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TRANSCRIPT
Layer-by-layer Adsorption: Factors Affecting the Choice of Substrates and Polymers
Iuliia S Elizarova*1 and Paul F Luckham2
1 Department of Materials, Imperial College London, Prince Consort Road, Royal School of Mines, London SW7 2BP, UK
2Department of Chemical Engineering and Chemical Technology, Imperial College London, Prince Consort Road, London SW7 2AZ,
UK
Highlights
Materials and mechanisms of the electrostatic layer-by-layer procedure are examined
The electrostatic layer-by-layer procedure is a process consisting of distinct stages
Each stage (adsorption of the first layer, second layer, multi-layering) is specific
Understanding of the underlying mechanisms serves as a guide to the technique
Abstract
The electrostatic layer-by-layer technique for fabrication of multi-layered structures of various sizes and
shapes using flat and colloidal templates coupled with polyelectrolyte layer-forming materials has attracted
significant interest amongst both academic and industrial researchers due to its versatility and relative
simplicity of the procedures involved in its execution. Fabrication of the multi-layered structures using the
electrostatic layer-by-layer method involves several distinct stages each of which holds great importance
when considering the production of a high-quality product. These stages include selection of materials (both
template and a pair of construction polyelectrolytes), adsorption of the first polyelectrolyte layer onto the
selected templates, formation of the second layer comprised of the oppositely charged polyelectrolyte and
guided by the interactions between the two chosen polyelectrolytes, and multi-layering, where a selected
number of layers are produced, and which is conditioned by both intrinsic properties of the involved
construction materials and external fabrication conditions such as temperature, pH and ionic strength. The
current review summarises the most important aspects of each stage mentioned above and gives examples of
the materials suitable for utilization of the technique and describes the underlying physics involved.
Introduction
Layer-by-layer assembly is a highly versatile, reproducible, efficient and simple technique for the fabrication
of multi-layered films with easily controlled and tuneable properties (thickness, composition, structure,
functions) on and around the selected substrate of any type and shape. This technique can be executed through
a variety of approaches based on different mechanisms, including electrostatic interactions, hydrophobic
interactions, hydrogen bonding, charge-transfer interactions, biologically specific interactions, coordination
chemistry, covalent bonding, stereocomplexation and surface sol-gel process [1].
Electrostatically-driven layer-by-layer was the original multi-layering procedure introduced by Iler [2] in the
very first paper regarding the subject in 1966. The study described a solution-based deposition of alternating
layers of negatively charged silica and positively charged boehmite particles onto a flat glass substrate. The
next study concerning this technique was reported by Decher 25 years later, in 1991, and described layer-by-
layer deposition of oppositely charged molecules (polyelectrolytes) onto charged flat substrates [3, 4]. Among
others, the electrostatic layer-by-layer technique has been used extensively in research ever since the latter
study was published (Figure 1), resulting in the development of the well-established conventional layer-by-
layer procedure.
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Figure 1 – Growth of the Number of the Layer-by-layer Related Publications (Web of Science Search 2018).
This procedure involves immersing (for flat surfaces) or mixing (for colloidal templates) the substrate material
with a dilute polyelectrolyte solution, waiting for polyelectrolyte to adsorb, washing the freshly-layered
substrate(s) to remove excess polyelectrolyte and repeating these steps for each following layer to be
fabricated. A schematic of the process is presented in Figure 2.
Figure 2 – Conventional electrostatic layer-by-layer assembly on (a) flat substrate and (b) colloidal substrates
(illustration adapted from [5] with permission of The Royal Society of Chemistry).
Electrostatic interactions, which allow for such consecutive deposition of charged materials, is by far the most
widely-used and studied mechanism within the layer-by-layer research area and is considered to be one of the
most important types of interaction in processes when both participating materials (substrate/layering
material) are charged [1]. The existing wide usage and the versatility of the technique facilitates its further
development and increasingly attracts new research interest; it is, therefore, necessary to have an in-depth
discussion of the theory behind the relevant aspects of the procedure, such as the choice of materials and their
properties, as well as the mechanisms involved in the multi-layering process. The outcomes of such a
discussion are presented in the current review and can be used as a starting manual for the goal-based
implementation of the technique. This review starts with a description of desired properties of the construction
materials – templates (flat surfaces and colloidal substrates such as particles, emulsions and liposomes) and
polyelectrolytes which are relevant to the layer-by-layer procedure. It continues with a detailed examination of
the underlying mechanisms and influential factors behind the electrostatic layer-by-layer assembly, including
adsorption of polyelectrolyte onto a solid surface, polyelectrolyte-polyelectrolyte interactions and,
consecutively, polyelectrolyte multi-layering.
