOI: 10.1039/C5RA01267H(2015).

373. “The role of intermetallics on the corrosion initiation of twin roll cast AZ31 Mg alloy”, X. Zhou, G. E. Thompson, G. Scamans, Z. Fan, S. Pawar, Journal of the ElectrochemicalSociety, 162, 9, C442-C448, DOI: 10.1149/2.0291509jes(2015).

374. “Effects of reagent purity on plasma electrolytic oxidation oftitanium in an aluminate-phosphate electrolyte”, A. Nemcova,A. Gholinia, P. Skeldon, G. E. Thompson, S. Aliasghari,Transactions of the IMF, 94, 1, DOI:10.1080/00202967.2015.1121692 (2015).

375. “Durability and corrosion of aluminium and its alloys:overview, property space, techniques and developments”, X. Zhou, G. E. Thompson, N. L. Sukiman, N. Birbilis, A. E. Hughes, S. J. Garcia, Aluminium Alloys, New Trends in Fabrication and Applications, chapter 2, 47-98, DOI: 10.5772/53752 (2015).

376. “Continuous and discontinuous localized corrosion of a 2xxxaluminium-copper-lithium alloy in sodium chloride solution”,C. Luo, S. P. Albu, X. Zhou, Z. Sun, X. Zhang, Z. Tang and G. E. Thompson, Journal of Alloys and Compounds, 658, 61-70, DOI: 10.1016/j.jallcom.2015.10.185 (2016).

377. “The effect of aluminium on twinning in binary alpha-titanium”, A. Fitzner, D. Prakash, M. Thomas, S. Y. Zhang, J. Kelleher, P. Manuel, M. Preuss, J. Quinta Da Fonseca, Acta Materialia, 103, 341-351, DOI: 10.1016/j.actamat.2015.09.048 (2016).

378. “Effect of interfacial reaction on the mechanical performanceof steel to aluminium dissimilar ultrasonic spot welds”, P. B. Prangnell, L. Xu, L. Wang, Y. C. Chen, J. D. Robson,Metallurgical and Materials Transactions A, 334-346, DOI: 10.1007/s11661-015-3179-7 (2016).

379. “Influence of water immersion post-treatment parameters on trivalent chromium conversion coatings formed onAA2024-T351 alloy”, J. Qi, T. Hashimoto, G. E. Thompson,Journal of the Electrochemical Society, 163 (5), C131-C138,DOI: 10.1149/2.0221605jes (2016).

380. “Grain boundary segregation of rare-earth elements inmagnesium alloys”, J. D. Robson, S. J. Haigh, B. Davis, D.Griffiths, Metallurgical and Materials Transactions A, 47 (1),522-530, DOI: 10.1007/s11661-015-3199-3 (2016).

381. “Protective film formation on AA2024-T3 aluminium alloy by leaching of lithium carbonate from an organic coating”, Y. Liu, P. Visser, X. Zhou, S. B. Lyon, T. Hashimoto, M. Curioni, A. Gholinia, G. E. Thompson, G. Smyth, S. R. Gibbon, D. Graham, J. M. C. Mol, H. Terryn, Journal of theElectrochemical Society, 163, C45-C32, DOI: 10.1149/2.0021603jes (2016).

382. “Dissimilar ultrasonic spot welding of aerospace aluminiumalloy AA2139 to titanium alloy TiAl6V4”, J. D. Robson, P. B. Prangnell, C. Q. Zhang, Journal of Materials Processing Technology, 231, 382-388, DOI: 10.1016/j.jmatprotec.2016.01.008 (2016).

383. “Investigation of S phase (Al2CuMg) dealloying by highresolution 2D and 3D electron imaging”, P. Skeldon, T. Hashimoto, X. Zhang, X. Zhou, S. J. Haigh, G. E. Thompson, Corrosion Science, 103, 157-164, DOI: 10.1016/j.corsci.2015.11.013 (2016).

384. “3D imaging by serial block face scanning electron microscopyfor materials science using ultramicrotomy”, T. Hashimoto, G. E. Thompson, X. Zhou, P. J. Withers, Ultramicroscopy, 163, 6-18, 10.1016/j.ultramic.2016.01.005 (2016).

385. “Effect of low levels of sulphate on the current density andfilm morphology during anodizing of aluminium in chromicacid”, P. Skeldon, D. Elabar, T. Hashimoto, J. Qi, G. E. Thompson, Electrochimica Acta, In press (2016).

386. “Quantification of the influence of increased pre-stretching on microstructure-strength relationships in the Al-Cu-Li alloyAA2195”, P. B. Prangnell, B. I. Rogers, Acta Materialia, In press (2016).

387. “The effect of nickel on the electrochemical behaviour of AA1050 alloys in nitric acid solution”, P. Skeldon, F. J. Garcia-Garcia, G. E. Thompson, Surface and InterfaceAnalysis, In press (2016).

388. “Influence of coating morphology on adhesive bonding of titanium pre-treated by plasma electrolytic oxidation”, P. Skeldon, G. E. Thompson, A. Nemcova, S. D. Aliasghari,Surface and Coatings Technology, In press (2016).

389. “The effectiveness of hot isostatic pressing for closing porosityin titanium parts manufactured by selective electron beammelting”, P. B. Prangnell, S. Tammas-Williams, I. Todd, P. J. Withers, Metallurgical and Material Transactions. A, In press (2016).

390. “The effectiveness of combining rolling deformation withwire-arc additive manufacture on b-grain refinement and texture modification in Ti-6Al-4V”, P. B. Prangnell, J. M. Donoghue, A. A. Antonysamy, F. Martina, P. A. Colegrove, S. W. Williams, Materials Characterization, In press and online (2016).

391. “3D corrosion characterization of rheocast aluminium alloy A356-T6.1.”, P. Skeldon, B. Mingo, R. Arrabal, A. Pardo, E. Matykina, Materials Characterization, In press (2016).

conFErEncE PAPErS; PrESEnTEd And In ProcEEdIngS

1. “Friction spot welding multi-material automotive bodystructures”, P. B. Prangnell, LATEST Multi-materials Workshop,Manchester (2010).

2. “Influence of water on growth of anodic zirconium oxidenanotubes in glycerol/fluoride electrolytes”, F. Muratore, A. Baron-Wiecheć, P. Skeldon and G. E. Thompson, 61st Annual Meeting of the International Society ofElectrochemistry, Nice (2010).

3. “Uso de trazadores metálicos en el estudio del crecimiento depeláculas nanoporosas en aluminio”, S. J. Garcia-Vergara andP. Skeldon, 6th Encuentro Nacional de Materiales. Medellin,Colombia (2010).

4. “Environmentally-friendly anodizing of aluminium alloys for aerospace”, G. E. Thompson, M. Curioni, E. Koroleva, P. Skeldon, T. Hashimoto and X. Zhou, Australasian CorrosionAssociation, Corrosion and Prevention, Adelaide (2010).

5. “Electrochemical methods to assist corrosion control oflightweight alloys”, M. Curioni and G. E. Thompson,Workshop on light weight metal corrosion and modeling for corrosion prevention, Rome (2010).

6. “Quantification of microstructural homogeneity and themechanisms of particle refinement during FSP of Al-Si alloys”,C. Y. Chan and P. B. Prangnell, 8th Int. Friction Stir WeldingSymposium, Timmendorfer Strand, Germany (2010).

7. “Optimisation of short cycle time friction spot welding of thinaluminium automotive sheet”, D. Bakavos, C. Y. Chan, L. Babout, and P. B. Prangnell, 8th Int. Friction Stir WeldingSymposium, Timmendorfer Strand, Germany (2010).

8. “Energy efficient spot welding of light alloys and dissimilarmaterials”, P. B. Prangnell, Advances in Metals ManufacturingTechnology, SMEA, Sheffield (2010).

9. “Loss of high angle boundary area during annealing a cryo-SPD processed Al-alloy with a nano-scale lamellar grainstructure”, Y. Huang, G. H. Zahid and P. B. Prangnell, 4th Internaional Conference on Recrystallisation and GrainGrowth, REX&GG, Sheffield (2010).

10. “Material constitutive behaviour and microstructure study on aluminium alloys for friction stir welding”, H. Wang, P. Colegrove, H. M. Mayer, L. Campbell and R.D. Robson,Advanced Materials Research, 89-91, 615-620 (2010).

11. “Feasibility study of short cycle time friction stir spot welding thin sheet al to ungalvanised and galvanized steel”, P. B. Prangnell, Y. C. Chen, H. Farid, 8th International FrictionStir Welding Symposium, Timmendorfer Strand, Germany(2010).

12. “Influence of water on growth of anodic zirconium oxidenanotubes in glycerol/fluoride electrolytes”, The 61st AnnualMeeting of the International Society of Electrochemistry, A. Baron Wiechec, F. Muratore, P. Skeldon, G. E. Thompson,Nice, France (2010).

13. “Effect of build geometry on texture and grain structuredevelopment in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer,Thermec, Quebec (2011).

14. “Friction spot welding dissimilar materials with rapid cycletimes”, P. B. Prangnell, Y. C. Chen, F. Haddadi, N. Iqbal and J. D. Robson, Thermec, Quebec (2011).

15. “Effect of wall thickness on grain structure and texture duringadditive layer manufacturing Ti-6Al-4V by electron beamselective melting”, A. Antonysamy, P. B. Prangnell and J. Meyer,Technology developments in Titanium, Rotherham (2011).

16. “Effect of zinc coatings on joint properties and interfacereaction in aluminium to steel ultrasonic spot welding”, F. Haddadi, D. Strong and P. B. Prangnell, TMS, San Diego,Sup. Proc. Vol. 1, Materials Processing and Energy Materials,735-742 (2011).

17. “Optimisation of aluminium to magnesium ultrasonic spotwelding”, A. Panteli, Y. C. Chen, D. Strong, Xiaoyun Zhang and P. B. Prangnell, TMS, San Diego, Sup. Proc. Vol. 1,Materials Processing and Energy Materials, 735-742 (2011).

18. “Mechanisms of joint formation in ultrasonic spot weldingaluminium automotive sheet”, in symposium, D. Bakavos, Y. C. Chen and P. B. Prangnell, TMS, San Diego, Sup. Proc.Vol. 1, Materials Processing and Energy Materials, 735-742 (2011).

19. “Environmentally-friendly anodizing of aluminium alloys”, G. E. Thompson, M. Curioni, P. Skeldon, X. Zhou and E. Koroleva, 2nd International Conference on SurfaceFinishing of Light Aluminium, Paris (2011).

20. “In-situ observation and modelling of intergranular cracking in polycrystalline alumina”, Materials Structure andMicromechanics of Fracture VI, Brno, Czech Republic (2011).

21. “Application of nuclear resonance analysis and narrowresonance profiling in understanding porous film growth onaluminium”, A. Baron-Wiecheć, P. Skeldon, G. E. Thompson, J. J. Ganem and I. C. Vickridge, International Workshop on High-Resolution Depth Profiling, Paris (2011).

22. “Direct deposition of electroless Ni-P coatings on magnesiumfrom basic and acid baths”, A. Zuleta, E. Correa, M. Sepulveda, J. G. Castaño, F. Echeverría, P. Skeldon and G. E. Thompson. Presented at Eurocorr 2011, Stockholm,Sweden (2011).

23. “Direct electroless nickel-boron plating on commercial purity magnesium”, E. Correa, A. Zuleta, M. Sepulveda, J. G. Castaño, F. Echeverría, P. Skeldon and G. E. Thompson.(2011). Presented at Eurocorr 2011, Stockholm, Sweden (2011).

24. “Contamination of surfaces in mass spectrometers”, J. Doff, G. Jones, D. Douce, E.V. Koroleva, P. Skeldon and G. E. Thompson. Presented at Isranalytica, 14th AnnualMeeting of the Israel Analytical Chemistry Society. Tel Aviv, Israel (2011).

25. “Crystallographic pitting in 3XXX aluminium alloys”, A. Laferrere, N. Parson, X. Zhou and G. E. Thompson.Presented at Eurocorr. Stockholm, Sweden (2011).

26. “Hydrogen production from sodium borohydride on a Ni-Ru catalyst; an electrochemisal study”, C. M. Rangel, V. R. Fernanded, M. J. F. Ferreira, A. M. F. R. Pinto, T. Hashimoto and G. E. Thompson. Presented at 4th WorldHydrogen Technologies Convention. Glasgow (2011).

27. “Polypyrrole films on aluminium from acid electrolytes:synthesis and characterisation”, L. C. Scienza and G. E. Thompson. Presented at 27th World Congress of thePolymer Processing Society. Marrakech, Morocco (2011).

28. “Characterisation of MEA degradation for an open aircathode PEM fuel cell”, R. A. Silva, T. Hashimoto, G. E. Thompson. Presented at III Iberian Symposium onHydrogen, Fuel Cells and Advanced Batteries. Zaragoza, Spain(2011).

29. “Tomography of localised corrosion in AA2024 aluminiumalloy”, X. Zhou, C. Luo, T. Hashimoto, E. Koroleva, A. E. Hughes, G. E. Thompson and P. Withers. Presented atInternational Corrosion Congress. Perth, Australia (2011).

30. “On the impact of second phase particles on twinning inmagnesium alloys”, M. R. Barnett, N. Stanford, J. Geng, and J. D. Robson, 2011, in TMS 2011, 289-293 (2011).

31. “Effect of build geometry on texture and grain structuredevelopment in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer,Thermec, Quebec, Canada (2011).

32. “Influence of build geometry on beta grain structure andtexture during additive layer manufacture (ALM) of Ti-6Al-4Vby electron beam selective melting”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Titanium Conference (2011).

33. “Microstructure formability relationships in new generationhigh strength aluminium automotive alloys”, R. A. Nolan, M-A. Kulas, J. Quinta da Fonseca and P. B. Prangnell, Euromat(2012).

34. “Abrasion circle friction spot welding for rapid FSSW Al tosteel automotive sheet”, P. B. Prangnell, 9th InternationalSymposium on Friction Stir Welding, Huntsville, Alabama, USA(2012).

35. “Assessment by X-ray CT of the effects of geometry and builddirection on defects in titanium ALM parts”, F. Léonard, S. Tammas-Williams , P. B. Prangnell, I. Todd, P. J. Withers, inSymposium, Conference on Industrial Computed Tomography,Wels, Austria (2012).

36. “Accelerated post-weld natural ageing in ultrasonic weldingaluminium 6111-T4 automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conferenceon Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

37. “Interfacial reaction during dissimilar joining of aluminumalloy to magnesium and titanium alloys”, J. D. Robson, A. Panteli, C. Q. Zhang, D. Baptiste, E. Cai, P. B. Prangnell, In Symposium 13th International Conference on AluminumAlloys (ICAA13) Edited by: H. Weiland, A.D. Rollett, W.A. Cassada, TMS, Pittsburgh, PA (2012).

38. “Interface structure and bonding in rapid dissimilar FSSW of al to steel automotive sheet”, Y. C. Chen and P. B. Prangnell, In Symposium 13th International Conference on Aluminum Alloys (ICAA13) Edited by: H. Weiland, A. D. Rollett, W. A. Cassada, TMS, Pittsburgh, PA (2012).

