782_0_pitting and galvanic corrosion behavior of laser-welded stainless steels.pdf

8/9/2019 782_0_Pitting and galvanic corrosion behavior of laser-welded stainless steels.pdf

1/11

Journal of Materials Processing Technology 176 (2006) 168178

Pitting and galvanic corrosion behavior of laser-welded stainless steelsC.T. Kwok a, S.L. Fong a, F.T. Cheng b,, H.C. Man c

a Department of Electromechanical Engineering, University of Macau, Taipa, Macau, Chinab Department of Applied Physics, The Hong Kong Polytechnic University, Hung Hom, Kowloon, Hong Kong, China

c Department of Industrial & Systems Engineering, The Hong Kong Polytechnic University, Hung Hom, Kowloon, Hong Kong, China

Received 18 October 2005; received in revised form 16 February 2006; accepted 21 March 2006

Abstract

Autogenous welded specimens of austenitic (S30400 and S31603), duplex (S31803) and super duplex (S32760) stainless steels were fabricated

by laser penetration welding (LPW) with a CW Nd:YAG laser in an argon atmosphere. The microstructure and the phases present in the resolidiedzoneof the laser-welded specimens were analyzedby optical microscopy and X-ray diffractometry, respectively. The pitting and galvaniccorrosionbehaviorof the stainless steelsin thelaser-welded andunwelded conditions in 3.5% NaCl solution at 23 C was studied by meansof electrochemicalmeasurements. X-ray diffraction analysis showed that the phases present in the weld metal depended on the composition of the base metal. Whilethe laser weld for S31603 retained the original austenitic structure, the laser weld of S30400 contained austenite as the major phase and -ferriteas the minor phase. On the other hand, a slight change of -ferrite to austenite ratio was found in both the laser welds of S31803 and S32760, withaustenite present at the -ferrite grain boundaries. The welds exhibited passivity but their pitting corrosion resistance was in general deterioratedas evidenced by a lower pitting potential and a higher corrosion current density compared with those of the unwelded specimens. The decreasein pitting corrosion resistance of the welds was attributed to microsegregation in the weld zone of S31603, and to the presence of -ferrite inS30400. For the duplex grades S31803 and S32760, the disturbance of the ferrite/austenite phase balance in the weld zone could be the cause of the decrease in corrosion resistance. The initial free corrosion potentials of the unwelded specimens were considerably higher than those of thecorresponding laser welds, indicating that the welds were more active and were expected to act as anodes in the weldment. The ranking of galvaniccurrent densities ( I G) of the couples formed between the laser-welds (LW) and the as-received (AR) specimens with area ratio 1:1, in ascendingorder, is: AR S31603/LW S31603 < AR S31803/LW S31803 < AR S32760/LW S32760 < AR S30400/LW S30400. The recorded I G in all coupleswas low (in the range of nA/cm 2). 2006 Elsevier B.V. All rights reserved.

Keywords: Laser welding; Stainless steels; Pitting corrosion; Galvanic corrosion; -Ferrite

1. Introduction

Owing to their excellent mechanical properties andcorrosionresistance, stainless steels are extensively used in many indus-trial and medical applications. Commercial products such asrazors, cigarette lighters, watch springs, motor and transformerlamination, hermetic seals, battery and pacemaker cans, andhybrid circuit packages require delicate welds with high qual-ity and precision. A kilowatt laser beam can melt and vaporizethe material, and the pressure of the vapor displaces the moltenmaterial so that a narrowand deep keyhole is formed. The key-hole supports the transfer of the laser energy into the materialand guides the laser beam deep into the material. Laser pene-

Corresponding author. Tel.: +852 2766 5691; fax: +852 2333 7629. E-mail address: [email protected] (F.T. Cheng).