Current review focuses on the fundamentals of the layer-by-layer procedure and does not describe the
techniques and methods of its implementation. Such methods and techniques can be found in the extensive
review by Guzmán et al [6].
1. Electrostatic layer-by-layer construction materials
Two functional components involved in the electrostatic layer-by-layer assembly are a charged template
material and two oppositely charged coating materials (polyelectrolytes).
1.1 Template materials
Templates of any shape and size are generally suitable for the electrostatic layer-by-layer process with the
only requirement of having a surface charge, therefore, a wide range of materials can be used as a core
structure for fabrication of multi-layers, including flat substrates, micro- and nano-scale soft and hard
colloidal templates.
1.1.1 Flat substrates
The use of flat substrates as “foundations” for the film build-up in multi-layering experiments was first
described in several of the original electrostatic layer-by-layer assembly studies by Decher [3, 4]. A planar
substrate geometry allows for the creation of flat polymer films with tunable thickness the area of which is
only limited by the fabrication methods (for example, the size of the polyelectrolyte solution container that is
used in the conventional dipping layer-by-layer procedure). Depending on the morphology of the selected
substrate, the resulting films can be of various surface geometries – smooth, wavy, porous or even patterned,
therefore, the term “planar” is used very generally and applies to any substrate that produces, technically, a
three-dimensional structure, but with low height-to-width aspect ratio.
The choice of material that can be used as a flat substrate for the layer-by-layer assembly is mainly guided by
application considerations which can be classified into two large groups. The first group requires so-called
“free-standing” multi-layered films that must be separated from substrates before being used for different
purposes. The second group, in contrast, utilises the layer-by-layer procedure to coat the substrate of interest
with a goal of providing various functionalities.
Free-standing polyelectrolyte multi-layered films can be obtained using two approaches. The first approach
utilises sacrificial substrates such as cellulose acetate [7, 8, 9] or polystyrene [10] that are deposited onto
various surfaces (for example, gold-coated glass) to act as a dissolvable precursor. Once the desired number of
layers is achieved, the multi-layered substrate is immersed in an appropriate solvent that only affects the
precursor and not the polyelectrolyte layers (for example, cellulose acetate is most commonly dissolved using
acetone, polystyrene – using tetrahydrofuran). The second approach does not rely on any anchor layer and
utilises properties of the substrate itself. Readily detachable polyelectrolyte films can be assembled using
hydrophilic surfaces. For example, one study reported using hydrophilic silicone as a base for the layer-by-
layer film construction in which the resulting film can be detached by simply immersing it in water [11]. This
preparation method does not require any additional film treatment steps to ensure its stability. Other studies
describe fabrication of films based on hydrophobic substrates such as propylene [12, 13] and Teflon (pre-
coated with polyethylene glycol and poly(acrylic acid)) [12, 14]; such films can be easily detached from a
substrate when dried, however, post-layer-by-layer cross-linking is required to keep the film stable and to
detach it without introducing any defects [11].
Fabrication of polyelectrolyte and composite colloid coatings using the layer-by-layer procedure has found its
applications in biomedicine, sensoring, optics, microelectronics and other industries. Layer-by-layer films can
provide further functionality in addition to the properties of the material to be coated by utilising intrinsic
properties of polyelectrolytes themselves, or by introducing additional agents into films. The material in need
of a multi-layered coating in such cases itself acts as a substrate. A good variety of examples can be found in
the area of biomaterials. One study concerning the coagulation of human blood on multi-layered
chitosan/dextran sulfate films used a cell culture plastic disk made of poly(ethyleneterephthalate) as a film-
base [15]; the multi-layered disks were then used for experiments without detachment. Another study reported
using treated poly(L-lactic acid), which is a biocompatible polymer that is widely used in orthopaedics, as a
positively-charged substrate for collagen/heparin multi-layers that are intended for regulation of bone cellular
functions (positive charge on the PLLA substrates is obtained by aminolysis process) [16]. Poly(sodium-4-
styrenesulfonate)/poly(allylamine hydrochloride) multi-layered membranes that contained inter-layer
additions of antibiotic drug (metronidazole) were fabricated on synthetic biocompatible aminolysed poly(D,
L-lactide-co-glycolide) supports to be used as a controlled drug delivery system in the treatment of dental and
periodontal infections[17]. Alongside with polymers, biocompatible metals have been used widely in the
medical field, and may also need surface modification. For example, one study reports the coating ZEK100 (a
magnesium alloy), which is used for fixation of fractured bones, with alginate and chitosan; the alloy required
pre-layering treatment and a precursor layer to be suitable for the coating procedure [18]. Another widely used
biomedical material that has been successfully coated with polyethyleneimine/poly(sodium-4-
styrenesulfonate) multi-layers with a goal of controlling cellular adhesion is silicone rubber [19]. Additional
information about layer-by-layer coatings that are used in biomedical applications, including polyelectrolyte
data and further details about substrates described above is well presented in the article by Lvov [20].