39. “Optimization of anodizing cycles for enhanced performance”,M. Curioni, T. Gionfini, P. Skeldon, E. Koroleva and G. E. Thompson, ASST 2012, Italy (2012).

40. “Application of electrochemical noise analysis to corrodingaluminium alloys”, M. Curioni, R. A. Cottis and G. E. Thompson, ASST 2012, Italy (2012).

41. “Measurement of electrochemical noise: Do we really need azero resistance ammeter?”, M. Curioni, ECG-COMON 2012,Petten, Netherlands (2012).

42. “Environmentally-friendly anodizing of aluminium alloys foraerospace”, G. E. Thompson, M. Curioni, E. V. Koroleva, P. Skeldon, T. Hashimoto and X. Zhou, Corrosion andPrevention 2010, Adelaide, Australia (2010).

43. “Revealing the 3D internal structures of aluminium and its alloys”, T. Hashimoto, X. L. Zhong, M. Curioni, X. Zhou, P. Skeldon, P. J. Withers and G. E. Thompson, ASST 2012, Italy (2012).

44. “Nanotomography for understanding the dealloying ofsecond phase particles in aluminium alloys”, T. Hashimoto, X. Zhou, M. Curioni, P. Skeldon and G. E. Thompson, ASST 2012, Italy (2012).

45. “Progress of galvanic corrosion in Elektron 21 magnesiumalloy”, J. Janiec-Anwar, G. E. Thompson, X. Zhou, M. Turski, T. Wilks and T. Hashimoto, 9th International Conference onMagnesium Alloys and their Applications, Vancouver, Canada (2012).

46. “Microstructure and corrosion resistance of eximer lasermelted Elektron 21 rare-earth magnesium alloy”, A. Shekhe,Z. Liu, P. Skeldon and G. E. Thompson, 9th InternationalConference on Magnesium Alloys and their Applications,Vancouver, Canada (2012).

47. “Thermal modelling of Al-Al and Al-steel friction stir spotwelding”, P. Jedrasiak, A Reilly, H. R. Shercliff, G. J. McShane,Y. C. Chen and P. B. Prangnell, In Mathematical Modelling ofWeld Phenomena 10, Austria (2012).

48. “Novel approaches to modelling metal flow in friction stir spotwelding”, A Reilly, H.R. Shercliff, G.J. McShane, Y. C. Chenand P. B. Prangnell, In Mathematical Modelling of WeldPhenomena 10, Austria (2012).

49. “Assessment of the advantages of static shoulder FSW forjoining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, and P. B. Prangnell, Thermec, Las Vegas, USA (2013).

50. “Estudio del proceso de formacion de recubrimientoselectroless Ni-P sobre el magnesio”, A. Zuleta, E. Correa, M. Sepulveda, L. Guerra, J. G. Castano, F. Echeverria, P. Skeldon and G. E. Thompson, Congresso Internacional deMateriales, Medellin, Colombia (2013).

51. “Enhanced photo- and under X-ray luminescence fromXerogels embedded in mesoporous anodic alumina”, N.Gaponenko, V. Kortov, V. Pustovarov, S. Zvonarev, A. Slesarev,M. V. Rudenko, L. S. Khoroshko, A. M. Asharif, I. Molchan, G. E. Thompson, A. Podhorodecki, J. Misiewicz, and S. Prislopskii, International Porous and Powder MaterialsSymposium, Turkey (2013).

52. “A study of mixed inhibitors for corrosion protection ofAA2024 T3 aluminium alloy”, A. C. Balsakas, M. Curioni, G. E. Thompson and G. Kordas, Eurocorr, Estoril, Portugal (2013).

53. “Corrosion testing of aerospace components byelectrochemical noise analysis”, M. Curioni, Z. Wang, A. C. Balaskas, E. Rahimi and G. E. Thompson, Eurocorr,Estoril, Portugal (2013).

54. “Reliability of noise resistance for the estimation of corrosionrate”, M. Curioni and G. E. Thompson, Eurocorr, Estoril,Porugal (2013).

55. “Influence of galvanized coatings on abrasion circle frictionstir spot welding aluminium to steel for automotiveapplications”, Y. C. Chen, S-F Liu and P. B. Prangnell, Thermec (2013).

56. “Mechanical and microstructural characterization ofpercussive arc welded hyper-pins for titanium to compositemetal joining, in LMT2013”, R. J. Oluleke, D. Strong, O. Ciuca, J Meyer, A. De Oliveira and P. B. Prangnell, 6th Int.Symp. on Light Metals Technology (2013).

57. “The effect of temperature on the formability of a highstrength aluminum automotive”, R. A. Nolan, M-A. Kulas, P. B. Prangnell, J. Quinta da Fonseca, MS&T 2013, MaterialsScience and Technology 2013, Montreal, Canada (2013).

58. “Grain structure evolution in alumnium to steel ultrasonic spot welding”, F. Haddadi, P. B. Prangnell, MS&T 2013,Montreal, Canada (2013).

59. “Advanced aluminium extrusion technology”, McCool, N. S. Malone, J. O’Connor, P. Howe, S. Mills, G. E. Thompson,Y. Liu, X. Zhou, M. Curioni, E. McAlpine, G. Scamans, C. Butler, Aluminium International Today (2013).

60. “Friction welding of titanium alloys: addressing the structuralintegrity issues through process optimization”, M. M Attallah,M. Preuss, S. E. Bray, Proceedings of the 1st International JointSymposium on Joining and Welding, Osaka, Japan, 313-315,DOI: 10.1533/978-1-78242-164-1.313 (2013).

61. “The effect of aluminium on deformation and twinning inalpha titanium: the 45° case”, A. Fitzner, D. G. Prakash, J. Quinta da Fonseca, M. Preuss, M. J. Thomas, S. Y. Zhang,Materials Science Forum, 765, 549-553 (2013).

62. “3D characterisation of short fatigue crack in titanium”, S. Birosca, F. A. Garcia-Pastor, M. Karadge, J. Y. Buffiere, M. Preuss, 6246, ICF12, Ottawa (2009), published (2013).

63. “Measurement of strain and lattice rotation in the particledeformation zone”, L. C. L. Ko and J. Quinta da Fonseca,Materials Science Forum, 753, 21-24 (2013).

64. “Assessment of the advantages of static shoulder FSW forjoining aluminium aerospace alloys”, H. Wu, Y. C. Chen, D. Strong, P. B. Prangnell, THERMEC 2013, Las Vegas, USA (2013).

65. “The effect of chloride as catalyst layer contaminant on the degradation of PEMFCs”, T. I. Pavia, T. Hashimoto, M. J. Plancha, G. E. Thompson, C. M. Rangel, IV IberianSymposium on Hydrogen, Fuel Cells and Advanced Batteries,Estoril, Portugal, June (2013).

66. “Terbium luminescence under X-rays from YAlO3 compositedeposited on porous anodic alumina”, N. V. Gaponenko , V. S. Kortov, V. A. Pustovarov , L. S. Khoroshko, A. M. Asharif,I. S. Molchan, G. E. Thompson, A. Podhorodecki, G. Zatrub, J. Misiewicz, Microwave and TelecommunicationTechnology (CriMiCo), 23rd International CrimeanConference, Crimea, Ukraine (2013).

67. “Effect of strain rate on the evolution of dispersoid particles in Al-Mn-Fe-Si Alloy during hot deformation”, T. Hill, J. D. Robson, N. Kamp, Light Metals Technology 2013, UK (2013).

68. “Constituent particles and dispersoids in an Al-Mn-Fe-Si alloystudied in three-dimensions by serial sectioning”, L. Dwyer, J. D. Robson, J. Quinta da Fonseca, N. Kamp, T. Hashimoto,G. E. Thompson, Light Metals Technology 2013, UK (2013).

69. “Reducing mechanical asymmetry in wrought magnesiumalloys”, J. D. Robson, Light Metals Technology 2013, UK (2013).

70. “Controlling interfacial reaction during dissimilar metalwelding of aluminium alloys”, L. Wang, Y. Wang, C. Zhang, L. Xu, J. D. Robson and P. B. Prangnell, Materials ScienceForum, 794-796, 416-42 (2014).

71. “Systematic evaluation of the advantages of static shoulderfsw for joining aluminium”, H. Wu, Y. C. Chen, D. Strong andP. B. Prangnell, Materials Science Forum, 794-796, 407-412(2014).

72. “Effect of grain boundary diffusion on growth kinetics ofintermetallic compounds between Al alloys and other alloys”,L. Wang, Y. Wang, L. Xu, C. Zhang, J. D. Robson and P. B.Prangnell, Materials Science & Technology Conference andExhibition 2014, Pittsburgh, PA, 1851-1858 (2014)

73. “Assessment of rapid refill FSSW for 6111-T4 aluminiumautomotive alloys”, B. Mohysen Al-Zubaidy, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir WeldingSymposium, Beijing, China, Publ. TWI, On CD (2014)

74. “Dissimilar friction spot welding of aluminium andmagnesium for automotive applications using novelapproaches - abrasion circle FSSW and refill FSSW”, Y. C. Chen, B. Mohysen Al-Zubaidy and P. B. Prangnell in 14th International Friction Stir Welding Symposium, Beijing,China, Publ. TWI On CD (2014).

75. “Analysis of the advantages of stationary shoulder friction stirwelding in near-net shape joining high strength aerospacealuminium alloy AA7050-T7651”, H. Wu, Y. C. Chen and P. B. Prangnell, 14th International Friction Stir WeldingSymposium, China, Publ. TWI On CD (2014).

76. “Corrosion behaviour of magnesium electrodes investigatedby real-time hydrogen measurement”, M.Curioni, T.Monettaand F.Bellucci, Proceedings of Eurocorr (2014).

77. “A unique approach of GDOES for improving scanningelectron microscopic imaging”, K. Kawano, K. Shimizu and G. E. Thompson, GD Day 2014 Symposium, Horiba, France(2014).

78. “The influence of hot forming on the microstructure and corrosion behaviour of AZ31B magnesium alloys”, A. Juliawati, X. Zhou, G. E. Thompson, O. E Fakir and J. Dear, Eurocorr, Pisa, Italy (2014).

79. “A new model for discontinuous and continuous precipitationin AZ91 magnesium alloy”, J. D. Robson, Materials ScienceForum 783, 461-466 (2014).

80. “The impact of machining on the corrosion behaviour ofAA7150-T651 aluminium alloy”, B. Liu and X. Zhou, Materials Science Forum, 794-796, 217-222 (2014).

81. “Texture evolution during wire drawing of Mg-RE alloy”, M. Chatterton, J. D. Robson, D. Henry, MagnesiumTechnology Symposium, TMS 2014, San Diego, USA (2014).

82. “The effect of temperature on the formability of a highstrength aluminium automotive”, P. Prangnell, R. Nolan, J. Quinta Da Fonseca, M. A. Kulas, Materials Science andTechnology 2014, Pittsburgh, USA (2014).

83. “Porous anodic oxides for corrosion protection of aerospacealloys: microstructure optimization and evaluation ofperformance“, M. Curioni, A. Balaskas, P. Skeldon and G. E. Thompson, ASST 2015, Madeira, Portugal (2015).

84. “The propagation of localized corrosion in Al-Cu-Li alloy”, X. Zhang, X. Zhou, Y. Ma, G. E. Thompson, C. Luo, Z. Sun, and Z. Tang, Proceedings of the 7th International Conferenceon Aluminium Surface Science and Technology, Madeira,Portugal (2015).

85. “Correlation between localized plastic deformation andlocalized corrosion in AA2099 aluminium-lithium alloy”, W. Huang, Y. Ma, X. Zhou, X. Meng, Y. Liao, L. Chai, Y. Yi, X. Zhang, Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira,Portugal (2015).

86. “Microstructural origin of localized corrosion in anodizedAA2099-T8 aluminium-lithium alloy”, Y. Ma, X. Chen, X. Zhou, Y. Yi, Y. Liao, W. Huang, Proceedings of the 7th

International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

87. “Influences of sulphur impurity on chromic acid anodizing”,D. Elabar, A. Nemcova, P. Skeldon, G. E. Thompson,Proceedings of the 7th International Conference on Aluminium Surface Science and Technology, Madeira, Portugal (2015).

88. “In-situ high temperature EBSD analysis of the effect of adeformation step on the alpha to beta transition in additivemanufactured Ti6Al4V”, J. M. Donoghue, J. Quinta Da Fonsecaand P. B. Prangnell, Ti-2015: The 13th World Conference onTitanium, On CD (2015).

89. “The origin and implications of microstructural banding inadditive manufacture with Ti6Al4V by plasma wiredeposition”, H. Zhao, J. M. Donoghue, S. Tammas-Williamsand P. B. Prangnell, Ti-2015: The 13th World Conference onTitanium, On CD (2015).

90. “Predicting the influence of porosity on the fatigueperformance of titanium components manufactured byselective electron beam melting”, S. Tammas-Williams, J. Donoghue and P. B. Prangnell, Ti-2015: The 13th WorldConference on Titanium, On CD (2015).

91. “Automated multi-scale microstructure heterogeneity analysisof selective electron beam melted TiAl6V4 components”, H. Zhao, A. A. Antonysamy, J. Meyer, O. Ciuca, S. W. Williamsand P. B. Prangnell, TMS 2015, Additive ManufacturingSymposium, Supplementary Proceedings, 429-435, DOI: 10.1002/9781119093466.ch54 (2015).

92. “Integration of deformation processing with additivemanufacture of Ti-6Al-4V components for improved β grainstructure and texture, additive manufacturing”, J. Donoghue,J. Sidhu, A. Wescott and P. B. Prangnell, TMS 2015, AdditiveManufacturing Symposium Supplementary proceedings, 437-444, DOI: 10.1002/9781119093466.ch55 (2015).

93. “Coating design for controlling phase IMC formation indissimilar Al-Mg metal welding, friction stir welding andprocessing symposium VIII”, Y. Wang, L. Wang, J. D. Robson,B. M. Al-Zubaidy and P. B. Prangnell, 171-179, TMS, DOI: 10.1002/9781119093343.ch19 (2015).

94. “In-situ high temperature EBSD analysis of the effect of adeformation step on the alpha to beta transition in additivemanufactured Ti6Al4V”, P. B. Prangnell, J. M. Donoghue, J. Quinta Da Fonseca, Ti-2015: The 13th World Conference on Titanium, San Diego, CA (2015).

95. “Effect of sulphate impurity in chromic acid anodizing of aluminium”, P. Skeldon, D. Elabar, A. Nemcova, G. E. Thompson, 7th International Conference on AluminiumSurface Science and Technology, Madeira, Portugal (2015).

96. “Effect of ionic fluids with imidazolium and lactam-basedcations on corrosion of mild steel”, I. S. Molchan, G. E. Thompson, P. Skeldon, R. Lindsay, G. Romanos,International Forum on Recent Developments of CCSImplementation, Athens, Greece (2015).