tration welding (LPW) can produce low-distortion and preciseweldments with minimal heat-affected zones [1,2]. In LPW of stainless steels, phase transformation is common. The mechani-cal properties and corrosion resistance of laser-welded stainlesssteels may be deteriorated due to microsegregation, unfavorablephase content, presence of porosities, solidication cracking,micro-ssures and loss of materials by vaporization. Galvaniccell may also be set up between different parts of the weld-ment.Galvaniccorrosion in weldmentsshould notbeoverlookedbecause it can lead to accelerated deterioration of the anodicregion especially in hostile environments. Pitting corrosion andgalvaniccorrosionhavebeeninvestigatedin thecouplesbetweendissimilar alloyssuch as 316L, Ti, Nb andTa [3], CoCr andREX734 [4], annealed and cold-worked 316L [5], and GTAW weldedand unwelded N08031 [6]. The pitting corrosion resistance of severalaustenitic stainlesssteels weldedby a CO 2 laser hasbeeninvestigated by Vilpas [7]. However, reports on the galvanic

0924-0136/$ see front matter 2006 Elsevier B.V. All rights reserved.

doi:10.1016/j.jmatprotec.2006.03.128
mailto:[email protected]://localhost/var/www/apps/conversion/tmp/scratch_4/dx.doi.org/10.1016/j.jmatprotec.2006.03.128http://localhost/var/www/apps/conversion/tmp/scratch_4/dx.doi.org/10.1016/j.jmatprotec.2006.03.128mailto:[email protected]


2/11

C.T. Kwok et al. / Journal of Materials Processing Technology 176 (2006) 168178 169

corrosion behavior in laser weldments of stainless steels arescarcely reported. The aim of the present study is to investi-gate the pitting corrosion behavior of various stainless steels inthe laser-welded and unwelded conditions in 3.5% NaCl solu-tion, and the galvanic effect in the laser weldments. The changein the pitting corrosion behavior of the laser-welded specimensand the presence of galvanic effect in the laser-weldments wereexplained in terms of the change in microstructure and chemicalcompositions. It must be pointed out that no attempt of opti-mization of processing parameters was made. The present studythus would serve only as a preliminary baseline investigation forreference in future studies on laser welding of stainless steels.Moreover, detailed mechanical properties will be reported else-where.

2. Experimental details

Austenitic (UNS S30400 and S31603), duplex (UNS S31803) and superduplex (S32760) stainless steels with different chemical compositions ( Table 1 )

were selected in the present study. The as-received (AR) stainless steels were inthe form of plates with a thickness of 1 mm. LPW was carried out using a high-power CW Nd:YAG laser with a power of 0.9 kW and a beam size of 0.5 mm indiameter (6.1 105 W/cm2). The laser beam was transmitted by an optical breandfocusedontothe specimenby a BK-7 lens with a focal lengthof 80mm. Theexible optical bre delivery was controlled by an XY table. Argon owingat 20 l/min was used as the shielding gas. In order to reduce thermal distortionof the workpiece, it was held in place by a clamping device. Beam scanningspeed of 35 mm/s was used. Such laser parameters were chosen for achievingfull penetration and minimal thermal distortion. The bead-on-plate seam weldswere made on the plates by line scanning of the focused laser beam.

The laser-welded specimens were sectioned, polished and etched. Themicrostructure and phases in the resolidied zones were analyzed by opticalmicroscopy (OM) and X-ray diffractometry (XRD), respectively. The radiationsource of the X-ray diffractometer was Cu K with nickel lter and generated

at 1.2 kW and the scan rate was 0.25

s 1

, with the scanning direction along theweld. The respective volume fraction of -ferrite present in the stainless steelswas evaluated by the direct comparison method [8]. Due to rapid solidication,the specimens exhibited a preferred orientation to some extent. The integratedintensities of the (11 1), (20 0) and (22 0) diffraction peaks for -austenite andthe (11 0) and (2 0 0) peaks for -ferrite were taken into account. The volumefraction of -ferrite (C ) was calculated using the following expression accord-ing to the ASTM Standard E974 [9]:

C = 1 +(I (111) /R (111) ) + (I (200) /R (200) ) + (I (220) /R (220) )

1.5((I (110) /R (110) ) + R (I (200) /R (200) ))

1

= 1 +(I (111) / 182.8) + (I (200) / 81.6) + (I (220) / 44.4)

1.5((I (110) / 233.8) + (I (200) / 31.9))

1(1)

where I (h k l) and I (h k l) are the integrated intensities of a given crystallographicplane (h k l) from the and phases, respectively, and the values of R (h k l)and R (h k l) of and for various planes were obtained from Jatczak et al.[10]. The chemical compositions of the resolidied microstructure after LPWwere analyzed by energy dispersion X-ray spectrometry (EDS). In addition,

the hardness of the laser-welded specimens was determined using a Vickersmicrohardness tester. The load applied was 200 g and the loading time was 15 s.