Another area that benefits from the layer-by-layer coatings is optics. One study reports anti-reflective coatings
fabricated using alternating layers of silica nano-particles, poly(diallyldi-methylammoniumchloride) and
poly(sodium p-styrenesulfonate) on glass substrates [21]. Glass substrates have also been used for creating
light-emitting devices based on poly(allylamine hydrochloride)-evans blue/poly(acrylic acid) polyelectrolyte
pair [22]. Other application examples include microelectronics (with poly(dimethylsiloxane) elastomers [23]
as the most commonly used substrates), packaging (poly(lactic acid) substrates) [24] and fabrics (silk
substrates) [25].
1.1.2 Colloidal substrates
The layer-by-layer procedure is capable of multi-layering of not only flat surfaces but other substrate
geometries as well, including variously-shaped colloidal particles with different surface morphologies [1]
(hard templates), emulsions [26, 27, 28, 29, 30] and liposomes [31, 32] (soft templates). Such substrates
generally serve as templates for fabrication of multi-layered containers (capsules) that can be used for various
purposes, such as controlled drug delivery and release, extrinsic self-healing materials, separation systems and
other applications that might utilise encapsulated substances [33, 34].
1.1.2.1 Particles
One of the main requirements for the template particles in terms of the layer-by-layer methodology is their
stability in aqueous suspensions. When using stable templates, the possibility of multi-layering-induced
aggregation is decreased (especially during the deposition of the first polyelectrolyte layer – stable particles
are less likely to be coated as an aggregate), which provides uniformity of the fabricated polyelectrolyte
shells. Particles in any suspension are influenced by van der Waals forces which promote attractive
interactions that lead to aggregation, both reversible and irreversible, meaning that in the absence of any
opposite particle interactions within the system, the stability of the particles cannot be achieved. Such
opposite interactions can be introduced by charging the surface of the particles; if particles are charged, they
experience a repulsive electrostatic inter-particle force which prevents them from coming into contact [35].
Since another crucial requirement for particles as a part of the electrostatic layer-by-layer process is the
presence of charge on their surface, charge-induced stabilisation strategies are considered to be of a high
importance.
Colloidal particles immersed in a liquid can obtain surface charge via four general mechanisms [35, 36]:
1) Dissolution of Constituent Ions
In cases when solids have limited solubility in water one of the ionic species that the solid is composed of has
a greater probability of migrating into the liquid phase. Such unequal dissolution creates the excess of
counter-ions on the surface of the solid particles which results in their either negative or positive surface
charge. The most known example of solids that are susceptible to partial dissolution is silver iodide. It has
very low solubility in water (10-16 mol∙L-1 at room temperature [36]) with silver ions Ag+ having a greater
tendency to move into aqueous phase than iodide I -, resulting in negatively charged particles. Surface charge
can be manipulated by changing the relative concentrations of ions by adding, for example, either AgNO3 or
NaI, which makes it is possible to manipulate the surface charge and make it positive in the case of AgNO3.
On the transition from a negative to a positive charge, another surface condition can be achieved, which is
called the point of zero charge (pzc), where the net surface charge of the particles is zero. The point of zero
charge is generally achieved when the excess concentration of certain ions (in the current example, Ag+) in
solution mitigates their tendency to migrate from the solid surface into water thus creating a balance that
results in the zero net surface charge.
2) Ionisation of Surface Groups
Particles that have acidic or basic surface groups can release or acquire protons (H+) as a result of the change
in the pH of the medium solution. Surface charge, in this case, is induced by the ionisation of such surface
groups.
Two important examples of surfaces that can be charged by manipulating of the pH are biological surfaces
(usually contain surface proteins that consist of carboxylic (COOH) and amine (NH2) groups, Table 1) and
metal oxides (which produce ionizable amphoteric surface groups when exposed to water, Tables 2 and 3).