97. “Microstructural origin of localized corrosion in anodizedAA2099-T8 aluminium-lithium alloy”, X. Zhou, Y. Ma, X. Chen, Y. Yi, Y. Lao, W. Huang, 7th InternationalConference on Aluminium Surface Science and Technology,Madeira, Portugal (2015).

98. “Effect of microstructure on the tensile strength of Ti6Al4Vspecimens manufactured using Additive ManufacturingElectron Beam Process”, P. B. Prangnell, T. Machry, D. Eatock,J. Meyer, A. A. Antonysam, A. Ho, Euro PM2015 Congressand Exhibition, Reims, France (2015).

99. “Effect of microstructure on the tensile strength of Ti6Al4Vspecimens manufactured using Additive ManufacturingElectron Beam Process”, P. B. Prangnell, T. Machry, D. Eatock,J. Meyer, A. A. Antonysam, A. Ho, Euro PM2015 Congressand Exhibition, Reims, France. In press (2016).

PrESTIgE,  AwArdS And InVITEd LEcTurES

Professor G. E. ThompsonDescription of Membership: Fellow, Royal Academy of Engineering (FREng)Date Applicable: Annually

Professor G. E. ThompsonDescription of Membership: Fellow, Electrochemical Society, New Jersey, USA(FECS)Date Applicable: Annually

Professor G. E. ThompsonDescription of Membership: Fellow, Institute of Materials, Minerals andMining (FIMMM)Date Applicable: Annually

Professor G. E. ThompsonDescription of Membership: Fellow, Institution of Corrosion (FICorr)Date Applicable: Annually

Professor G. E. ThompsonDescription of Membership: Fellow, Institute of Metal Finishing (FIMF)Date Applicable: Annually

Professor P. B. PrangnellDescription of Membership: Thermec Conference OrganisationDate Applicable: Annually

Professor J. D. RobsonDescription of Membership: EPSRC College Peer reviewDate Applicable: Annually

Professor M. PreussDescription of Membership: Member of the ILL Sub-Committee for theUpgrade Endurance Programme Date Applicable: Annually

Professor M. PreussDescription of Membership: Chair of the Science and Technology AdvisoryPanel a New Engineering Instrument at the European Spallation Source,Lund, SwedenDate Applicable: Annually

Professor M. PreussDescription of Membership: Member of the ILL Scientific CouncilDate Applicable: Annually

Professor G. E. ThompsonDescription of Membership: Editorial Board Member of Corrosion ScienceDate Applicable: 1992 – Present

Professor G. E. ThompsonDescription of Membership: Editorial Board Member of Anti Corrosion Methods and MaterialsDate Applicable: 1997 – Present

Professor G. E. ThompsonDescription of Appointment: Officer of the Order of the British Empire (OBE)for research activities of relevance to the defence industries June 2000

Professor G. E. ThompsonDescription of Membership: Editorial Board Member of Electroplating andFinishingDate Applicable: 2005 – Present

Professor J. D. RobsonDescription of Membership: Light Metals Board, IOM3Date Applicable: 2005 - Present

Professor M. PreussDescription of Membership: Titanium Information Group (TIG) MemberDate Applicable: 2009 - Present

Dr M. CurioniDescription of Membership: Member of NACE InternationalDate Applicable: 2009 – present

Dr M. CurioniDescription of Membership: Member of Electrochemical SocietyDate Applicable: 2009 – present

Professor M. PreussDescription of Membership: EPSRC College for Reviewing ProposalsDate Applicable: 2010 - Present

Professor P. SkeldonDescription of Membership: Member of the Electrochemical SocietyDate Applicable: 2010 - present

Professor P. SkeldonDescription of Membership: Member of the Electrochemical SocietyDate Applicable: 2010 - present

Professor J. D. RobsonDescription of Membership: Manchester Metallurgical Society (Vice President)Date Applicable: 2011 - Present

Professor M. PreussEditorial Role: Section Editor of Encyclopaedic for Aerospace Engineeringcovering High Temperature MaterialsDate Applicable: Dec 2011 - ongoing

Professor J. D. RobsonDescription of Membership: Co-chair and Organizer of Magnesium Technology Symposium, EuroMatDate Applicable: 2011

Professor X. ZhouDescription of Membership: Ontario Centre of Excellence Assessment PanelDate Applicable: 2012

Professor X. ZhouDescription of Election: Elected Fellow for the Institute of MaterialsDate Elected: August 2012

Professor X. ZhouDescription of Election: Elected Fellow for the Institute of CorrosionDate Elected: April 2012

Professor X. ZhouDescription of Membership: International Advisory Panel, 9th InternationalConference on Magnesium Alloys and their Applications, Vancouver, CanadaDate Applicable: 2012

Professor X. ZhouDescription of Membership: ICAA14 International Organizing CommitteeMemberDate Applicable: 2012 - 2014

Dr J. Quinta Da FonsecaDescription of Election: Election to ISIS Beam Time Access PanelDate Elected: August 2012 for 2 years

Dr M. CurioniDescription of Membership: Member of Institute of Corrosion Date Applicable: 2012 – present

Professor G.E.ThompsonDescription of Membership: International Organising Committee Memberfor ASST Conference 2014.Date Applicable: 2013

Professor G. E. ThompsonDescription of Membership: Member of the Scientific Board, Advances inMaterials Science Date Applicable: 2013 – present

Dr J. Quinta Da FonsecaDescription of Membership: Advanced Sheet Forming committee of the IOM3Date Applicable: 2013 – present

Professor M. PreussDescription of Membership: Member of the Scientific Advisory CommitteeLaboratory Nuclear Materials at the Paul Scherrer Institute, Switzerland. Date Applicable: 2013 – present

Professor M. PreussDescription of Membership: Member of the Jules Horowitz Test Reactor UKsteering committee. Date Applicable: 2013 – present

Professor P. B. PrangnellDescription of Membership: Light Metals Session Chair: Euromat 2015Date Applicable: Sept 2015

Professor X. ZhouDescription of Membership: IOM3 Light Metals Board Date Applicable: 2015 – present

Prestige

Awards

Professor J. D. RobsonDescription of Award: IOM3 Grunfeld Memorial Award and Medal 2011Awarding Body: IOM3Date Awarded: March 2011

Dr A. Antonysamy Description of Award: Winner of the Best Research Poster at the 'National Level Conference on Technology Developments in Titanium' Awarding Body: Titanium Information Group TIG-UK Date Awarded: April 2011

Dr J. WangDescription of Award: 1st Prize in the EPSRC LATEST2 Symposium PosterCompetition 2011Awarding Body: The University of ManchesterDate Awarded: May 2011

Dr K. LiDescription of Award: 1st Prize in The University of Manchester PGR Conference Poster Competition 2011Awarding Body: The University of Manchester Date Awarded: May 2011

Dr K. LiDescription of Award: 3rd Prize in Young Lecture Competition 2012Awarding Body:IOM3 North WestDate Awarded: March 2012

Dr A. Lafferrere and Mr J. SmithDescription of Award: IOM3 Colin Humphrey’s Education Award 2012 Awarding Body: IOM3 Date Awarded: March 2012

Dr A. NěmcováDescription of Award: 1st Prize in the 15th International Corrosion andCorrosion Protection of Metals Conference Poster CompetitionAwarding Body: ICCPMDate Awarded: October 2012

Dr C. ZhangDescription of Award: 1st Prize in the EPSRC LATEST2 Researcher SymposiumPoster Competition 2012 Awarding Body: The University of ManchesterDate Awarded: October 2012

Ms B. LiuDescription of Award: 3rd Prize in Young Lecture Competition 2013Awarding Body: IOM3 Date Awarded: March 2013

Professor M. PreussDescription of Award: IOM3 Grünfeld Memorial Award and Medal 2013Awarding Body: IOM3Date Awarded: March 2013

Dr. J. Janiec-AnwarDescription of Award: 3rd Prize in The University of Manchester PGR Conference Poster Competition 2013Awarding Body: The University of Manchester Date Awarded: May 2013

Dr. C. ZhangDescription of Award: 2nd Prize in The University of Manchester PGRConference Poster Competition 2013Awarding Body: The University of Manchester Date Awarded: May 2013

Ms B. LiuDescription of Award: 1st Prize in The University of Manchester PGR Conference Poster Competition 2013Awarding Body: The University of Manchester Date Awarded: May 2013

Dr M. Curioni, Professor P. Skeldon and Professor G. E. ThompsonDescription of Award: Co-recipients of the Jim Kape Memorial Medal of theInstitute of Metal Finishing 2013Awarding Body: IOM3 Date Awarded: August 2013

Mr A. BalaskasDescription of Award: 2nd Prize in the Materials Research Exchange PosterCompetition 2014Awarding Body: Materials KTN CoventryDate awarded: February 2014

Dr. David GriffithsDescription of Award: Materials Literature Review Prize of IOM3 Awarding Body: IOM3 Date awarded: March 2014

Ms B. LiuDescription of Award: 1st Prize, Poster Competition, The 14th InternationalConference on Aluminium AlloysAwarding Body: ICAA14Date awarded: June 2014

Professor G. E. ThompsonDescription of Award: Doctor Honoris CausaAwarding Body: Universidad de Santiago de ChileDate awarded: November 2014

Professor J. D. RobsonDescription of Award: 2015 Hume-Rothery PrizeAwarding Body: IOM3Date awarded: July 2015

Dr Alphons Antonysamy receiving his award for best research poster at the 'National Level Conference on Technology Developments in Titanium', on behalf of the Chairman of the Titanium Information Group

Professor George Thompson receiving the degree of “Doctor Honoris Causa” from the University of Santiago de Chile

Professor J. D. RobsonInvited Lecture: PRICM Conference, Cairns, Australia (August 2010)

Professor J. D. RobsonInvited Lecture: IPSUS Summer School, Germany (August 2010)

Professor J. D. RobsonInvited Lecture: OPTIMoM Conference, Cambridge, UK (September 2010)

Professor J. D. RobsonInvited Lecture: MagNet Conference, Canada (October 2010)

Professor G. E. ThompsonInvited Lecture: “Reducing the energy cost of anodizing”, AustralasianCorrosion Association, Melbourne, Australia (November 2010)

Professor G. E. Thompson Plenary Lecture: “Environmentally-friendly anodizing of aluminium alloys foraerospace”, Corrosion and Prevention Conference, Adelaide, Australia(November 2010)

Professor M. PreussInvited Lecture: “So you think you understand deformation in metals?”Imperial College London, UK (January 2011)

Professor J. D. RobsonInvited Lecture: Thermec Conference, Quebec, Canada (August 2011)

Professor P. B. PrangnellInvited Lecture: “Friction spot welding dissimilar materials with rapid cycle times”, Thermec, Quebec, Canada (August 2011)

Professor P. B. PrangnellInvited Lecture: “Effect of build geometry on texture and grain structuredevelopment in additive layer manufacture (ALM) of Ti-6Al-4V”, Thermec,Quebec, Canada (August 2011)

Professor J. D. RobsonInvited Lecture: EuroMat Conference, France (September 2011)

Professor J. D. RobsonInvited Lecture: European Conference on Aluminium Alloys (ECAA), Germany (October 2011)

Professor G. E. ThompsonInvited Lecture: “Environmentally-friendly anodizing of aluminium alloys”, 2nd International Conference on Light Metal Surface Finishing, Paris, France(November 2011)

Professor X. Zhou Invited Lecture: “Nanotomography of localised corrosion in aluminium alloys”,The Australian Research Council (ARC) Centre of Excellence for Design in LightMetals Annual Conference, Melbourne, Australia (November 2011)

Professor G. E. ThompsonPlenary Lecture: “Fundamental studies to assist development ofenvironmentally-friendly anodizing treatments on aluminium alloys”, China(Ningbo) International Forum on Advanced materials and Commercialization,Ningbo (December 2011)

Professor X. ZhouInvited Lecture: “Electron tomography of aluminium alloys”, Constellium,Grenoble, France (December 2011)

Professor P. B. Prangnell“Effect of build geometry on texture and grain structure development in additive layer manufacture (ALM) of Ti-6Al-4V”, A. A. Antonysamy, P. B. Prangnell and J. Meyer, Thermec 2011, Quebec, Canada, MaterialsScience Forum, V706-709, 205-210,doi:10.4028/www.scientific.net/MSF.706-709.205 (2012)

Professor G. E. ThompsonPlenary Lecture: “Fundamental studies to assist development ofenvironmentally-friendly coatings on aluminium alloys”, Materials Science and Engineering Symposium, Doha, Qatar (February 2012)

Professor X. ZhouInvited Lecture: “Near-surface microstructure and anodic film growth on aluminium alloys”, Sapa Technology Centre, Sapa Group (February 2012)

Professor J. D. RobsonInvited Lecture: The Minerals, Metals and Materials Society (TMS), Florida, USA(March 2012)

Professor M. PreussInvited Lecture: “Variant selection in titanium alloys”, Titanium EuropeanConference, Bristol, UK (March 2012)

Professor X. Zhou Invited Lecture: “Corrosion control of aluminium alloys for aircraftapplication”, The 2nd International Symposium on Aeronautical Engineering,Santiago, Chile (March 2012)

Professor G. E. ThompsonInvited Lecture: “In-SEM tomography (nano- and micro-tomography with3View and XuM capabilities)”, FESI-UK Forum for Engineered StructuralIntegrity Conferences and Related Continuing Professional Development,Manchester, UK (April 2012)

Professor G. E. ThompsonInvited Lecture: “Revealing the three dimensional internal structure ofaluminium alloys”, Aluminium Surface Science and Technology Symposium(ASST VI), Sorrento, Italy (May 2012)

Professor J. D. RobsonInvited Lecture: Magnesium Technology Conference, Canada (July 2012)

Professor J. D. RobsonInvited Lecture: Welding Summer School, Leicester, UK (August 2012)

Professor X. Zhou Invited Lecture: “Initiation and propagation of IGC in AA2xxx aluminiumalloys”, Airbus, UK (August 2012)

Professor M. PreussInvited Lecture: “Titanium and related research - materials performance”, Bao steel and IMR, Shenyang, China (September 2012)

Dr J. Quinta da FonsecaInvited Lecture: IMR, Shenyang, China (September 2012)

Professor X. ZhouInvited Lecture: “New observation of intergranular corrosion in aluminiumalloy”, The 16th Asian Pacific Corrosion Control Conference, Kaohsiung,Taiwan (October 2012)

Dr J. Quinta da FonsecaInvited Lecture: IOM3, Surrey, UK (October 2012)

Professor X. ZhouInvited Lecture: “Nanotomography of Localized Corrosion in AluminiumAlloys”, China State Key Laboratory for Marine Corrosion and Protection,Beijing, China (November 2012)

Dr J. Quinta da FonsecaInvited Lecture: IOM3, Surrey, UK (December 2012)

Professor P. B. Prangnell“Loss of high angle boundary area annealing a cryo-spd processedaluminium ally with a nano-scale lamellar grain structure”, Y. Huang, G. H. Zahid and P. B. Prangnell, 4th International Conference onRecrystallisation and Grain Growth, REX&GG, Sheffield, UK, MaterialsScience Forum, 715-716, 219-226 (2012)