Cyclic potentiodynamic polarization scans were carried out using an EG&GPARC 273 corrosion system according to ASTM Standard G61-94 [11] f orinvestigating the pitting corrosion behavior. Free corrosion potential ( E c) mea-surement and galvanic corrosion test were conducted using the same corrosionsystem conforming to ASTM Standard G71-81 [12]. The base stainless steelsand their welds for corrosion studies were cut into 6mm 10 mm plates. Priorto corrosion tests, the surface of all specimens was freshly ground and thenpolished with 1 m-diamond paste in order to keep the surface roughness con-sistent. The specimens were embedded in epoxy resin with an exposed areaof 4mm 2 of the weld track or unwelded region. The specimens were cleaned,degreased and dried before the polarization test in 3.5% NaCl solution, whichwas kept at a constant temperature of 23 C and open to air. A saturated calomelelectrode (SCE) was used as the reference electrode and two parallel graphiterods served as the counter electrode for current measurement. For the cyclicpotentiodynamic polarization test, all data were recorded afteran initial delayof 30 min for the specimen to stabilize. The potential was increased from 200mVbelow the corrosion potential in the anodic direction at a scan rate of 5 mV s 1 .The scan was then reversed when an anodic current density of 5mA cm 2 wasreached and continued until the loop closed at the protection potential. Galvaniccorrosion test was performed using the built-in zero-resistance ammeter (ZRA)in the potentiostat.The galvaniccurrent density ( I G) andgalvanic potential( E G )in the couples formed by the as-received specimen and the laser weld were con-tinuously monitored for 24 h. The exposed area ratio of anode to cathode of allgalvanic couples was 1:1.

3. Results and discussion

3.1. Microstructural and metallographic analysis

Full penetration was achieved in all specimens in the LPWand the widths of welds were about 0.8mm. Typical cross-sectional view of laser-welded (LW) S31603 is shown in Fig. 1.

Fig. 1. Cross-sectional view of laser-welded S31603.

Table 1Nominal compositions (wt.%) of various stainless steels

Fe Cr Ni Mo Mn W Cu C Si P S N Cr eq /Nieq a

S30400 Balance 18.4 8.7 1.6 2.1 0.08 0.3 0.1 0.1 1.70S31603 Balance 17.6 11.2 2.5 1.4 1.4 0.03 0.4 1.62S31803 Balance 22.5 5.6 2.9 1.5 0.2 1.6 0.03 0.4 3.59S32760 Balance 25.6 7.2 4.0 0.6 0.8 0.7 0.03 0.3 0.2 2.09

a

Creq =[Cr] + [Mo] + 1.5[Si] + 0.5[Cb]. Ni eq = [Ni] + 0.5[Mn] + 30[C]+ 30[N].


3/11

170 C.T. Kwok et al. / Journal of Materials Processing Technology 176 (2006) 168178

Fig. 2. XRD patterns of as-received stainless steels and laser welds: (a) S30400, (b) S31603, (c) S31803 and (d) S32760.

X-ray diffraction analysis showed that the phases present in theweld metals depended on the composition of the base metal.According to the XRD patterns in Fig. 2, the laser weld forS31603 retained the original austenitic structure, while the laser

weld for S30400 contained austenite as the major phase and -

ferrite as the minor phase. On the other hand, both S31803 andS32760were mainly composed of -ferrite,with austenite as theminor phase. The microstructures of the stainless steels beforeand after laser welding are shown in Fig. 3. In LW S30400, the

skeletal network of residual -ferrite is present in the austenitic


4/11


matrix ( ) as shown in Fig. 3(e). Austenitic dendrites in dif-ferent orientations are observed in LW S31603 as shown inFig. 3(f ). After laser welding, the grain size of LW S30400 andLWS31603, which were predominantly austenitic, was reneddue to rapid solidication. On the contrary, the grain size in LW

S31803andLW S32760was increasedand their microstructuresare shown in Fig. 3(g and h), respectively. The Widmanstattenstructure of semi-continuous dendritic austenite was present inthe columnar grain boundaries of ferrite. When the melt poolof the weld zone of the duplex grade stainless steels solidies,

Fig. 3. Microstructure of various stainless steels in unwelded (as-received, AR) condition: (a) AR S30400, (b) AR S31603, (c) AR S31803 and (d) AR S32760; and

in laser-welded (LW) condition: (e) LW S30400, (f) LW S31603, (g) LW S31803 and (h) LW S32760.