Table 1 – Biological surfaces – examples of conditions for ionisation of surface groups
Low pH No dissociation of COOH groups, surface remains uncharged;
NH2 groups are protonated, surface acquires positive charge.
Characteristic pH Point of zero charge, the number of dissociated COOH groups is in balance with the number of
protonated NH2 groups (balance depends on the number and type of surface groups; for most
biological surfaces at pH 4-5 [36]).
High pH No dissociation of NH2 groups, surface remains uncharged;
COOH groups are protonated, surface acquires negative charge.
Table 2 – Metallic oxide surfaces – examples of conditions for ionisation of surface groups
Low pH M-OH2+, positive surface charge;
pH < 5.8 Ti-OH + H+ → Ti-OH2+
Characteristic pH MOH, point of zero charge (isoelectric point);
depends on the crystalline form of oxide, origin, preparation, impurities; a rough guide for some
widely used materials can be found in Table 3.
High pH M-O-, negative surface charge;
pH > 5.8 Ti-OH + OH- → Ti-O- + H2O
Table 3 – The point of zero charge as a function of pH for common metal oxides [37].
Oxide SiO2 TiO2 Fe2O3 Al2O3 MgO
pzc 2 6 8 9 12
It should be noted that not only surfaces that contain two types of surface groups can change their ionisation
degree; one surface group can also undergo ionisation change resulting in a stronger or weaker surface charge
but with no charge reversal. The trend of the surface becoming less negative with a decrease of the pH stays
the same.
3) Isomorphous substitution
A process when one atom substitutes another in the crystal structure without a significant structural change is
called isomorphous substitution. For such substitution to happen, the participating atoms should have similar
ionic radii and valence state [38]. Most known materials that undergo this process are clays. Kaolinite, for
example, consists of alternating layers of tetrahedral silica and octahedral alumina which share apical
oxygens; bilayers are bound together by van der Waals forces and hydrogen bonding. When Si4+ gets
substituted by Al3+ the lattice acquires a residual negative charge. Much like metal oxides, the same negatively
charged kaolinite particles can acquire a positive charge at low pH conditions; as a result, the combined effect
of a positive charge and negative faces charge can result in edge-to-face aggregation of particles [36].
4) Ion adsorption
In cases when particles do not have any ionisable surface groups (2) and cannot be ionised in their bulk form
(1) their surface can be charged by adsorption of ionic species from the medium solution. Adsorption of ions
onto neutral surfaces must involve other interactions favourable to electrostatic interactions and is called
specific adsorption [36]. The most well-known example of this charging mechanism is an adsorption of an
ionic surfactant. Surfactants consist of a hydrophilic head, which is ionisable, and a hydrophobic tail which
attaches to the surface of the particle to minimise its contact with water. This results in either negative or
positive surface charge provided by the hydrophilic heads “floating” around the particle. A well-known
example where ion adsorption-induced surface charge is utilised are inks where mixtures of surfactants are
used as dispersants; carbon black, for instance, can be easily suspended in water if treated with anionic
surfactant [35].
When charged and placed into water, particles acquire a two-layered charge structure: an electric double layer,
also referred to as the “Stern layer”, and a “diffuse layer” of weakly associated ions (Figure 11). The potential
of the surface layer (e.g. of the particle itself) is defined by potential-determining ions, species which by virtue
of their electron distribution between the solid and liquid phase determine the difference in potential between
these phases (IUPAC). Examples of such ions include the aforementioned Ag+ and I- ions (1) since surface
charge changes on addition of either ion type; as for materials with ionisable groups, protons strictly speaking
cannot be considered potential-determining ions from the thermodynamic point of view, however, they do
show the change of the surface charge with a change of pH [36].
1.1.2.1.1 Examples of commonly used template particles
Depending on the application, core particles might be used for the production of non-loaded hollow capsules
where they are used without any treatment and removed on completion of the layer-by-layer procedure to
produce capsule shells for post-loading [39, 40, 41, 42] or may serve as a cargo loading base where substance
of interest (both molecules and nanoparticles [43]) is attached to the sacrificial or non-sacrificial particle
before being encapsulated (for example, porous particles provide high loading efficiency) [44, 45, 46, 47, 48].
Some of the most used template particles and their layer-by-layer relevant characteristics are presented in
Table 4.