Professor J. D. RobsonInvited Lecture: Constellium CRV, Grenoble, France (January 2013)

Professor M. PreussInvited Lecture: “Variant selection in titanium alloys”, BARC seminar series,Mumbai, India (February 2013)

Professor G. E. ThompsonInvited Lecture: “Presentation of LATEST2 to Light Metals Workshop withBrunel University” Uxbridge, UK (April 2013)

Professor J. D. RobsonInvited Lecture: Magnesium Technology Workshop, Madrid, Spain (May 2013)

Professor X. ZhouPlenary Lecture: “New development in research for corrosion resistant film onaluminium alloys”, The 3rd International Conference, Aluminium 21-Coatings,St Petersburg, Russia (June 2013)

Dr J. Quinta da FonsecaInvited Lecture: Constellium, Grenoble, France (June 2013)

Professor G. E. ThompsonPlenary Lecture: “Development of environmentally-friendly anodizingconditions”, Italian Metallurgical Society, Naples, Italy (July 2013)

Invited Lectures

Professor J. D. RobsonInvited Lecture: Light Metals Technology Conference, Windsor, UK (July 2013)

Professor X. ZhouInvited Lecture: “Environmentally-friendly surface treatment for Al-Li alloy”, Beijing Institute of Aeronautical Materials, Beijing, China (August2013)

Professor X. ZhouInvited Lecture: “Grain boundary precipitation and corrosion behaviour of Al-Li alloy”, Constellium, Grenoble, France (September 2013)

Professor X. ZhouInvited Lecture: “Electrochemical methods and surface analysis in corrosion research”, Vrije Universiteit Brussel, Belgium (September 2013)

Professor G. E. ThompsonInvited Lecture: “LATEST2 programme grant activities”, Light Metals Board,Institute of Materials, Minerals and Mining, London, UK (September 2013)

Professor M. PreussInvited Lecture: “Fundamental deformation mechanisms in Ni superalloys”Rolls-Royce, Derby, UK, (September 2013)

Professor G. E. ThompsonInvited Lecture: “Overview of recycling research at TARF-LCV meeting”,Coventry, UK (October 2013)

Professor J. D. RobsonInvited Lecture: “A new model for discontinuous and continuous precipitationin AZ91 magnesium alloy”, Thermec Conference, USA (December 2013)

Professor G. E. ThompsonInvited Lecture: “Environmentally-friendly anodizing of aluminium alloys”,Hatfield Memorial Lecture, Sheffield, UK (December 2013)

Professor P. B PrangnellInvited Lecture: “Assessment of the advantages of static shoulder FSW for joining aluminium aerospace alloys”, Thermec, Las Vegas, USA (December 2013)

Professor M. PreussInvited Lecture: “Effect of macrozones and alloying chemistry on strainheterogeneity in titanium alloys”, TMS, San Diego, California, USA (February 2014)

Professor P. B. PrangnellKeynote opening address: “Antonysamy, EBSD analysis to understand additivemanufacturing (3D printing) in titanium: RMS – Electron Backscatter DiffractionMeeting”, London (March 2014)

Professor M. PreussInvited Lecture: “Fundamentals of titanium alloys in context of dwell fatigue”,CECAM, Lugano, Switzerland (April 2014)

Professor J. D. RobsonInvited Lecture: "The effect of hot deformation on dispersoid evolution in amodel 3xxx alloy”, ICAA14, Norway (June 2014)

Professor X. ZhouInvited Lecture: “Anodic film formation on new generation aerospacealuminium alloys”, The 65th Annual Meeting of the International Society of Electrochemistry, Lausanne, Switzerland (August 2014)

Professor M. PreussInvited Lecture: “Irradiation growth mechanisms in Zr alloys studied byultrahigh resolution EDX spectrum imaging and synchrotron x-ray diffraction”,Zirconium Workshop, Oxford, UK (September 2014)

Professor M. PreussInvited Lecture: “Irradiation growth mechanisms in Zr alloys studied byultrahigh resolution EDX spectrum imaging and synchrotron x-ray diffraction”,European MRS, Warsaw, Poland (September 2014)

Professor J. D. RobsonInvited Lecture: “Microstructural modelling for design of magnesium alloys”,OPTIMoM conference, Pembroke College, Oxford, UK (September 2014)

Professor G.E ThompsonInvited Lecture: “Manchester materials activities and LATEST2 review toUSACH”, Santiago, Chile (November 2014)

Professor J. D. Robson“Improving formability and joining of light alloys through metallurgicalunderstanding”, Advanced Engineering Open Conference 2014, Birmingham, UK (2014)

Dr T. Burnett“Understanding engineering failures from the component-scale to the nano-scale using 3D imaging”, Advanced Engineering Open Conference 2014,Birmingham, UK (2014)

Dr J. Quinta da FonsecaInvited Lecture: “The evolution of deformation patterning in two FCC metalswith difference stacking fault energies” TMS 2015, Orlando, USA (March 2015)

Professor G. E. ThompsonInvited Lecture: “Influences of sulphur impurity on chromic acid anodizing”,Aluminium Surface Science and Technology (ASST VII), Madeira, Portugal (May 2015)

Dr M. CurioniInvited Lecture: ‘’Looking closely at magnesium corrosion: electrochemicalmethods, real-time optical imaging and hydrogen measurement’’, 17th TopicalMeeting of the International Society of Electrochemistry (Multiscale Analysis ofElectrochemical Systems), Saint-Malo, France (June 2015)

Professor X. ZhouInvited Lecture: “Tailoring aluminium alloy surface for transportationapplications”, The 1st America’s Conference on Aluminium alloys, Toronto,Canada (August 2015)

Dr J. Quinta da Fonseca Keynote Lecture: “ The kinematics of deformation and the development ofsubstructure in the particle deformation zone” Risoe International Symposium(September 2015)

Professor M. PreussInvited Lecture: “A study of early deformation twinning in a titanium alloy by x-ray diffraction contrast tomography”, MS&T, Columbus, Ohio, USA(October 2015)

Professor X. Zhou Invited lecture: “Tailoring the surface of light alloys for adhesive bonding and painting”, 5th Global Automotive Lightweight Materials conference,Birmingham, UK (April 2016)

Professor X. Zhou Invited lecture: “Corrosion and protection of lightweight automotive alloys”,International Conference Automotive Corrosion Protection, Berlin, Germany(February 2016).

Professor X. Zhou delivering an invited lecture on “Nanotomography of Localised Corrosion in Aluminium Alloys”.

humAn cAPITAL ImPAcT

A high priority for the EPSRC LATEST2 Programme Grant was to help addressthe skills gap in metallurgical and corrosion science training, to contribute tothe future generation skills base for academia and industry and to help provide the globally competitive and innovative materials engineers needed by the UKmanufacturing sector.

During the lifetime of the award, there was on going development andprogression of both students and researchers. Specifically, one of our Co-Investigators has been awarded an EPSRC Leadership Fellowship andpromoted to Professor of Metallurgy. A second has been promoted to Reader, and then Professor, a third has been promoted to Senior Lecturer and then Professor, and one of our Post Doctoral Researchers has beenpromoted to LATEST2 Research Fellow and then Lecturer, in recognition of their achievements.

The EPSRC LATEST2 Programme Grant has successfully attracted high qualitystudents and researchers, the majority of whom are now progressing with their careers either within academia or within industry.

On the following pages are some examples of profiles of the early careersdestinations of LATEST2 students and researchers.

During my Bachelors degree in metallurgicalengineering at Periyar University in India, Ideveloped an interest in metallurgicalengineering. After graduating I began myworking career as a ‘Metallurgical Processand Quality Control Engineer’ at TVS BrakesIndia Ltd, Foundry Division, Tamilnadu.After 2 years of Foundry experience, I hadthe opportunity to pursue my Mastersdegree at IIT kharagpur with sponsorshipfrom the Ministry of Human ResourceDevelopment of India, where I gained an in-depth understanding of Metallurgical andMaterials Sciences. I was awarded a DAADscholarship to complete my one yearmaster’s research project at the TechnicalUniversity-Dresden, Germany as a Sandwichprogramme between IIT-India and GermanyUniversities. After completing my Mastersdegree, I worked at Renault-NissanTechnology and Business Centre, India as aMaterials Engineer/Specialist. After workingto standards and specifications set bymaterial scientists, I realised that I stilllacked knowledge of what factors defineand restrict metallic materials in real timeengineering applications. This in fact,stimulated me to pursue a research coursefocused on advanced manufacturingprocesses and materials and hence I choseto pursue my PhD in the reputed Universityof Manchester on the fast growingtechnology of Additive Manufacturing ofTi6Al4V alloys which was sponsored by theEPRSC LATEST Programme Grant, and EADSInnovations Work, UK.

Specifically, my thesis was focused on‘Microstructure, Texture and MechanicalProperty Evolution during AdditiveManufacturing of Ti6Al4V Alloy forAerospace Applications’. I enjoyed theresearch environment, technical advice and experimental help offered by myProfessor/Advisor, laboratory technicians,and more importantly the advancedfacilities which were made available to me within the School of Materials at TheUniversity of Manchester. I worked utilisedthe SEM-EBSD, high resolution 3D x-raytomography, high resolution Megellam SEM(which could replace high resolution TEMimaging capability), x-ray diffraction forresidual stress and texture analysis, tensiletesting, etc. During my PhD I had theopportunity to work closely with keyindustrial partners such as EADS-Airbus(collaborator for PhD work), BombardierAerospace, TWI, Timet, etc. I also had theopportunity to collaborate with otheruniversities such as Cranfield University (via RUAM Project-Ready to Use AdditiveManufacturing) and University of Sheffield(AMRC) in the field of AM in the UK withunique multidisciplinary experiments on theleading edge of advanced technologydevelopment. These collaborations helpedme to share my thoughts and gainknowledge on the latest advances inresearch and development in this area. I wasvery pleased with the guidance received andthe quality of my ‘PhD Thesis’ which Isubmitted to The University of Manchesterand has been downloaded more than 600times within a year from all around theworld (the top 10 countries to download itinclude the USA, India, Germany, Japan,China, Iran, France, Vietnam, Belgium andSingapore). In addition, 7 journals andconference papers have been published out of this research on microstructure andmechanical properties of TiAl4V alloys using AM.

After completing my PhD in May 2012, Iobtained a position as Materials Lead at theAdditive Manufacturing Centre, GKNAerospace, Filton, UK in June 2012. Where Iam now attempting to industrialise theresearch topic that I worked on during myPhD, where Ti6Al4V parts are manufacturedthrough an additive manufacturing routefor real-time use in aerospace applications.This work is being carried out under anecoHVP project (ecologically High ValueParts) with a £10 million investment fromGKN and EADS (50-50 % collaboration)including £2 million from the BIS-UKGovernment. Since Additive manufacturingoffers complete design freedom andapproximately 30% overall weightreduction of existing parts. I am enjoyingbeing part of big ecoHVP team as MaterialsLead and, also since joining I have beeninvolved with 4 other projects as materialsadvisor and, currently working towards aproject leader/managerial position in nearfuture at GKN Aerospace, UK for materialsrelated projects. I am also representing GKN Aerospace as a part of the ASTM F42Committee working on establishing,reviewing and approving the new standardsfor additive manufacturing.

I would certainly recommend any industrialresearchers or Materials Science andEngineering students to pursue high end research on advanced characterizationand manufacturing technologies at The University of Manchester.

Dr. Alphons AnandarajANTONYSAMYmaterials Lead at gKn Aerospace Filton, uK

After completing my PhD, my scientificcareer began when I obtained a position asassistant professor at the Silesian Universityof Technology in Gliwice, Poland in 2005. I was involved in a project focused on aninvestigation of the relationship betweenstructure and thermal crystallizationprocesses of amorphous soft magnetic Fe-based alloys as well as their magneticfeatures and corrosion behavior.

I first joined the School of Materials at TheUniversity of Manchester in 2008 as a MarieCurie Fellow (IEF for Career Development,FP7). During my time at Manchester I was a frequent user of the Van de Graaffaccelerator at the Université Pierre et MarieCurie in Paris, where I used a wide range ofIon Beam Analytical techniques to study themechanism of anodizing. Thanks to theproject I got an opportunity to performunique multidisciplinary experiments at theedge of electrochemistry and nuclear physics.

After finishing my Marie Curie fellowship in2010 I was privileged to join the EPSRCLATEST2 Programme Grant and continuedmy scientific adventure within a vibrantenvironment created by the LATEST2 Team.Thanks to the project’s research plan andavailability of a variety of equipment Igained invaluable hands-on experience inconducting experiments in electrochemistryand materials/surface science. Thanks to thegreat knowledge of my supervisors and veryhelpful colleagues within the LATEST2 team,I have gained not only hands-on experiencebut also new, and more importantly,transferable skills. I feel fortunate to take

these important lessons with me. Thiscombined experience gave me a veryimportant confidence for moving to CulhamCentre for Fusion Energy (CCFE) and beingsuccessful as an independent scientist in ademanding environment.

The Culham Centre for Fusion Energy(CCFE) hosts the world's largest magneticfusion experiment JET (Joint EuropeanTorus), on behalf of its European partners.The JET facilities are operated for scientistsfrom around Europe, co-ordinated by theEFDA-JET Close Support Unit (under theEuropean Fusion Development Agreement).I work in the R&D Experimental Departmentand my work includes responsibility for awide range of surface analysis techniquesapplied to materials extracted from JETtokamak, development of links with UK and overseas Universities to encourageparticipation in exploitation of JET data and also assistance in operation of some ofJET diagnostic during plasma campaigns.

Dr Aleksandra Baron-WiechećPhysicist in culham centre for Fusion Energy (uKAEA), uK

I joined TWI in 2011 and currently work inCambridge as the Section Manager ofStainless Steel and Non-Ferrous AlloysSection, Materials Group.

My position requires me to lead a widerange of projects, from rapid turn-roundfailure investigations to long-term R&Dprogrammes for individual companies,consortia of companies and Governmentalprogrammes in oil and gas, powergeneration, heavy engineering andtransport sectors. I am also involved withconsultancy work, including failure analysisand managing and conducting single andjoint industrial and research projects withmain areas of focus related to materialsassessment/selection, microstructureproperty relationships, welding metallurgy(similar and dissimilar joints) and fabricationcracking, combined with expertise in serviceperformance and failure including corrosion,creep, fracture and resistance toenvironmentally assisted cracking of metallicmaterials with particular interest inimproving materials qualification and designof duplex stainless steels, titanium,aluminium and nickel alloys.

Before joining TWI, I studied and worked atThe Materials Science Centre, The Universityof Manchester more than 7 years. Aftercompleting my MSc in 2005, I pursued a

PhD in Mechanical Metallurgy of LightAlloys with the thesis title of ‘FundamentalSuperplasticity of Aluminium Alloys’. Duringthe course of my PhD, I challenged widelyheld views on superplasticity, namely grainboundary sliding and slip, and quantitativelydemonstrated that superplasticity isprimarily a result of diffusion creep. Afterfinishing my PhD I stayed on as a ResearchAssociate with my main areas of focusrelating to advance metal forming of a wide range of ferrous and non-ferrous alloy sheets.