5/11


Fig. 3. (Continued ).


6/11


Table 2Volume fraction of -ferrite and microhardness in as-received (AR) and laser-welded (LW) regions

Stainlesssteels

C (AR)(%)

C (LW)(%)

Differencein C (%)

Hv0.2(AR)

Hv0.2(LW)

S30400 0 14 +14 176 301S31603 0 0 0 179 194S31803 60 62 +2 268 316S32760 54 50 4 290 314

the possible phase transformation sequence upon cooling maybe represented as:

Liquid liquid + ferrite ferrite ferrite + austenite

The degree of completion of the transformation and hence thenal phase structure of the weld metal depend on the composi-tion of the base metal and the welding parameters [13].

Based on the XRD spectra, the volume fractions of -ferrite(C ) of various laser welds were calculated using Eq. (1) andshown in Table 2 . -ferrite did not exist in LW S31603, whereas14%, 62% and 50% of -ferrite were present in LW S30400,LW S31803 and LW S32760, respectively. The effect of laserwelding on themicrostructural changeof various stainlesssteels

underthe samelaser processingconditions wasdifferentbecauseof their difference in chemical compositions. The ratios of thechromium equivalent (Cr eq) and the nickel equivalent (Ni eq) of the stainless steels are shown in Table 1 . As the Cr eq /Nieq ratioincreased, the ferrite-forming tendency of the stainless steelsincreased. Thehighest volume fraction of -ferrite wasobservedin S31803, which hadthe highest Cr eq /Nieq ratio. In addition, thesolid-state transformation of -ferrite to austenite is consideredtobe diffusional.Thus,the high solidication rate typical in laserprocessing would also suppress the ferrite-to-austenite transfor-mation, resulting in a high fraction of -ferrite. The increasein volume fraction of -ferrite in LW S31803 in the presentstudy was also reported by others [14,15] in theautogenous laserwelding of duplex stainless steels. The disturbance of the fer-rite/austenite phase balance in theweld metal might be remediedvia the use of welding consumables having a more austeniticcomposition, and/or the use of a shielding gas containing anappropriate amount of N 2, which is an austenite stabilizer [16].However, there is a higher probability of forming intermetallic

precipitates and nitrides in the weld metal, both of which woulddecrease the corrosion resistance [2,17].

The hardness proles along the depth and across the cross-section of the weld zones of various specimens are shown inFig. 4, and the results are summarized in Table 2 . The hardness

Fig. 4. Hardness proles of various laser-welded specimens: (a) along the depth of the cross-section and (b) across the cross-section.


7/11


Fig. 5. E c vs. time of the as-received stainless steels and their corresponding weldments: (a) S30400, (b) S31603, (c) S31803 and (d) S32760 in 3.5% NaCl solution.

values in the welds were nearly constant and higher than thoseof the base metals (hardness outside the welds) as shown inFig. 4(b). The hardness of the weld zone for S31603, S31803and S32760 was higher by 818% as compared with that of thebase metals. Themost signicant changein hardness is observedin LW S30400, with an increase of about 70%. The increase inhardness could be attributed to the renement of grains and alsoto the presence of hard -ferrite.

3.2. Free corrosion potential

From measurements of the free corrosion potentials ( E c) of the base stainless steels and their corresponding laser welds(Fig. 5), information about the dynamic behavior of the passiveoxide lm might be obtained. The E c of the unwelded speci-mens increased towards more noble values and became steadyat the end of the 2-h test. This reects that the growth of passiveoxide wasalmost complete. The steady values of E c after 2 h areshown in Table 3 . For unwelded S32760, the oxide lm was themost stable because it was highly alloyed with the elements Cr,Mo and N, all of which could enhance passivity. It can be alsoobserved that the E c of all unwelded stainless steels are con-siderably higher than those of their corresponding welds. Forinstance, the E c of as-received S32760 (3 mV SCE) is higher

than that of its laser weld ( 327 mV SCE).