Table 4 – Common colloid layer-by-layer templates
ParticleSize, µm
General polydispersity
Surface charge Solvent required to remove core
Non-porousPolystyrene
0.1 – 5 [43]Monodisperse
[49]
Negative [50, 51]
Tetrahydrofuran [43, 50, 52]
Melamine formaldehyde
Positive [40, 53]
Hydrochloric acid [40, 53], generally can be decomposed under
acidic conditions [43]Silica Negative [39,
54, 55]Hydrofluoric acid [39, 43, 49]
Gold nanoparticles
0.01-0.04 [56, 57, 58, 59]
Monodisperse [56, 57, 58, 59]
Negative [56, 57, 58, 59]
Potassium cyanide solution [56, 57, 58, 59]
PorousMesoporous silica
Available in both micro and nano-range [60];
≤0.2 µm desirable sizes for medical
applications [61], all other applications utilize 1-5µm [60]
Moderately polydisperse and
monodisperse [60]
Negative [61] Hydrofluoric acid [39, 43, 49]
Calcium carbonate
3-5 [62, 63, 64, 65, 66], 0.4-0.9 [67]
Polydisperse [49]Negative [62,
65]Ethylenediaminetetraacetic acid
[62, 65, 66]
1.1.2.2 Emulsions
Emulsions, which are dispersions of one liquid immiscible in a second liquid continuous phase, can also be
used as templates for the electrostatic layer-by-layer procedure. These systems can be classified by their type
(oil-in-water and water-in-oil) and size as micro-emulsions (< 100 nm), mini-emulsions, or nano-emulsions
(100 nm – 1 µm) and macro-emulsions (>1 µm), although the size classification is very general. A more
rigorous way to classify emulsions is with regard to their thermodynamic stability using the following
equation:
∆ G form=∆ A γ12−T ∆ Sconf (1)
where ∆Gform is the associated free energy of droplet formation, ∆A is a change in the interfacial area, γ12 is the
interfacial tension between phases 1 and 2 at the temperature T, and ∆Sconf is the configurational entropy
change which can be approximated as
∆ Sconf=−nk b∙[ ln (φ)+{(1−φ )
φ}∙ ln(1−φ)] (2)
where n is the number of droplets, kb is the Boltzmann constant, φ is the volume fraction of the dispersed
phase.
Micro-emulsions are formed when ∆Gform is negative – this means they are thermodynamically stable and form
spontaneously (in conditions of low interfacial tension, ∆Sconf > ∆Aγ12). If the value ∆Gform is positive (∆Sconf <<
∆Aγ12), meaning that emulsions are not formed spontaneously and work is required, emulsions are not
thermodynamically stable. This applies to macro-emulsions.
In mini-emulsions ∆Sconf < ∆Aγ12 resulting in still positive ∆Gform, however, those two values are much closer in
magnitude than in the case of macro-emulsions [35].
To act as layer-by-layer templates, much like particles, emulsions must be stable (e.g. droplet coalescence
must be minimised) and have a surface charge. Stability of emulsions can be achieved by increasing
electrostatic or steric (or a combination of both) repulsions to counteract van der Waals forces; for the same
reasons, as for particles, electrostatic stabilisation is more applicable and therefore will be discussed below.
Only oil-in-water emulsions are considered since the electrostatic layer-by-layer is a water solution based
process.
Electrostatic repulsion can be introduced by adsorption of an ionic surfactant onto surfaces of droplets [68].
Surfactant heads assemble at the interface and produce a surface charge that leads to the formation of an
electric double layer (essentially, the same structure is formed as in particle-in-water case) on the droplets;
when these droplets approach one another the overlap of the formed double layers creates a mutual repulsion.
The droplet of any liquid phase immiscible in water and stabilised by an ionic surfactant can be used as a
template for the layer-by-layer procedure. Some of the most used ionic surfactants when producing liquid core
layer-by-layer structures are anionic sodium docusate salt (AOT) [69, 70] and sodium dodecyl sulfate [28, 71,
72], cationic dioctadecyldimethylammonium bromide (DODAB) [29]. Other suitable ionic surfactants are
presented in Table 5 [73].
Table 5 – Commonly used ionic surfactants
Anionic (1) carboxylates: alkyl carboxylates-fatty acid salts; carboxylate fluoro-surfactants;(2) sulfates: alkyl sulfates (sodium lauryl sulfate); alkyl ether sulfates (sodium laureth sulfate);(3) sulfonates: docusates (dioctyl sodium sulfosuccinate); alkyl benzene sulfonates;(4) phosphate esters: alkyl aryl ether phosphates; alkyl ether phosphates.