Throughout these years, the EPSRC fundedLight Alloys Towards EnvironmentallySustainable Transport (LATEST) ProgrammeGrants, 1st and 2nd Generation, providedme with financial support and also gave methe opportunity to work with a number ofknowledgeable academics based at theSchool of Materials and collaborate with anumber of prominent industrial partners.The experience has indeed had a significantand positive effect on my personaldevelopment and has helped me develop a successful career.

Dr. Kasra SotoudehBEng. mSc, Phd, cSci mImmmSection managerStainless Steel and non-FerrousAlloys Sectionmaterials groupTwI Ltd. cambridge

After completing my Dr.-Ing. in OvGUniversität Magdeburg, Germany andpostdoctoral research tenure in University ofOxford. In 2008 I joined the School ofMaterials, The University of Manchester, asa Research Associate. I have been workingon hexagonal metals with a specialemphasis on light metals (titanium andmagnesium) in close association with theLATEST2 investigators, Dr. João Quinta daFonseca and Professor Michael Preuss. Oneof the main aspects of my research hasbeen characterizing and modeling theheterogeneous nature of hexagonal metaldeformation and investigating its effects onmaterials performance. The encouragingsupport of Joao and Michael, and thevibrant research environment in the

LATEST2/School of Materials offered me the motivation to become an expert inhexagonal metals (titanium, magnesiumand zirconium), texture evolution,thermomechanical processing, phasetransformations and in a wide range of thestate-of-the-art analytical tools, such asEBSD, image correlation, in-situ neutron andX-ray synchrotron diffraction and crystalplasticity finite element modeling.Furthermore, this also provided me with anopportunity to work on Nuclear Materials(zirconium), with other research groups(Professor Phil Withers), Universities(Sheffield and Birmingham) and Industries(Rolls-Royce plc, Serco and Timet UK).

Dr. Leo Prakash D.GSenior Lecturer materials research center, School of Engineering, university of Swansea, uK

Having completed my Masters degree inBiomedical Materials Science at TheUniversity of Manchester, I spent three yearsworking for BAE SYSTEMS developing andassessing Radar Absorbing Materials usingvarious Composite and Elastomericmaterials. I rejoined the School of Materialsin 2009 to study for a PhD in MetallicMaterials as part of the Light Alloys TowardsEnvironmentally Sustainable Transport(LATEST2) Research Programme of work,funded by EPSRC.

Within the LATEST2 framework I was ableto work with knowledgeable supervisors,researchers, students and technicians withinthe university, and collaborated with manypeople from other organisations, such asCranfield University and the Beijing Instituteof Aeronautical Materials. I was fortunate tohave the opportunity to present my work atconferences in the UK and the USA which,coupled with the diverse backgrounds ofmy LATEST2 peers, has enabled me to buildan international network of fellowmetallurgists. The facilities available to meduring my PhD allowed me to conduct indepth research into Solid State joining ofaluminium to magnesium, the issues facingjoining these two materials, and findingpotential solutions. I enjoyed working on aproject that had genuine focus on both theadvancement of scientific knowledge andits application to a real world issue;successful joining of aluminium tomagnesium could result in a significantreduction in automotive emissions.Ultrasonic welding, friction stir welding,scanning electron microscopy, x-raydiffraction and electron backscatterdiffraction were amongst the techniques Iused, and there were many other advancedfacilities available as well. To date, the

research I conducted within my PhD hasdirectly resulted in three published academicpapers, with a fourth having been accepted.

I currently work for AMEC, Clean Energy –Europe in Warrington, a focused supplier of consultancy, engineering and projectmanagement services to its customers in theworld's oil and gas, mining, clean energy,environment and infrastructure markets. My role is as Task Manager for a largeproject researching the Effect of a Heat Fluxon the Corrosion of Zirconium in Nuclearreactors, and I also work as a StructuralIntegrity Consultant providing safety adviceto a naval plant. My PhD developed manyof the skills that are necessary in my currentjob: oral and written communication skills,communicating technical content effectivelyand undertaking independent research areall essential, as are some of the technicalskills I learnt during my studies, such as microscopy.

Dr Lexi Panteliconsultant in materials Science for clean Energy – EuropeAmec, uK

After completing my Bachelors degree inMetallurgical and Materials Engineering inObafemi Awolowo University, Nigeria, Icame to the U.K. to study for a Masters inMaterials for Industry in LoughboroughUniversity. By this stage, I had developed astrong interest in engineering materials andwanted to undertake a PhD at a worldrenowned institution.

I decided to come to The University ofManchester as it had a great reputationworldwide in the field and also beyond this,and on a personal note, I had a strong

recommendation from my mentor who hadstudied at The University of Manchester inthe 1970s in a similar field. On this basis, Iaccepted an offer to undertake a researchPhD on a project titled the “Metallurgicalperformance of hyper joints in composite tometal joining” which was sponsored byEPRSC LATEST2 Programme Grant andEADS Innovations Work, UK. I wasparticularly interested in the project becauseit offered me the unique experience ofdirect collaboration with industrial partnerslike EADs and TWI on a novel means ofcomposite to metal joining. The projectinvolved investigating the use of titaniumalloys for making hyper-joint features viadifferent manufacturing routes such asadditive layer manufacturing and arc-percussive welding. The project alsoinvolved conducting series of mechanicaltesting to ascertain the performance of suchhyper-joints features and modelling usingAbaqus FE to simulate experimentalobservations. I was able to achieve the aimsand objectives of the project in part due tothe wide range of research facilitiesprovided by the university and mostimportantly because of the technical adviceand assistance offered by both my academicand industrial supervisors.

I currently work with Rawwater EngineeringCompany Limited (RECL) as a Metallurgist.RECL is an oil industry flow-assurancecompany providing specialist testing andconsultancy in the fields of well technology,water management, materials science andimproved oil recovery. In my role as aMetallurgist for RECL, I am responsible forleading the materials section in alloydevelopment that is being considered formetal to metal sealing in oil wellabandonment process. In the short periodof time that I have being working for RECL,I have come to appreciate all the skills andknowledge I have gained during the courseof my PhD from materials testing,characterisation using the SEM and evenreviewing FEA models. Being in a smallteam, I have been given high levelresponsibilities including liaising withexternal product qualification agencies,decision making and project management.For this and many more, I am deeplygrateful to The University of Manchester,EPRSC LATEST2 Programme Grant for givingme the opportunity to undertake my PhDdegree successfully which has now givenme the right platform to begin my career inengineering and materials science at RECL.

Rotimi Joseph Olulekemetallurgist at rawwaterEngineering company Limited

While at The University of Manchester I studied for an MSc in AdvancedEngineering Materials which complimentedmy previous industrial experience andundergraduate Mechanical Engineeringdegree. After completing my MSc I wasoffered the opportunity to study for anEngD sponsored by Magnesium Elektronand contributing to the EPSRC LATEST2Research Programme at The University of Manchester.

This combination of industrial and academicworking environments made for a veryinteresting and rewarding research project.Working on the inspection of cast lightalloys I frequently used the facilities of theManchester X-ray Imaging Facility andelectron microscope suite. Combined withthe support of the academic staff andfellow students the research degree was apositive experience which has enabled meto secure employment in the UK.

Since leaving Manchester I worked as analloy development metallurgist for Oil andGas Well Abandonment applications. I wasable to undertake this role thanks to theskills I learnt both technical and professionalduring my studies. Indeed the reputation ofThe University of Manchester helped me tosecure my current position as a MaterialsEngineer for Amec Oil and Gas, UK. Since commencing this role I have beenresponsible for carrying out an audit on a forge in Italy and working as part of amulti-disciplined team on maintenanceprojects for North Sea production platforms. David Mackie

MSc BEng(Hons)materials EngineerAmec oil and gas, uK

After obtaining my PhD degree in CorrosionScience and Engineering from the Universityof Manchester in 2013, I remained within the institution to begin work as a Research Associate.

During my time at Manchester, I gainedskills and experience about surface analysis,surface engineering, corrosion evaluationand microstructure characterisation ofaluminium alloys. These have benefited mycareer development in industry specificallywith regards my current employer, InnovalTechnology Limited. Thanks to the LATEST2programme, I had opportunities tocollaborate with the world's leadingcompanies including Novelis, Sapa Groupand Constellium including research projectsabout aluminium alloys for automotive,aerospace and packaging applications. Byparticipating in the projects, I developed theskills to solve technical problems, developnew technologies and optimise processesfor aluminium industry.

In May 2015 I joined Innoval TechnologyLimited, a collaborator of the LATEST2programme, as Surface Scientist. InnovalTechnology Limited provides consultancyand technical support to investors,manufacturers and end-users of aluminium,and other metals, across a broad range ofindustry sectors including rolling, extrusion,forging and finishing throughout the world.The skills and experience obtained from theLATEST2 programme, has enabled me toestablish myself as a consultant to provideexpertise for various developments insurface engineered products and newproduction processes.

Dr. Junjie WangSurface ScientistInnoval Technology Limited, uK.

I joined the LATEST2 research programthrough the Advanced Metallic SystemsCentre for Doctoral Training aftercompleting my undergraduate studies inPhysics and Chemistry at Durham University.I wanted to do my PhD level studies in anapplied field with industrial relevance, whileretaining the freedom and independence to pursue my own research ideas andscientific interests.

During my PhD at Manchester University Ifound I had these freedoms together withaccess to state of the art equipment and theacademic support network needed to carryout outstanding research. My PhD, informing lightweight magnesium alloys, wassponsored by Magnesium Elektron, aleading magnesium producer. Thissponsorship helped to direct my researchtowards the practical challenges facing theindustrial use of magnesium, while the deepunderstanding of fundamental metallurgywithin the academic community atManchester encouraged a rigorous scientificapproach which I have found to be a strongasset in my present job.

I currently work for TWI, which is amaterials, joining and technologyorganisation, as a Project Leader in thestainless steels and non-ferrous alloyssection. I manage a wide range of projectsacross various materials and processes frombrazing lightweight aluminium alloys todissimilar joining of stainless steels andnickel alloys. Clients vary from individualindustrial members to internationalconsortia, such as the RecycAl Europeancollaborative project which I currentlymanage. Exposure to state of the artequipment and the encouragement andsupport to attend various internationalconferences have been critical in developingthe confidence, management andinterpersonal skills that I now take forgranted in my current role.

Dr. David GriffithsProject Leader Stainless Steels and non-Ferrous Alloys TwI Ltd, cambridge, uK.

I returned to the University of Manchester in2011 as a LATEST2 PhD Research Affiliatehaving completed my first degree in Physicsthere some years prior. My PhD thesisconcerned the quantitative characterizationand finite element modelling of 3D imagedatasets as applied to corrosion andprotection. My primary experimentaltechnique involved the sectioning of lightalloys and coatings in the chamber of anSEM to produce high resolution 3D images.I also supported a number of experimentalteams at I13 Imaging Beamline at DiamondLight Source, where multidisciplinaryresearchers use very special kinds of X-raysto do Computed Tomography. This kind ofimaging is a very powerful complimentarytechnique that is applicable to a range ofdisciplines which has allowed me tocollaborate extensively.

I thoroughly enjoyed being part of theLATEST2 research team who are highlyskilled and knowledgeable researchers thatare a pleasure to work with. I found a hugeamount of support from the university andLATEST2 in developing my career. Fromgetting involved in outreach activities tolearning new computer programminglanguages, there was always a way toprogress and gain experience. I now hold aPDRA position at the Manchester X-rayImaging Facility (MXIF) where I'm able tomaintain the collaborations I firstestablished during my time at LATEST2. I am currently using 3D imaging and in-situmicro-mechanical testing rigs to revealfailure mechanisms of materials such asthermal barrier coatings and other porousmaterials. My greatest achievement to dateis the publication of my paper “QuantitativeCharacterization of Porosity andDetermination of Elastic Modulus forSintered Micro-silver Joints” which is aculmination of a number techniques which Ideveloped during my PhD.

Dr. James Andrew CarrPost-doctoral research Associatemanchester x-ray Imaging Facility,School of materials, the university of manchester

I joined the School of Materials at TheUniversity of Manchester in 2009 as aResearch Associate focusing on dissimilarmaterials joining using novel solid statejoining techniques. From 2010 to 2015, Iwas privileged to join the EPSRC LATEST2project and continued my research in thefield of dissimilar materials joining forautomotive industry. Thanks to Prof. PhilPrangnell, Dr Joe Robson, Mr David Strongand their excellent team for supporting mein that period at Manchester. With theirsupport, I’ve gained enormous knowledgein the field of material joining and materialcharacterization and obtained manychances to present our research work to theworld in very important internationalconferences like THERMEC, TMS, FSWsymposium, ICAA etc. All those experiencesare invaluable to me and helped mesuccessfully move on to work in industry in 2015.

In February of 2015, I landed a job at TheManufacturing Technology Centre (MTC) asa senior research engineer and continuedmy research in the field of solid statejoining. The MTC was established in 2010with the objective of bridging the gapbetween academia and industry. The MTChas a world leading friction weldingcapability. Extensive investment has beenmade in two tri-mode rotary friction welders(125T and 300T) with inertia, direct driveand hybrid capability. These machines haveadvanced controls, including precision upsetand final length control and orientationcontrol. The MTC also has the world’slargest linear friction welding machine, with the benefits of fast cycle times anddissimilar materials joining capability for arange of larger scale cross-sections. I’mcurrently the technical lead in the field ofrotary welding and the project manager of the core research project.

Dr. Yingchun ChenSenior research Engineer The manufacturing Technologycentre (mTc), coventry, uK

After completing my PhD in LoughboroughUniversity, I was delighted to join theLATEST2 research group as a ResearchAssociate working with Dr Joe Robson for 2years. My work concerned optimisingjoining performance between Al alloys andother metals e.g. steels, Mg alloys, and Tialloys, and developing materials modellingto understand and simulate microstructureevolution. I have to say, this 2-yearexperience very enjoyable and helpful.LATEST2 is a large, friendly research group,and I have made many friends here,including some for life. LATEST2 is one ofthe best research groups in the University ofManchester, perhaps the UK! Here we haveadvanced equipment, powerful software,and a great deal of expert knowledge withcontinually emerging ideas. An easy way toimprove is working with excellent peopleand advanced facilities, and LATEST2provides a platform with both.

With the abilities and experience I gainedfrom LATEST2, I was recruited by JaguarLand Rover as an Engineer within thejoining technologies group. My current jobfocuses on joining technologies betweenmetals (e.g. Al-Al, or Al-Steel) in theautomotive industry, which is similar to theprojects I studied within LATEST2. Thanks tothe knowledge and experience which Igained from Dr. Joe Robson, Prof. PhilPrangnell, and Dr. Ying-Chun Chen fromLATEST2 group, I can successfully resolveproblems during the advancedmanufacturing stages, and utilise myknowledge of modelling welding processesand Friction Stir Welding and UltrasonicWelding in my current role within JaguarLand Rover.