3.3. Pitting corrosion behavior

Cyclic potentiodynamic polarization curves of variousunwelded stainless steels and their laser welds in 3.5% NaClsolution at 23 C are shown in Fig. 6. The corrosion parameters,including pitting potential ( E pit), protection potential ( E prot ) andcorrosion current density ( icorr ), are summarized in Table 3 . Allunwelded stainless steels and their laser welds exhibited passiv-ity in 3.5% NaCl solution. However, there was a general andsubstantial shift of the polarization curves towards higher cur-rent densities, indicating deterioration in corrosion resistance.

Table 3Corrosion parameters of unwelded (AR) and laser-welded (LW) stainless steelsin 3.5% NaCl solution at 23 C, open to air

Specimens E c (mV) E pit (mV) E prot (mV) icorr ( A/cm2)

AR S30400 270 330 39 0.416LW S30400 310 85 11 3.475AR S31603 256 423 76 0.252LW S31603 343 195 39 6.456AR S31803 301 1170 1179 0.405LW S31803 348 671 111 9.429AR S32760 3 1040 980 0.138LW S32760 327 1040 954 0.518


8/11


Fig. 6. Potentiodynamic polarization curves of the as-received stainless steels and their corresponding weldments: (a) S30400, (b) S31603, (c) S31803 and (d)S32760 in 3.5% NaCl solution.

In addition, the pitting corrosion resistance and the repassiva-tion capability of the laser welds were lower than those of theunwelded specimens as reected by lower values in both E pitand E prot . The ranking of the pitting corrosion resistance of thespecimens is as follows:

ARS30400 < ARS31603 < ARS32760 < ARS31803

and

LWS30400 < LWS31603 < LWS31803 < LWS32760 .

Decrease in E pit is observed in the laser welds for S30400(from 330 mVto 85mV SCE), S31603(from423mV to195mVSCE) and S31803 (from 1170 mV to671 mV SCE). On the otherhand, there is no signicant change in E pit in the laser weld forS32760. In addition, the corrosion current densities of all weldsincreased.

While the results in the present study indicate a decrease incorrosion resistance for stainless steels due to laser welding,laser cladding (LC) of stainless steel on mild steel followedby laser remelting resulted in increase of corrosion resistanceas reported by Li et al. [18,19] . This is not unexpected as inlaser surfacing the processing condition is chosen to yield ahomogeneous surface layer while in welding the primary aim is

to achieve joining. Some improvement in pitting resistance of

laser-surface melted S30400 [2023] and S31603 [20,24] wasreported by several authors due to the removal of MnS inclu-sions (for S30400 and S31603) and the trapping of sulfur inthe -ferrite (for S30400). For S32760, there is no signicantchange in E pit and E prot resulting from laser surface melting[20], consistent with the present results.

The change in corrosion behavior due to laser welding couldarise from different causesdepending on the base stainless steel.Pan et al. attributed the deleterious effect of -ferrite on thepitting corrosion resistance of S32100 to the galvanic effectexisting between -austenite and -ferrite [25]. In fusion weld-ing, solidication from the melt pool in general results in localcompositional variations, which would in turn result in less sta-ble passive lm and hence lower corrosion resistance [26]. Thecompositional heterogeneity in the weld metal could arise fromthree main causes: microsegregation during weld metal solid-ication, element partition in solid-state transformation fromferrite to austenite, and precipitation of intermetallic phases,carbides and nitrides, leading to the formation of Cr-depletedregions. The microstructure in a weld is a complex functionof the solidication parameters (solidication rate and temper-ature gradient at the solid/liquid interface), which in turn aredetermined by the processing parameters and the alloy compo-

sition [27,28] . Though microsegregation is generally small in


9/11


Table 4EDS composition analysis of different regions in laser welds

Specimen Region Cr (wt.%) Ni (wt.%) Mo (wt.%)