Zwitterionic (amphoteric, charge depends on pH)
(1) RN+H2CH2COO-;(2) RN+(CH3)2CH2CHSO3
-;(3) Phospholipids: Phosphatidylcholine (Lecithin) [74].
Cationic (1) RN+H3Cl- (salt of a long-chain amine);(2) RN+(CH3)3Cl- (quaternary ammonium chloride – quats);(3) Ester – quats;Benzyldimethylhexade cylammonium chloride [34].
Once emulsified with an appropriate surfactant, emulsion droplets can serve as templates for the layer-by-
layer procedure which is to be started with a polyelectrolyte of the opposite to the selected surfactant charge.
1.1.2.3 Liposomes
Artificial spherical vesicles with an aqueous core embedded into one or multiple phospholipid bilayers or
lamellae are called liposomes [75]. Phospholipids are the main construction components for the outer part of
liposomes called the membrane. Another important element of the structure is cholesterol which acts as an
additive and fills up empty spaces between the phospholipids in the membrane. Cholesterol promotes a
stronger bond of the bilayer enhancing its stability. Liposomes can be prepared in different sizes (0.025 – 2.5
µm [76]), can contain a different number of bilayers and can be either charged (anionic or cationic) or neutral.
Other classifications available based on functionality – liposomes are classified as conventional, stealth,
ligand-targeted, long-release, triggered-release, most of which are properties relevant to drug-delivery
applications [75].
Liposome charge and stability are the most important characteristics in the scope of the layer-by-layer
process, the same as for particles and emulsions. Stability of liposomes is a complex phenomenon consisting
of physical, chemical and biological aspects. Physical stability is of the most practical interest since it largely
defines liposome shelf-live; processes such as aggregation and coalescence that are common for all colloidal
systems affect liposomes as well. Aggregation in liposomes, although in most cases reversible, can lead to
their irreversible coalescence, therefore, increasing their size, which normally is an undesirable outcome [77].
Liposome stability can be enhanced in the same ways as for all other colloids – by the introduction of either
steric or electrostatic repulsion. As in the case of particles and emulsions, electrostatic stabilisation of
liposomes is desired if they are to be used as the layer-by-layer templates.
Different types of liposomes can be prepared using a variety of conventional and novel methods [75]. For
example, both neutral and charged liposomes of the same size distribution can be fabricated by using the
traditional solvent injection method that involves dissolving the constructive phospholipids in an organic
solvent (most commonly ethanol or ether) followed by injection of the resulting mixture into an aqueous
buffer which results in spontaneous formation of vesicles [75, 78]. Depending on the charge of the lipids used
for fabrication, liposomes of corresponding surface charge can be produced. Examples can be found in Table
6 (reproduced from [78] with permission by Attribution 4.0 International (CC BY 4.0) licence), where PC is
soybean phosphatidylcholine, Chol is cholesterol, CHEMS-PEG is a PEGylated cholesterol derivative,
CHEMS is cholesterol hemisuccinate (anionic) and Chol-NH2 is N1-cholesteryloxycarbonyl-1, 2-
diaminoethane (cationic).
Table 6 – Fabrication of liposomes and corresponding characteristics
Formulation Molecular ratio Particle size, nm Zeta potential, mV
PC/Chol/CHEMS-PEG 40/17/3 249.3 ± 12.3 -9.6 ± 0.4 (neutral)
PC/Chol/CHEMS/CHEMS-PEG 40/8.5/8.5/3 275.3 ± 10.6 -31.2 ± 0.9 (anionic)
PC/Chol/Chol-NH2/CHEMS-PEG 40/8.5/8.5/3 271.6 ± 13.8 39.6 ±1.2 (cationic)
1.2 Polyelectrolytes
Polymers that contain ionisable groups along their chain structures that can dissociate in polar solvents (most
commonly water) into charged chains, macroions and small counterions are called polyelectrolytes [79]. A
schematic representation of the structure acquired by polyelectrolytes in solution is shown in Figure 3.
Figure 3 – Schematic representation of a polyelectrolyte in solution
In the electrostatic layer-by-layer procedure these materials represent fundamental construction elements
along with substrates of choice (flat surfaces, particles, emulsion droplets etc.) which are used for the
fabrication of multi-layered films/shells on the selected template. To understand interactions between
templates and polyelectrolytes, as well as polyelectrolyte-polyelectrolyte interactions that allow for the
formation of multi-layered structures, classifications and properties of these polymers should be discussed,
being fundamentals for all underlying layer-by-layer mechanisms.