Dr. Li WangEngineerJaguar Land rover, uK

I joined the LATEST2 research group fromwithin The University of Manchester, havinggained my first degree in aerospaceengineering from The School of Mechanical,Aerospace and Civil Engineering. Prior tostarting my PhD, I completed a master’slevel taught course in all aspects ofmetallurgy as part of the advanced metallicsystem centre for doctoral training. I chooseto do a PhD in the LATEST2 programmebecause it combined strong contacts toindustry with access to high qualitylaboratory equipment and support staff.

I will shortly submit my PhD thesis on thequantification of defects, and their effect onmechanical properties, in titaniumcomponents manufactured by selectiveelectron beam melting. My academicsupervisor provided me with excellentsupport throughout my project,encouraging me to challenge myself and in the process develop my skills as aresearcher. As a result I have had theopportunity to present at severalinternational conferences and industrialmeetings with GKN, Rolls-Royce, andAirbus. Internal seminars prior to this withinthe LATEST2 group provided me with theconfidence to present my work to industrialand scientific leaders in the field.

I have recently started work as a Post-Doctoral Research Associate at theUniversity of Sheffield on an EPSRC fundedprogram grant, DARE, ‘Designing Alloys forResource Efficiency’. In addition to thetechnical abilities I gained during my PhD,the project planning and management skillshave proved invaluable in adaptingeffectively to this new role. I am now co-supervising a group of new PhD andmaster’s students in their research, whichhas been made easier by the excellentexamples I was set in the LATEST2 program.

Mr Sam Tammas-WilliamsPost-doctoral research Associatedesigning Alloys for resourceEfficiency (dArE)The university of Sheffield

After obtaining a BSc and a MSc inMaterials Science and Engineering fromPolitecnico di Milano (Italy), I wanted toexperience doing research in a world-leading university and I decided to apply fora PhD at the University of Manchester,where I started in 2006. During my PhD Iworked within the LATEST portfolio grant,focussing on the development of new,chromate-free, anodizing treatment for thecorrosion protection of aerospace alloys.After completing my PhD, I remained at theUniversity of Manchester initially as a

Research Associate and widened myresearch interests to a variety of issuesrelated to the corrosion protection of LightAlloys. In 2011, with the beginning of theLATEST2, I was awarded a ResearchFellowship and in 2014 I was appointedLecturer in Corrosion and Protection at The University of Manchester.

My Current work focuses on protectivesurface treatments for light alloys withparticular attention to anodic oxidation anduse of environmentally friendly inhibitors toprovide long-term active protection. Thisapproach involves the investigation offundamental and applied aspects of theanodic oxidation such as the effects of theelectrical parameters and electrolytecomposition on the long term protectivebehaviour. Understanding the interactionsbetween the microstructural featurespresent on practical alloys and the corrosionenvironment, in the presence or absence ofprotective treatments and corrosioninhibitors, is also a key aspect of myresearch activity.

I also work on the development ofadvanced electrochemical methods for theassessment and prediction of the corrosion

behaviour. In particular, I developelectrochemical techniques that enable toobtain corrosion-related information byapplying minimal or no electricalperturbation to the corroding surface andare therefore intrinsically representative ofthe real-life behaviour. This involves thedevelopment of software and hardware formeasurement and analysis ofelectrochemical noise generated duringcorrosion and real-time imaging ofcorroding surfaces.

The LATEST2 programme grant wasparticularly beneficial to my scientific careerthanks to the exciting and challengingobjectives that the team has developedduring the years. This combined with thecritical mass of researchers and expertise,and the strong interactions with industry ina wide range of sectors, gave me theopportunity to focus on the fundamentalscience required to solve the newtechnological challenges appearing in the future but also on increasing thetechnology readiness level of conceptsdeveloped during the early stages of myscientific career.

Dr. Michele Curioni Lecturer in corrosion Protection, The university of manchester

I became interested in materials sciencewhile working as a trainee in a moderncermet factory of the Guehring group in myhometown Berlin, Germany. Experiences inthe sinter plant, the quality managementand the R&D department of G-ELIT inBerlin-Wittenau, informed my mastersstudies in material science at the Technical

Institute of Berlin in 2010. The studiesinstilled an in-depth knowledge of materialscience, including ceramics polymers andglasses. The focus of my final project waslight metals, specifically mechanicalanisotropy of extruded and rolled AZ31,accomplished in the Extrusion Research andDevelopment Centre Berlin.

The School of Materials at the University ofManchester offered me the chance tocontinue my research on deformation oflight metals during a PhD project. Thewelcoming LATEST2-team offered a lot offreedom to complete my project, “TheEffect of alloying elements on deformationand ductility in Titanium”. Free access tothe vast range of characterisationtechniques, from classical metallographyand XRD over diverse mechanical testers toelectron microscopy, allowed understandinghow alloying effects the material propertiesand deformation mechanisms. Tenundergraduate projects under mysupervision enhanced my four-year PhD notonly scientifically but also personally. The

LATEST2 team encouraged me tocommunicate material science in general tothe public and my project in particular tothe scientific as well as industrial community.

Most importantly for my career, wereconferences I was able to attend, whichbrought me into contact with industry,including Constellium and BCAST (BrunelCentre for Advanced SolidificationTechnology). Furthermore, Constelliumoffered an interesting and challenging jobas a research fellow with excellent futureperspectives. Together with ConstelliumsR&D team, at AMCC (Advanced MetalCasting Centre, Brunel University) wedevelop crash management systems fromcasting new alloy compositions over specificthermo-mechanical treatments in lab scale,to improving designs of the final product. Iam looking forward to a good start at theAMCC, and working as the first part of the metal research park in Brunel, which will upscale the laboratory breakthroughs of BCAST.

Dr. Arnas Fitzner material Scientist in the Amcc,Advanced metal casting centre,Brunel university, uK

I joined the EPSRC LATEST2 ProgrammeGrant during my PhD within the AdvancedMetallic Systems Centre for DoctoralTraining (CDT). Upon completion of my PhDI continued work within LATEST2, as a Post-Doctoral Research Associate. The AdvancedMetallic Systems CDT provided me with thetools I needed to further my career as anexperienced mechanical engineer, andmaterials science in advanced light alloyswas the ideal stepping stone into scientificresearch at a world-leading university.

My PhD project with the LATEST 2 team, at The University of Manchester, wasenhanced by a broad academic supportnetwork and the right tools needed to carryout outstanding research in the field of lightalloy research. My research was enabled byfree access to a vast range of characterisationtechniques at the fore-front of materialsresearch including classical metallography,3D X-ray tomography and advancedelectron microscopy techniques.

My PhD project was sponsored byConstellium, who provided developmentmaterial for a novel application. My researchwas based around the investigation of thecorrosion behaviour of development

aluminium alloys for the transport industry. I gained skill sets at the forefront ofaluminium surface science, corrosionscience and aluminium alloy processing,including the ability to solve complicatedtechnical issues encountered in sheetaluminium production. Equally importantfor my research was the opportunity toattend monthly seminars, group meetingsand conferences to showcase studentcontributions. The EPSRC LATEST2Programme Grant enabled and encouragedthe sharing of information and scientificcommunication with other research groupsand industry. In addition, outreachprogrammes organised by the LATEST2team were particularly interesting forstudents and researchers alike, enablingpractical demonstrations of materialsscience to the community.

In August 2015 I began as a Post-DoctoralResearch Associate for LATEST 2 as part of a joint venture between Otto-Fuchs and Airbus. The many skills gained from my experiences with LATEST 2 have helped me to interact with industry as ametallurgist, and an environmentaldegradation and surface Scientist.

Dr. Alex CassellPost-doctoral research AssociateEnvironmentally Assisted degradation,School of materials,The university of manchester

I joined the EPSRC LATEST2 ProgrammeGrant at The University of Manchester aspart of an Erasmus programme “StudentMobility for Training”, during my PhD in2012. My research centred on developingplasma electrolytic oxidation coatings onmagnesium alloys and studying theirmicrostructure, corrosion behaviour andfatigue performance. The opportunity touse a wide range of modern experimentalfacilities in cooperation with highlyexperienced researchers helped me toobtain valuable results for my PhD thesisand successfully complete my doctoratedegree at Brno University of Technology inthe Czech Republic. It also helped informmy decision to continue working in anacademic environment.

After completing my PhD in 2013, I wasappointed as a Post-Doctoral ResearchAssociate within LATEST2, where I furtheredmy knowledge of surface engineering.Collaboration with international partnersgave me, amongst other things, anopportunity to regularly use the Van deGraaff accelerator at the University ofNamur in Belgium. I used a range of ionbeam analytical techniques to study themechanism of anodizing of light alloys. The opportunity to discuss results at regular meetings also helped to develop my presentation and communication skillsin the English language.

Being part of the EPSRC LATEST2Programme Grant, with close cooperationand supervision by experts in the field, hashad a strong positive effect on my personaldevelopment. I believe that gainingtransferable multidisciplinary skills inmaterial science, electrochemistry andnuclear physics will help me successfullyprogress in my scientific career.

Dr Aneta NěmcováPost-doctoral research Associatecorrosion and Protection centre School of materialsThe university of manchester

After completing my PhD at Delft Universityin the Netherlands, I sought to further myexpertise in physical metallurgy and have agreater understanding of the mechanicalbehaviour of materials. Hence, I joined the EPSRC LATEST2 Programme Grant as aPost-Doctoral Research Associate at the

University of Manchester. Here, my workfocused on devising novel in-situcharacterization techniques (using bothElectron Backscattered diffraction anddigital image correlation) to understand thelinks between microstructure and itsdevelopment during deformation and theformability of Mg alloys. Thanks to theavailability of a range of equipment, Igained invaluable hands on experience in electron microscopy, digital imagecorrelation and sheet metal testing. Thanks to the expertise of my supervisor Dr. Joao Quinta da Fonseca and very helpfulcolleagues within the LATEST2 team, Igained not only hands on experience butalso attained important transferable skills.My supervisor’s additional freedom inpermitting me to publish my PhD workresulted in me publishing an article in ActaMaterialia. This combined experience gaveconfidence to my career as a successfulmaterials scientist, and as such helped mesecure a position within Tata Steel Researchand Development.

The Tata Steel Group is among the top-tenglobal steel companies with an annualcrude steel capacity of nearly 30 milliontonnes per annum. It is the world's second-most geographically-diversified steelmanufacturer and second largest steelproducer in Europe. I work in the MaterialsDesign department where I manage severalprojects involving new product developmentof steels for automobile, oil and gas,construction applications and high strengthsteels for heavy transportation and liftingequipment. My job responsibilities includedesigning and developing novel steel alloys,steel composites and perform experimentswith various microscopy and analyticaltechniques. In addition, I collaborate withUniversities in the UK and overseas byworking as an interface between scientificand industrial research.

Dr Ganesh Kumar Tirumalasettymaterial ScientistTata Steel Europe, rotherham, uK

I arrived at the University of Manchester in2012 having finished my PhD in physics atthe University of Debrecen, Hungary. Ijoined the EPSRC LATEST2 ProgrammeGrant as a Research Associate focusing onthe plastic deformation of hexagonal metalalloys. My primary aim was to understandthe limits of formability of industrial alloysby means of crystal plasticity finite elementmodels, building on my experience instatistical mechanics. I was aided in mywork by constant discussions with well-established researchers within the LATEST2group and also international collaborations.I had at my disposal a wide range of state-of-the-art experimental characterisationtechniques. I had the chance to co-superviseMSc and PhD students and benefitedgreatly from working in a diverse multi-disciplinary group. I found LATEST2 and theUniversity of Manchester as a whole, to bea very supportive, straight-forward andfriendly environment that has helped megain valuable professional experience andhas made my time there most enjoyableand memorable.

In October 2015, I took a position asresearch associate at the University ofAveiro, Portugal, in one of the leadingresearch groups in the statistical physics of complex networks. I am studying thestructure and evolution of multiplexnetworks as part of the project MULTIPLEXfinanced by the European Commission.Although my research interests havechanged, I gained a lot of experience inacademic research in general during mytime at LATEST2. The three years I spent atthe University of Manchester has beeninvaluable in helping me form my decisionto pursue an academic career.

Dr Gabor TimarPost-doctoral research AssociategnET – complex networksdepartment of Physicsuniversity of AveiroPortugal

I joined the EPSRC LATEST2 ProgrammeGrant at the University of Manchester in2011 as a PhD student supervised byProfessor George Thompson, ProfessorPeter Skeldon and Dr. Michele Curioni. Theaim of my project was to enhance thecorrosion resistance of aluminium alloys foraerospace industry using rare earth metals.While working within LATEST2 I became aspecialist in materials science andelectrochemistry, with particular emphasison corrosion protection and analysis ofmaterials. I gained substantial skills insurface analysis and characterization ofmaterials using electron microscopy, XPS,XRD and other methods. The LATEST2programme provided a stimulating andfriendly environment to work within.Furthermore, The University of Manchesterand the School of Materials were extremelyfamily friendly, providing help and advicebefore and during my maternity leave andsupporting me when I returned to continuemy project. At the moment I am writing up my thesis and will submit in the coming months.

Upon finishing my research project at theUniversity of Manchester, I have beenemployed by the Pilkington Technical, whichis a part of the international NSG Groupand one of the world’s leading specialistglass manufacturers. My role is AdvancedTechnologist within the Research andDevelopment group. I provide technicalsupport to manufacturing lines and developnew products, improving properties ofautomotive, architectural and technicalglass. The knowledge and experience Iobtained while working within LATEST2 isinvaluable. Many, if not most, of themethods and instruments I use for mycurrent work I learned during my PhDproject. Even more important are theproblem-solving and analytical skills which I also gained, as these have provided mewith a sound basis for my future career.

Irina GordovskayaAdvanced technologistnSg groupPilkington Technical centreLathom, uK

The LATEST2 team have successfullydeveloped and executed an effectivescience communication programme toengage with a wide range of targetaudiences. The key goals were to raiseawareness of the research being undertakenand its value, to develop collaborations bothacademic and industrial, to facilitateeffective knowledge transfer and helpaddress the skills gap by attracting highquality students and researchers into theengineering and physical sciences.

The outreach activities were coordinated bya dedicated Science Communication Officer,supported by the LATEST2 academicchampion, academic staff, students andexternal industrial collaborators. Theactivities were specifically developed to effectively reach a wide range of target audiences.

ImPAcT - ScIEncE communIcATIon

LATEST2 ScIEncE communIcATIon ProgrAmmE

OuR "IMPACT" STRATEGy SuCCESSFuLLy REAChED ThE FOLLOWING AuDIENCES:

InduSTry

MATErIAL ScIEnTISTS

PuPILS

AcAdEmIA

CommunITy

TEAchErS And cArEEr AdVISorS

Events for Schools and CollegesDuring the lifetime of the award LATEST2ran a wide variety of events aimed at schooland college students and their teachers. Thekey aims of the activities were to engagestudents with Materials Science and raiseawareness of the subject, the EPSRC, and to introduce them to some of the researchtaking place in this area, as well as highlightthe range of careers and courses available.We engaged with students in a lot ofdifferent ways; our researchers visitedschools to deliver lectures and workshops,we hosted work experience students andwe also ran practical activities at TheUniversity of Manchester for studentsincluding full Residential EngineeringSummer Schools and a regional “LATEST2Ultimate Car Challenge” competition.