LW S30400 16.4 7.8 19.9 8.2

LW S31603 Dendrite core ( ) 16.1 9.6 1.5

Interdendritic ( ) 18.2 12.3 2.1LW S31803 20 6.3 1.8

24 5.4 2.6

LW S32760 26.7 7.1 3.2 26.1 7.2 3.8

laser welding in comparison with conventional welding becauseof a higher solidication rate in the former, some degree of microsegregation still occurred in the laser welds of variousstainless steels in the present study. EDS compositional anal-ysis of the different phases or regions in the laser welds isshown in Table4 . ForLW S31603, thedifference in compositionbetween thedendriticcoresand the interdendritic regions revealsmicrosegregationduringsolidication,witha subsequent Cr andMo enrichment of the liquid phase when the solidication frontgrew from the core to the boundary of the dendrites while Nisegregated in the opposite direction, similar to that reported inthe literature [29]. For LW S30400, which exhibited primaryaustenitic solidication, a small amount of ferrite was formedfrom the melt between dendrites as result of microsegregation.For LW S31803, which was predominantly ferritic, differencein the composition between austenite and ferrite existed, sim-ilar to the case of LW S30400. The Cr, Ni and Mo contentsin the austenite and ferrite for LW S32760 were very close in

each phase, indicating minimal microsegregation. The impair-ment in the pitting corrosion resistance of the laser welds mightbe attributed to microsegregation, and also to unfavorable fer-rite/austenite phase content [30], in addition to the presence of defects arising from welding. The corrosion behavior of LWS32760 was relatively close to that of the base metal becausemicrosegregation was minimal.

3.4. Galvanic corrosion behavior

Plots of galvanic potentials ( E G) and galvanic current den-sities ( I G) of the galvanic couples between the base stainlesssteels and their corresponding laser welds as a function of time

are shown in Fig. 7. Since the values of the E c for all base stain-less steels were higher than those of their welds ( Fig. 5), thewelds were more active and are expected to act as the anodewhen coupled to the corresponding base metals. From Fig. 7, itcan be observed that the current densities of all the couples werechanging with time in the initial stage and then reached differ-ent steady-state values at the end of the 24-h test. The values of E G and I G for different galvanic couples attained after 24h areshown in Table 5 . The ranking of I G in the galvanic couples inascending order is as follows:

ARS31603 / LWS31603 < ARS31803 / LWS31803

< ARS32760 / LWS32760 < ARS30400 / LWS30400

Fig. 7. Time dependence of (a) E G and (b) I G for various galvanic couples in

3.5% NaCl solution.

Thegalvaniccorrosion rates (i.e. I G) in all these couples werelow, only in therangeofnA/cm 2. Thegalvanic corrosionrate in agalvaniccouple dependson thedifference in corrosionpotentials(the driving force) of the members in the galvanic couple and ontheir polarization characteristics (the resistance), both of whichin turn depend on the compositions and microstructures of themembers [31].

I G for AR S30400/LW S30400 was the highest due to a largedifference in volume fraction of -ferrite for members in thiscouple (+14%). The amount of -ferrite in the austenite matrixdetermines the E c, and hence the I G in the couple. The valuesof I G in AR S32760/LW S32760 and AR S31803/LW S31803were much smaller since the difference in volume fraction of -

Table 5Steady-state E G and I G of galvaniccouplesbetweenthe unweldedstainless steelsand their weldments

Galvanic couples E G (mV) I G (nA/cm 2)

AR S30400/LW S30400 311 78.6AR S31603/LW S31603 330 26AR S31803/LW S31803 304 8.6AR S32760/LW S32760 347 35


10/11


ferrite was relatively small. I G was the lowest in AR S31603/LWS31603 because there was no change in phase structure (100%austenite) in this case, and galvanic corrosion was attributableto the minor changes in microstructure. Nevertheless, the gal-vanic couples formed between the base stainless steels and theirwelds exhibited negligible galvanic effect as evidenced by thelow values of I G, only of the order of nA/cm 2. There is no risk of triggering the phenomenon of pitting corrosion, because the E pit of the welds for various stainless steels were in the rangeof 851040mV versus SCE and much higher than the E G of various couples (ranging from 347mV to 304 mV SCE). Inaddition, the welded surface of different stainless steels after thegalvanic corrosion tests did not reveal any surface damage suchas pits or discoloration.