Polyelectrolytes can be classified by two primary functional attributes: dissociation degree (the fraction of an
original number of polyelectrolyte molecules dissociated once placed in a solvent) and nature of the
counterions produced into solution [80]. A simplified classification diagram is presented in Figure 4.
Figure 4 – Classification of polyelectrolytes
Polyelectrolytes can be also classified based on positions of their functional groups into integral and pendant
types (Figure 5).
Figure 5 – Classification of polyelectrolytes (from left to right): integral type polycation, pendant type
polyanion, integral type polyampholyte.
The specific character of the interactions of the macro-ion with counter-ions in polyelectrolyte solutions is one
of the defining aspects of these materials that differentiate them from simple electrolytes. One of the methods
used for the assessment of ion activity within polyelectrolyte solutions is potentiometry, which allows not
only for the determination of the number of functional groups but also gains the acidity constants that are
directly related to the degree of dissociation (an indicator of polyelectrolyte strength). Potentiometry is usually
carried out in form of titrations accompanied by measurements of H+-ions activity as a function of pH change
using a reference electrode. Polyacids may be titrated with hydroxides, polybases – with acids.
Polyelectrolytes dissociate differently from non-polymer materials, which can be illustrated by an example
comparison of a weak acid and a weak polyacid dissociation during potentiometric titrations [80].
For a weak acid HA, the dissociation constant Ka can be defined as follows:
K a=¿¿ (3)
where [H+], [A-] and [HA] are concentrations of [H+], [A-] and HA respectively.
This expression can be transformed into a more practically used value pKa as
pK a=−log10 K a=pH−log10 ¿¿¿ (4)
By introducing the degree of neutralisation of acid by a titrant α 'which is directly related to [A-], pKa can be
calculated using Henderson-Hasselbalch equation:
pK a=pH + log10(1−α')
α ' (5)
Let us now consider the ionisation equilibrium in a solution of a weak polyacid which has N ionisable groups
per macromolecule. If each monomer contains one ionisable group, then N is also equal to the degree of
polymerisation; the dissociation degree of such a system is strictly speaking defined by N different
dissociation constants. When a titration is performed on such materials the increase in the neutralisation
degree results in an increase of the charge density on the polymer chain producing an additional electrostatic
attraction that affects yet non-detached counter-ions; pKa values of different functional groups change during
the process of titration [81]. This additional attraction results in a necessity of an additional work ∆Gel to
detach a proton from a polymer chain, which is defined as
∆ Gel=N A eψ (6)
where NA is the Avogadro constant, e is the elementary charge, and ψ is the electrostatic potential on the
surface of the polyelectrolyte.
The degree of dissociation α for polyelectrolyte can be calculated from the degree of neutralization
α=α'+CH +¿
CPE¿ (7)
where CH+¿¿ is a molar concentration of H+ ions and CPE is a molar concentration of the polyelectrolyte
segments.
Taking into account the extra work for ion separation and a newly-defined degree of dissociation α we can
relate the apparent acidity constant p Kapp(PE ) to the intrinsic acidity constant p Ka0
p Kapp(PE )=p Ka0+0.4343
∆ Gel
RT (8)
which can be found from the correlation with the potentiometric pH so that the Henderson-Hasselbalch
equation becomes
pH=p Ka0− log10
(1−α)α
+0.4343∆ Gel
RT
(9)
Experimentally p Kapp(PE ) can be found by performing titrations and plotting the differential curve in
coordinates of ∆ pH as a function of titrant concentration (per unit of polyelectrolyte mass), where ∆ pH is
the change of pH per addition of unit of titrant. The maximum on the resulting curve corresponds to the
concentration of the functional groups (equivalent point, Figure 6a). After the titration curve is obtained the
degree of neutralization a ' of each point on the curve is calculated and a pH=f ( log10a'
(1−a')) curve is
constructed which allows for determination of p Kapp(PE ) at half-neutralisation (α '=0.5) using a modified
Henderson-Hasselbalch equation:
p Kapp(PE )=pH−m ∙ log10α '
(1−α' ) (10)
where m can be found as a slope of the aforementioned curve and is a characteristic for electrostatic
interactions between polyelectrolyte functional groups (Figure 6b). The maximum acidity of the polycation or
maximum basicity of polyanion is achieved at α '=0, correspondingly both are a minimum at α ' → 1. Half-
neutralisation point of α '=0.5 is significant because it allows for the determination of an intrinsic intrinsic
p Ka0 value under conditions where the electrostatic interaction of the polymer chain and counterions is
screened by the presence of low molecular salts [80]: m∙ log10α '
( 1−α ' )=0, meaning p Ka
0=pH (α¿¿ '=0.5)¿.