The programme of activities for schools andcolleges went from strength to strengthduring the lifetime of the award, achievingyear on year growth. In year 1 the teamachieved 1500 contact points and thatfigure was more than doubled in the most recent period. Over the lifetime of the award we achieved over 12,500contact points with students from schoolsand colleges.

Activities have included participating inPhysics at Work Events, LATEST2 ResidentialEngineering Summer Schools, University of Manchester Science Spectacular Fairs, Headstart Summer Schools, DragonFly Days, IOM3 Open Days, DiscoverEngineering Days, Aim Higher SummerSchools, The Institution of Engineering and Technology Christmas Lectures andmore recently Manchester Teen Tech andthe LATEST2 Ultimate Car Challenge.

A couple of the key events held during the lifetime of the award arehighlighted here.

LATEST2 Engineering MaterialsResidential Summer SchoolsThe Residential Summer Schools haveproven to be a phenomenal success andhave been run every year since 2010. Atotal of 350 students aged 14 – 16 yearsold, from across the country attended the 5 Day Residential Summer Schools over thelifetime. It is also important to note thatwith the support of the Widening Participationteam we were able to offer a number ofbursary places to enable students from difficulteconomic backgrounds to attend.

The aims of the LATEST2 EngineeringResidential Summer Schools were for school students to:

• Engage with the University and help themfind out more about the exciting world ofmaterials science and potential universitystudy and careers,

• Learn about the EPSRC, the Engineeringand Physical Sciences in general and morespecifically the important research beingundertaken by the ESPRC LATEST2Programme Grant,

• Find out what life is like for a student at The University of Manchester,

• Take part in lectures, practical lab basedactivities and team challenges, and workwith current engineering students andworld-class scientists,

• Learn more about the fascinating field ofmaterials science, and see how we designmaterials for automotive and aerospace,

• Experience a site visit to a majormanufacturer in the automotive oraerospace sector; e.g. Airbus, JaguarLandRover.

The Engineering Residential Summer Schoolshave been such a great success that theywill continue to be run by The School of Materials.

LATEST2 ultimate Car ChallengeThe Ultimate Car Challenge was developedas a regional competition to enablesecondary school pupils from across GreaterManchester to compete in teams to try todesign and build the ultimate model scalextricslot car based on realistic design criteriaincluding, weight, cost, CO2 footprint, safetyand asthetics. Pupils were mentored bypostgraduate students from across theFaculty of Engineering and Physical Sciences.The aim of the competition was to give pupilsan insight into the world of engineering andthe careers and courses available, to engagethem with materials science and to providethe postgraduate students with experience of outreach activities.

Pupils were supplied with a wide range ofmaterials to choose from when building theircar including aluminium, steel and carbonfibre, and we encouraged students to thinkabout the advantages and disadvantages ofeach material. The pupils also had to take anumber of factors into account when designingtheir car including the cost and environmentalimpact of the materials used, make sure theirdesign was aerodynamic and think abouthow their car will survive a corrosion test!

Each Postgraduate student was paired with aschool, and they ran weekly workshops withthe students, supporting them to design andbuild their car. The competition culminated ina two-day finals event at the University ofManchester, where the winning team fromeach school came to compete, and their carswere put through various tests including adrag race, circuit time trials, and crash andcrush tests! The cars were judged by a panelof experts including representatives fromJaguar Land Rover, The LATEST2 advisorypanel and the School of Materials at The University of Manchester.

Students attending the EPSRC LATEST2 Engineering Residential Summer School 2014 LATEST2 Ultimate Car Challenge Winning Team

The Ultimate Car Challenge was developedand run for the first time in 2014, withfunding provided by the Royal Academy ofEngineering through their Ingenious PublicEngagement Grants Scheme and supportedby the EPSRC LATEST2 Programme Grant.Over the course of the project we workedwith 272 pupils aged 13 – 16 years old, andran 159 school or university basedworkshops. The challenge was a hugesuccess, and the positive impact of theproject was quantified via student surveys inwhich 71% answered ‘yes’ or maybe’ to thequestion – ‘Would you be interested instudying engineering?’ compared to 54% atthe start of the project.

Comments made by some of the pupilsinvolved in the project include; “I have learntthat there are many things engineers can doand that it is fun!” and “I have learnt howchallenging and exciting engineering canbe.” One of the elements most enjoyed bythe students was the practical experience ofgetting hands-on and actually building thecar. All of the postgraduate students involvedsaid that they would like to take part insimilar activities in the future, and felt thatthey were now either confident, or veryconfident, of carrying out public engagementactivities – showing the project haddeveloped their skills in this area.

Due to the enormous success of the LATEST2Ultimate Car Challenge, it ran again in 2015,this time fully funded by the EPSRC LATEST2Programme Grant.

More information about the Ultimate CarChallenge can be found at:www.ultimatecarchallenge.co.uk

Events for the CommunityLATEST2 was committed to delivering aprogramme of activities aimed at thecommunity, including for both family andadult audiences. Each year we wereinvolved in a variety of different events,including taking part in large sciencefestivals such as the Manchester Science Spectacular.

Our community events focused on runninghands-on activities aimed at raisingawareness of materials science and toshowcase some of the research taking placewithin the LATEST2 programme. Theseactivities were designed to be suitable for avariety of audiences, and encouragedpeople to engage with the science in a funand practical way. Our community eventshave been a huge success, and each yearwe looked to develop the programmefurther and reach new audiences.

During the lifetime of the award we havereached over 35,000 contact points withthe general community. Activities have

included participating in CheltenhamScience Festivals, Airbus Family Days, JodrellBank Summer Science Festivals , Big BangScience Spectaculars, Meet the ScientistDays at Manchester Museum of Science andTechnology and Low Carbon Vehicle CENEXEvents. A major event that we have beeninvolved with successfully since June 2013 is the Cheltenham Science Festival.

Cheltenham Science Festival Cheltenham is one of the largest sciencefestivals of its kind, and each year attractsscientists from across industry and academiawho come to share their latest researchwith the public through lectures andinteractive activities. In June 2013 we had a stand in the Discover Zone, runninghands-on materials science activities aimedat a family audience. The Discover Zone is ahugely popular part of the festival, and overthe course of the week is attended by over7,000 people.

Following the success of this, we took partin the Festival again in 2014, but on thisoccasion we asked to develop activities forthe adults-only zone. In 2015 we returnedto the Discover Zone, and were linked in tothe Back to the Future theme of the Festival.

We have a run a variety of hands-onactivities at the Festival, including usingchocolate to explore impact testing, by

LATEST2 Ultimate Car Challenge Track Test LATEST2 general outreach event for the community

LATEST2 Ultimate Car Challenge Crush Test School visit

investigating how tough different chocolatebars are using a model impact tester andcomparing their structure to engineeringmaterials; e.g. thinking about what an Aerobar can tell us about a metal foam! Otheractivities have included demonstrating theprinciple of electro-plating, a recyclingchallenge dance mat, getting people to tryto match every-day objects with imagestaken of them using electron microscopes!

The events were attended by members ofthe public, ranging from young children upto adults, and have been a great way toengage with a broad audience.

Events for Industry and AcademiaThe LATEST2 team have delivered acomprehensive programme of events forindustry and academia, in order to help toestablish and build long-term strategicpartnerships with leading industrial andother research institutions and, facilitatenetworking and knowledge transfer.

As well as organising one or two dayacademia-industry targeted workshops, theLATEST2 team have had a presence at anumber of trade and industry focused fairs.For example, LATEST2 has given invitedpresentations at the Advanced EngineeringConference held at the NEC Arena ,the UK’slargest free-to-attend engineeringconference programme, where the supplychain meet with visiting engineering andprocurement decision makers from OEMsand top tier organisations spanning:Aerospace; Automotive; Motorsport;Marine; Civil Engineering, and more.Attendance over the 2 days was 13,000delegates. The team also participated in theEPSRC Conference, Manufacturing theFuture. The programme of events for

Industry and Academia developed each year and one of the key events held ishighlighted below. The LATEST2 teamorganised and hosted the LATEST2 GuestSeminar Series featuring a wide range ofguest speakers from both Academia andIndustry. The team have also helpedorganise a number of major conferencesincluding; the Aluminium Surface Scienceand Technology 2012 and 2015; the LightMetals Symposium at EUROMAT 2015 aswell as hosting a number of workshops forexample; Challenges for Joining LightWeight Dissimilar Materials for AutomotiveApplications; Advanced Tools forCharacterisation; and a TitaniumInformation Group Meeting. The teamhosted a key road mapping event held in2014 in collaboration with the Institute ofMaterials Mining and Minerals (IOM3) light metals Board as highlighted below.

Light Alloys Road MappingWorkshop Fundamental challenges in light alloys researchsupporting innovation inadvanced manufacturing for environmentally sustainable transportThe road mapping workshop was held tofocus the future direction of UK light alloyresearch. The aim of the meeting was toidentify the research challenges that willneed to be addressed, to support futureindustrial innovation in advancedmanufacturing with light alloys in thetransport sector. The workshop was byinvitation only. Forty-two technical expertsparticipated in the event, including technical

experts from the aerospace and automotiveindustries and across the materials supplychain in titanium, magnesium andaluminium.

The aim of the meeting was to help todefine future research challenges,addressing questions such as:

• What developments are needed to help facilitate and support innovativemanufacturing in lightweight metallic materials?

• What fundamental enabling research is critical to deliver the light alloytechnologies required by the transport sector?

• What are the key technology areas andresearch challenges for maximum impact?

• What fundamental research synergiesexist between different sectors?

The outcomes of the road mappingworkshop were widely circulated toacademia and industry.

LATEST2 dissemination activities have been further supported by the website,newsletters and published reports. Inaddition the LATEST2 team haveencouraged visits to and from industry andto and from other academic institutions.

LATEST2 Light Alloys Road Mapping WorkshopLATEST2 Conference

Academic CollaboratorsAdvanced Metallic Systems Centre for DoctoralTraining (CDT), UK Brno University of Technology, Czech RepublicBrunel Centre for Advance SolidificationTechnology (BCAST), UKBrunel University London, UKCranfield University, UKDeakin University, Australia Diamond Light Source, UK Engineering and Physical Science ResearchCouncil (EPSRC), UK EPSRC Centre for Innovative Manufacturing inLiquid Metal Engineering (LiME), UKHokkaido University, Japan Imperial College London, UK

Institut Laue-Langevin (ILL), FranceIowa State University, USAISIS, UKMaterials Performance Centre (MPC), UKMonash University, AustraliaThe National Center for Metallurgical Research(CENIM), SpainNational Centre of Scientific Research(DEMOKRITOS), GreeceOhio State University, USAPolitecnico di Milan, ItalyRWTH Aachen University, Germany Universidad Complutense de Madrid, SpainUniversidad de Santiago de Chile (USACH), Chile Universitié Pierre et Marie Curie, FranceUniversity of Antioquia, Colombia

University of Birmingham, UK

University of Cambridge, UK

University of Kaiserslautern, Germany

The University of Manchester Aerospace ResearchInstitute (UMARI), UK

The University of Manchester, Manchester X-RayImaging Facility, UK

University of Milan, Italy

University of Naples Federico II, Italy

University of Nottingham, UK

University of Sheffield, UK

University of Strathclyde, UK

Warwick Manufacturing Group (WMG), UK

Xi’an Technology University, China

coLLABorATorS

Industrial and RO CollaboratorsAirbus, an EADS Company, UKAkzo Nobel N. V., the NetherlandsAlcoa Inc., UKAston Martin Lagonda Ltd, UKAustralian Government Department of Defence,AustraliaBAE Systems plc, UKBeijing Aeronautical Manufacturing TechnologyResearch Institute (BAMTRI), China Baosteel Group, ChinaBeijing Institute of Aeronautical Materials (AVIC),ChinaBMW, UKBP, UKBridgnorth Aluminium Limited, UKConstellium, FranceCommonwealth Scientific and Industrial ResearchOrganisation (CSIRO), Australia EADS Innovation Works, UKEuropean Synchrotron Radiation Facility (ESRF),France

Engineered Capabilities Ltd, UKFEI Company, UKFord, USA Goodrich, UKHeat Trace Ltd, UK Helmholtz-Zentrum Geesthacht Centre forMaterials and Coastal Research, Germany Innoval Technology Ltd, UK Institute of Materials, Minerals and Mining(IOM3), UKJaguar Land Rover (JLR), UK Magnesium Elektron, UKMichell Instruments, UKNovelis Inc., USANorthwest Aerospace Alliance (NWAA), UK Northwest Automotive Alliance (NAA), UKOtto Fuchs KG, GermanyPoeton Industries Ltd, UKPOSCO Engineering & Construction Ltd, South KoreaRio Tinto Group, UKRolls-Royce plc, UK

Sapa AS Group, Sweden Siemens VAI – Metals Technologies Ltd, UKTata Steel Europe Limited, UKTechnology Strategy Board (TSB), UKThe Welding Institute (TWI), UK Titanium Metals Corporation (Timet), UK

Outreach CollaboratorsEngineering Development Trust (Headstart), UKInstitute of Materials, Minerals and Mining(IOM3), UKJodrell Bank Centre for Astrophysics, UKMuseum of Science and Industry (MOSI), UKNuffield Foundation, UKRoyal Academy of Engineering, UKScience, Technology, Engineering and MathematicsNetwork (STEMNET), UKSmallpeice Trust, UKThe University of Manchester Widening Participation, UKWomen’s Engineering Society (Dragonfly), UK

Philip Prangnell joined the Manchester Materials Science Centre in 1992 after completing his PhD in Metal Matrix Composites atCambridge University. He was promoted to Chair in Materials Engineering in 2005 and is Co-director of the Metallic Systems Centreof Doctoral Training Centre in Metallurgy with Sheffield University. He officially took over the Directorship of the LATEST2 in June2015 after a lengthy period as acting Programme Director. His research activities are largely focused on studying material interactionsin advanced thermomechanical processing and joining techniques for light alloys (mainly aluminium and titanium). This work hasrecently expanded to include the metallurgical optimisation of additive manufacturing. He has on going collaborations with majoraerospace companies, including EADS, Airbus, and Rolls-Royce, as well as companies within the supply chain (e.g. Constellium,Siemens, GKN). He is also working with DSTL and BAE Land systems on aluminium intensive fighting vehicles.

mAnAgEmEnT TEAmProfessor Philip B. Prangnell LATEST2 Programme director, Theme Leader and Principal Investigator chair in materials Engineering,The university of manchester co-director of the metallic Systemsdoctoral Training centre of metallurgy

Joe Robson graduated in Natural Sciences from the University of Cambridge in 1993, and obtained his PhD from the sameinstitution in 1996. Since then he has worked at Cambridge, Swansea, and Manchester universities, and in 2003 was appointedto a Lectureship, becoming a Reader in 2012 and obtaining a personal chair in 2015. In June 2015, Joe took up the position ofDeputy Programme Director and remains a Co-investigator on the EPSRC LATEST2 Programme Grant and a member of the LightAlloy Processing group with research interests that are focussed on microstructural evolution and control in industrial alloys, withan emphasis on modelling. Joe's work involves close collaboration with a range of industrial partners including MagnesiumElektron, Novelis, Constellium, Alcoa, and BP plus international research centres including Helmholtz Zentrum Geesthacht andDeakin University, Australia.