4. Conclusions

Autogenous laser welding of two austenitic and two duplexstainless steels in Ar atmosphere was attempted and the pittingand galvanic corrosion behavior of the weldments were studied.The following conclusions can be drawn:

1. The laser weld of S30400 was essentially austenitic with thepresence of a small amount of ferrite while the laser weld of S31603 remained purely austenitic. On the other hand, theferrite/austenite phase balance for the two duplex stainlesssteels was slightly disturbed.

2. The microhardness of the laser welds for various stainlesssteels generally increased, possibly due to the increase in thevolume fraction of ferrite, or to grain renement.

3. All laser welds for stainless steels exhibited passivity in3.5% NaCl solution but their pitting resistance deterioratedas evidenced by lower pitting potentials andhigher corrosioncurrent densities compared with those of the base metals. Itis attributed to microsegregation (for all stainless steels stud-ied), to the presence of -ferrite (S30400) or to incorrectphase balance (S31803 and S32760).

4. Galvanic current densities in thecouples formed between thebase stainless steels and their welds were very low (in rangeof nA/cm 2), indicating very small galvanic effect.

Acknowledgments

Theauthors wish to acknowledge thesupport from the infras-tructure of the University of Macau and the Hong Kong Poly-technic University.

References

[1] J. Mazumder, Laser beam welding, ASM Handbook, vol. 6, 10th ed.,Welding, Brazing, and Soldering, ASM International, Materials Park,OH, USA, 1990, pp. 263268.

[2] D. Schuocker, Welding with lasers, in: High Power Lasers in ProductionEngineering, Imperial College Press, UK, 1999, pp. 337370.

[3] J. Gluszek, J. Masalski, Galvanic coupling of 316L steel with titanium,niobium, and tantalum in Ringers solution, Br. Corros. J. 27 (1992)

135138.

[4] L. Reclaru, R. Lerf, P.Y. Eschler, A. Blatter, J.M. Meyer, Pitting, creviceand galvanic corrosion of REX stainless-steel/CoCr orthopedic implantmaterial, Biomaterials 23 (2002) 34793485.

[5] C.C. Shih, C.M. Shih, Y.Y. Su, S.J. Lin, Galvanic current induced byheterogeneous structures on stainless steel wire, Corros. Sci. 47 (2005)21992212.

[6] E. Blasco-Tamarit, A. Igual-Munoz, J. Garcia Anton, D. Garcia-Garcia,Effect of aqueous LiBr solutions on the corrosion resistance and galvaniccorrosion of an austenitic stainless steel in its welded and non-weldedcondition, Corros. Sci. 48 (2006) 863886.

[7] M. Vilpas, Prediction of Microsegregation and Pitting Corrosion Resis-tance of Austenitic Stainless Steel Welds by Modelling, VTT Publica-tions, 390 VTT, Espoo, 1999, p. 70.

[8] B.D. Cullity, Elements of X-Ray Diffraction, Addison-Wesley, NY, 1978,p. 411.

[9] ASTM Standard E975-03, Standard Practice for X-Ray Determinationof Retained Austenite in Steel with Near Random Crystallographic Ori-entation, ASTM International, Philadelphia, 2003.

[10] C.F. Jatczak, J.A. Larson, S.W. Shin, Retained Austenite and its Mea-surements by X-Ray Diffraction, SP-453, SAE, Philadelphia, 1980, p.14.

[11] ASTM Standard G61-94, Standard Method for Conducting Cyclic Poten-tiodynamic Polarisation Measurements for Localised Corrosion Suscepti-bility of Iron-, Nickel-, or Cobalt-Based Alloys, Annual Book of ASTMStandards, ASTM International, Philadelphia, 1994.

[12] ASTM Standard G71-81, Conducting and Evaluating Galvanic Tests inElectrolytes, Annual Book of ASTM Standards, ASTM International,Philadelphia, 1992.