Professor Joseph D. Robson LATEST2 deputy Programme director and co-InvestigatorProfessor of metallurgy

Michael Preuss is Deputy Director of the Materials Performance Centre and the Nuclear Rolls-Royce University Technology Centrein Manchester. He is a Co-investigator on the EPSRC LATEST2 Programme Grant and the Heterogeneous Mechanics in HexagonalAlloys across length and time scale (HEXMAT) Programme Grant and recently became Director and Lead PI on the New NuclearManufacturing (NNUMAN) Programme Grant. In 2010, Michael was awarded an EPSRC Leadership Fellowship, which hecommenced in April 2011. Michael's research focuses on microstructure, mechanical properties and residual stresses in hightemperature materials for the aeroengine and nuclear applications.

Professor Michael Preuss LATEST2 co-Investigator Professor of metallurgy, deputy director of the materials Performance centre and nuclear rolls-royce university Technology centre

Peter Skeldon graduated in Physics from the University of Manchester in 1974, and obtained a PhD from the same institution in1977. He subsequently worked in industry in the area of electronic and composite materials, before joining the United KingdomAtomic Energy Authority, where he was employed for ten years researching corrosion of reactor materials in high-temperaturewater and sodium environments. He was appointed to a Lectureship at The University Of Manchester Institute of Science Technology in 1992, progressing to Professor in Corrosion Science and Engineering in 2005. Peter is a Co-investigatoron the EPSRC LATEST2 Programme Grant, with research interests that are focused on surface treatments of light alloys.

Professor Peter Skeldon LATEST2 co-Investigatorchair in materials Engineering

Xiaorong Zhou graduated from the Department of Chemistry and Chemical Engineering of Hunan University, China in 1983. Heobtained an MSc in materials science and engineering at Beijing University of Aeronautics and Astronautics, China in 1986. Hewas then appointed research engineer in Beijing Institute of Aeronautical Materials. Xiaorong received his PhD in corrosionscience and engineering from UMIST in 1994. Subsequently, he joined the Corrosion and Protection Centre of The University of Manchester (then UMIST) in 1994 initially as Research Fellow, then Lecturer, then was promoted to a chair in 2015. Xiaorongis a Co-investigator on the EPSRC LATEST2 Programme Grant and recently took over as Theme leader on advanced surfaceengineering and a member of the Corrosion and Protection group. Xiaorong is a visiting professor to University of Santiago of Chile, Chile and Beijing Aeronautical Manufacturing Technology Research Institute, China. Xiaorong’s research interests lie in corrosion control of light alloys and developing novel surface engineering approaches.

Professor Xiaorong Zhou LATEST2 Theme Leader and co-Investigator Professor of corrosion Science and Engineering

João Fonseca completed his PhD on the mechanical behaviour of high volume fraction MMCs at the University of Leeds in 2001.He then moved to the School of Materials at the University of Manchester, where he became a lecturer in 2005 and a seniorlecturer in 2011. He is currently active in a number of different research groups, including the Engineering and ProcessMetallurgy group and the Materials Performance Centre. He is a Co-investigator on the EPSRC LATEST2 Programme Grant,where he is leader of the formability theme. Current projects in LATEST2 aim to understand the limits of formability of highstrength aluminium alloys and hexagonal metals such as titanium and magnesium.

Dr João Fonseca LATEST2 Theme Leader and co-InvestigatorSenior Lecturer

Michele obtained a BSc and MSc in Materials Science and Engineering from Politecnico di Milano (Italy), thereafter embarking ona PhD at the University of Manchester, working within the LATEST Portfolio Partnership. Michele’s PhD focussed on thedevelopment of new, chromate-free, anodizing treatment for the corrosion protection of aerospace alloys. After completing hisPhD, Michele remained at the University of Manchester initially as a Research Associate, widening his research interests to avariety of issues related to the corrosion protection of Light Alloys. Then in 2011 he was awarded a Research Fellowship, and in2014 appointed Lecturer in Corrosion Protection. His current work focuses on protective surface treatments for light alloys withparticular attention to anodic oxidation and use of environmentally friendly inhibitors to provide long-term active protection.

Dr Michele Curioni LATEST2 co-Investigator and acting Academic outreach championLecturer in corrosion Protection

George Thompson graduated in Metallurgy from the University of Nottingham in 1967 and was awarded his PhD from the sameinstitution in 1970 for studies on the precipitation in Al-Cu and Al-Li alloys. After postdoctoral studies at Nottingham on theeffects of heat and mass transfer on the corrosion behaviour of selected metals, he joined Howson Algraphy Ltd (now Agfa UK),lithograhic plate manufacturer, in Leeds in 1973. During the period in industry, he was seconded to UMIST (now known as TheSchool of Materials in The University of Manchester) where promotions were gained from Section Leader to Principal Scientist. In1978, he joined the academic staff at the Corrosion and Protection Centre in UMIST, and became Professor of Corrosion Scienceand Engineering in 1990. He has previously served as Head of the Corrosion and Protection Centre and Deputy Head of theSchool of Materials at The University of Manchester.

Professor Thompson became an Emeritus Professor in 2015 after previously leading the programme. His research interests arelargely focused on the corrosion and protection of light alloys, with applications in the architecture, automotive, aerospace,lithography and packaging sectors, and electronic materials.

Professor George Thompson LATEST2 director 2010 - 2015, co-Investigatorchair in materials Engineering

Sue led the Administrative Support Team, specific responsibilities included the overall project management of the LATEST2Programme, staff and student recruitment, monitoring and reporting on the performance of the Programme and helping toensure it was on track to deliver the vision and objectives on time and within budget. She helped to develop and manageexisting and new external and internal collaborations with key stakeholders, and attracted new funding to the Programme.Additionally she was responsible for developing the communication strategy, advertising and promotion including websitedevelopment. Other aspects of her role included IP and risk management, information management including data collection,storage and dissemination.

Ms Susan C. Davis LATEST2 Programme Project manager

Lisa provided a wide ranging administrative support role across the whole Programme, working particularly closely with theProgramme Director, Project Manager, Science Communication Officer and Co-Investigators. She provided secretarial support,and was responsible for placing and receipting orders, booking accommodation and transport for the Team. She played a veryactive role in organising a wide range of meetings, workshops, symposia and conferences, including promotion of the events andbooking of the appropriate venues. She also contributed to the development and implementation of the LATEST2 ManagementInformation System, promotional materials and the website and regularly assisted and participated in outreach activities.

Ms Lisa Beattie LATEST2 Programme Administrative Assistant

Mr Rodney C. Jones Rjinntech Ltd, uKInternational Advisory Panel chairperson

Rod Jones worked in the metals industry for almost50 years and is now an independent consultant.

Having graduated in Metallurgy following asandwich degree course at Aston University withindustrial sponsorship from Henry Wiggin &Company Limited he did research initially into high temperature material for aircraft engineapplications at British Non-Ferrous Metals Research Association.

Following the transition of the company into BNFMetals Technology Centre he specialised in the fieldof process development and control of fabricationprocesses in the copper- and aluminium alloyindustries. He then moved to Alcan International to continue process developments primarily in the aluminium rolling industry.

After a period as Programme Director at theBanbury Laboratories he moved into operationshaving responsibilities for technology in the U.K.fabrication plants and subsequently across Europeas Technical Director. Whilst retaining a seniortechnology position in Europe he returned to AlcanInternational at Banbury as Laboratory Director.

Following Alcan’s merger with Alusuisse he movedto Switzerland to lead the application of aluminiumin automotives followed by obtaining the positionof VP Technology for Alcan’s Engineered Productsdivision. This position expanded further followingAlcan’s acquisition of Pechiney with globalresponsibility for the research laboratories andcritical technology teams becoming based in Paris.

Key responsibilities of this position became thetechnology aspects of the spin-off of major rolledproducts businesses as Novelis and, following the purchase of Alcan by Rio Tinto, the sale ofEngineered Products to private equity (now known as Constellium). Following completion of this sale he established RJInnTech Limited, an independent consultancy.

ProFILE

Current Advisory Panel Members

Previously Serving Advisory Panel Members

InTErnATIonAL AdVISory PAnEL

The International Advisory Panel stood as international experts in the areas of the EPSRC LATEST2 ProgrammeGrant. The Panel was made up of both national and international, academic and individual members withmany years experience. The role of the Panel was to advise the Management Team on Strategic directions tobenchmark the quality and progress of our research against our objectives and on the international stage.

Dr Helen FinchJaguar Landrover, uK

Dr Hans Polakr&d manager AerospacecoatingsAkzonobel, netherlands

John FergusonJF consultancy Services, uK

Dr Ian NorrisTwI Ltd, uK

Dr Jonathon MeyerAdditive manufacturing managerAirbus / EAdS, uK

Professor Dorte Juul Jensenuniversity of denmark

Professor Bevis HutchinsonSwerea KImAB, Sweden

Professor Warren PooleThe university of Britishcolumbia, canada

Dr Neil CalderEngineered capabilities Ltd, uK

Ms Carol Holdennorth west Automotive Alliance, uK

Mr Simon GardinerAirbus, uK

Dr Mark WhiteJaguar Landrover, uK

Dr Floris KooistraAkzonobel, netherlands

Professor Stefan Zaeffereruniversity of Aachen, germany

Principle InvestigatorsProfessor Philip Prangnell, June 2015 – present

Professor George Thompson, July 2010 – June 2015

Co-InvestigatorsDr Michele Curioni

Professor Michael Preuss

Dr Joao Quinta Da Fonseca

Professor Joseph Robson

Professor Peter Skeldon

Professor Xiaorong Zhou

EmeritusProfessor George Thompson

Administrative TeamMs Lisa Beattie, Programme Administrative Assistant

Ms Susan Davis, Programme Project Manager

Ex Administrative TeamMs Karen Donnelly-Bale, Science Communication Officer

Ms Cacia Percival, Programme Administrative Assistant

Mr Max Rowe, Science Communication Officer

Ms Laura Winters, Science Communication Officer

LATEST2 TEAm mEmBErS

Post-Doctoral Research AssociatesDr Abdelhadi Abouarkoub Dr Aleksandra Baron-Wiechec Dr Alexander CassellDr Yingchun Chen Dr Daniel Esqué Dr Sergio Gonzalez Dr Paloma Hidalgo-ManriqueDr Naveed Iqbal Mr Dingle Jose Dr Alice Laferrere Dr Yanwen LiuDr Aneta NemcovaDr Alberto Orozoco-CabelleroDr Surajkumar Pawar Dr Irina Shchedrina Dr Gaurav SinghDr Kasra Sotoudeh Dr Yingtao TianDr Gabor Timar Dr Ganesh Tirumalasetty Dr Junjie Wang Dr Li WangDr Lei YangDr Yuan Feng YangDr Sergiu Albu

PhD ResearchersDr Ramadan Abuaisha Ms Juliawati AliasDr Sepideh Aliasghari Mr Basem Al-ZubaidyDr Alphons Antonysamy Mr Michael AtkinsonDr Elkandari Bader Mr Andronikos BalaskasMr Tomas BrownsmithMr Lee Campbell Dr James Carr Dr Mark Chatterton Mr Alex CharlesworthMr Alec DavisDr Uyime Donatus Mr Jack Donoghue Mr Jefri Draup Dr Liam Dwyer Mr Dawod ElabarMr Yingwei Fan Dr Arnas Fitzner Mr Joseph FixterMr Benjamin GardenerMr Matthew GoodhallMs Irina Gordovskaya

Dr David Griffiths Dr Farid Haddadi Ms Janette HarrisMs Rose Hartley Dr Tom Hill Mr Alistair HoDr Justyna Janiec-Anwar Dr Patryk Jedrasiak Mr Aaron JordanMr Zelong Jin Dr Kayoko Kawano Mr Michael KenyonDr Lawrence Ko Ms Heike KrebsMs Virginie LandaisMs Bing LiuMr Feng LiDr Kai Li Dr Zuojia Liu Dr David Lunt Dr Chen Luo Dr Yanlong Ma Ms Faye McCarthyDr Sonia Meco Dr Tatsiana Molchan Dr Francesca Muratore Ms Laura NervoDr Ross Nolan Dr Rotimi (Joseph) Oluleke Dr Chuleeporn Paa-Rai Dr Alexandra Panteli Dr Goncalo Pardal Mr Andrew PlattsMr Jiantao (Alexander) Qi Mr Reafat ElaishDr Aiden Reilly Mr Ben RodgersMr Gunan ShangDr Ahmad Shekhe Dr Albert Smith Dr Tahani Suliman Mr Tianzhu Sun Dr Sam Tammas-Williams Mr Andres TaylorMs Jeanette Torrescano AlvarezMs Jennifer UsioboMs Yin WangDr Hao Wu Dr Lei Xu Mr Hao Zhao Dr Chaoqun (Jason) Zhang Ms Xinxin ZhangMr Wu Wei

EngD ResearchersDr Michelle Collins Dr David Mackie Dr Malgorzata Witkowska Dr Nick Wright

MPhil ResearchersMs Milena Urban

VisitorsDr Antonello Astarita Mr Manuel Azocar Professor Matthew Barnett Mr Jawed Kamran Mr Ziwen Cao Ms Anna Carangelo Mr Esteban Correa Dr Alaa El-Banna Dr Zuwei Feng Mr Pengtao Gai Mr Oscar Galvis Mr Juan Manuel Hernandez-Lopez Mr Bo-Young Jeong Mr Jawed Kamran Mr Mustafa Kocabas Dr Jianping LiMs Lea Loaks Ms Alice Mazzarolo Ms Beatriz Mingo-Ramon Ms Lisa Munoz Mr Hayato OkumuraMr Jack Palmer Mr Ferdinando Quintiero Ms Guisi Rita La MonicaMr Albert Smith Mr Mahmood Tahir Ms Laura Tamayo Mr Daniel Trost Dr Etsushi Tsuji Mr Nelson Vejar Dr Shu Yang Dr Yicong Ye Mr Alejandro ZuletaDr Xinnian Xia

D = Departed

Royal Charter Number RC000797KD262 04.16

LATEST2 Administration TeamThe University of ManchesterSchool of MaterialsE1, The MillSackville StreetManchester M13 9PL United Kingdom

tel +44 (0)161 306 5959fax +44 (0)161 306 4865email latest2@manchester.ac.ukwww.manchester.ac.uk/latest2