[13] D.N. Noble, Selection of wrought duplex stainless steels, ASM Hand-book, vol. 6, 10th ed., Welding, Brazing, and Soldering, ASM Interna-tional, Materials Park, OH, USA, 1990, pp. 471481.

[14] J.M. Robinson, R.C. Reed, A. Camyab, CO 2 laser welding of duplexand super-duplex stainless steels (the effect of argonnitrogen assist gasmixtures), in: Proceedings of the 4th International Conference on Trendsin Welding Research, TN, USA, 1995, pp. 499504.

[15] N.A. McPherson, H. Samson, T.N. Baker, N. Suarez-Fernandez, Steelmicrostructure in autogenous laser welds, J. Laser Appl. 15 (2003)200210.

[16] V. Muthupandi, P. Bala Srinivasan, S.K. Seshadri, S. Sundaresan, Cor-rosion behavior of duplex stainless steel weld metals with nitrogenadditions, Corros. Sci. Technol. 38 (2003) 303308.

[17] N.A. McPherson, K. Chi, T.N. Baker, Submerged arc welding of stain-less steel and the challenge from the laser welding process, J. Mater.Process. Technol. 134 (2003) 174179.

[18] R. Li, M.G.S. Ferreira, M.A. Anjos, R. Vilar, Localized corrosion of laser surface cladded UNS S31254 superaustenitic stainless steel onmild steel, Surf. Coat. Technol. 88 (1997) 9095.

[19] R. Li, M.G.S. Ferreira, M.A. Anjos, R. Vilar, Localized corrosion per-formance of laser surface cladded UNS S44700 superferritic stainlesssteel on mild steel, Surf. Coat. Technol. 88 (1997) 96102.

[20] C.T. Kwok, H.C. Man, F.T. Cheng, Cavitation erosion and pitting cor-rosion of laser surface melted stainless steels, Surf. Coat. Technol. 99(1998) 295304.

[21] E. McCafferty, P.G. Moore, Electrochemical behavior of laser-processedmetal surfaces, J. Electrochem. Soc. 133 (1986) 10901096.

[22] O.V. Akgun, T.O. Inal, Desensitization of sensitized 304 stainless steelby laser surface melting, J. Mater. Sci. 30 (1992) 21472153.

[23] M. Carbucicchio, G. Palombarini, M. Rateo, G. Sambogna, Improve-ment of surface properties of AISI 304 stainless steel by laser melting,Hyperne Interact. 112 (1998) 1924.

[24] C. Carboni, P. Peyre, G. Beranger, C. Lemaitre, Inuence of high powerdiode laser surface melting on the pitting corrosion resistance of type316L stainless steel, J. Mater. Sci. 37 (2002) 37153723.

[25] Q.Y. Pan, W.D. Huang, R.G. Song, Y.H. Zhou, G.L. Zhang, Theimprovement of localized corrosion resistance in sensitized stainless steelby laser surface remelting, Surf. Coat. Technol. 102 (1998) 245255.

[26] T.G. Gooch, Corrosion behavior of welded stainless steel, Weld. J. 75(1996) 135s154s.


11/11


[27] S.A. David, S.S. Babu, J.M. Vitek, Welding: solidication andmicrostructure, JOM 55 (2003) 1420.

[28] N. Suutala, Effect of solidication condition on the solidication modein austenitic stainless steels, Metall. Trans. A 14 (1983) 191197.

[29] W.R. Cieslak, D.J. Duquette, W.F. Savage, Pitting corrosion of stainlesssteel weldments, in: S. David (Ed.), ASM Conference on Trends inWelding Research in the United States, New Orleans, USA, November1618, 1981, pp. 361379.

[30] A. Wahid, D.L. Olson, D.K. Matlock, Corrosion of weldments,ASM Handbook, vol. 6, 10th ed., Welding, Brazing, and Solder-ing, ASM International, Materials Park, OH, USA, 1990, pp. 10651069.

[31] H.P. Hack, Galvanic corrosion, in: R. Baboian (Ed.), Corrosion Testsand Standards: Application and Interpretation, ASTM STP 978, ASTM,1995, pp. 186196.

782_0_pitting and galvanic corrosion behavior of laser-welded stainless steels.pdf

Documents