All these differences between the dissociation behaviour of low molecular acids and polyacids can be clearly
seen from their titration curves (Figure 6c). It can be observed that polyacid behaves as a weaker acid in
comparison to its low molecular analogue, even though they consist of the same ionisable groups. Due to the
increasing electrostatic chain-counter-ion interaction that accompanies dissociation of a polyacid, it behaves
as a weaker acid. If a low molecular weight electrolyte is added to the polyacid solution, its ions screen the
charge of a chain and the titration curve becomes more like that of a low-molecular acid.
(a) (b) (c)
Figure 6 – Potentiometric titration curves [81]
The behaviour of polyelectrolytes in solutions is most often explained in terms of “Counterion Binding
Theory” of Manning [82]. The main concept of this theory is that there is a certain critical value of charge
density that can exist on the polyelectrolyte chain that, if exceeded, leads to condensation of counter-ions onto
the chain in order to lower its charge. In this theory, the polyelectrolyte is simplified to a form of an infinitely
long chain which has uniformly-spread charges attached to it (each charge is separated from another by the
length b). The characteristic dimensionless value for linear charge density of such polyelectrolyte chain ε is
then defined as
ε= q2
ϵ kbTb (11)
where q is the protonic charge, ϵ is the dielectric constant of a solvent, k b is Boltzmann’s constant, T is the
temperature, b is the average linear charge (univalent groups) spacing.
The theory postulates that ε cannot be greater than 1; if ε>1 a fraction of counterions electrostatically
“condense” onto the chain to lower its charge density to a maximum value ε=1. Other counterions generate
an “counterion atmosphere” around the polyelectrolyte chain that behaves according to Debye–Hückel theory
(which in simplified form states that each ion in solution polarises its environment and creates an “cloud” of
oppositely-charged ions around it) [82]. The mechanisms of such “condensation” and an overall applicability
of this theory is still debated, although it is considered to be a main polyelectrolyte solutions theory.
Another widely accepted theory of polyelectrolyte behaviour in solutions is based on so-called “electrostatic
blob” model [83] built around polymer scaling theory. It suggests that a weakly charged polyelectrolyte chain
can be presented in a form of chain of electrostatic blobs (Figure 7) of a size defined as
ε el a(f 2 lb
a)−1
3 (12)
where a is a size of a monomer, f is a fraction of charged monomers within polyelectrolyte chain,
lb=e2
4 πϵ kb T is the Bjerrum length (the separation distance at which the electrostatic interaction between two
elementary charges is comparable to the thermal energy scale kBT; e is the elementary charge, ϵ is the
dielectric constant of water).
Figure 7 – Electrostatic blob model
Each blob contains gel ( f 2lb
a )−23 monomers, and the length R of the resulting chain containing N monomers
in absence of added salt can be expressed [84] as
R Na( 1a )
13 ( ln N
3)
13
(13)
In the presence of added salt, the chain becomes less elongated due to the screening of polyelectrolyte charge
by the salt ions; the screening effect can be characterised by the Debye screening length
κ−1=(8 πnlb)−12 (14)
If this screening length is smaller than the size of a chain, the chain becomes less elongated which leads to
bending; the influence of this effect is addressed in terms of a persistent length lp, which is a length of a chain
over which it remains in a stretched geometry [83]. This parameter is theorised to decrease with salt
concentration as a function of κ−1or κ−2 in different theories; at very high added salt concentrations the
electrostatic interaction within polyelectrolyte chain becomes short-range.
In the case of more concentrated solutions, the blob model predicts strong chain-chain interactions and their
overlap, which allows treating such solution as a disordered and isotropic liquid with a presence of local chain
order as shown in Figure 7.
Other theories include the extended “Scaling Theory” by A. Dobrynin [85] and Poisson-Boltzmann approach
by M. Fuoss [86].
1.2.1 Examples of commonly used polyelectrolytes
As previously mentioned, polyelectrolytes can be classified into polyacids, polybases, polyampholytes and
polysalts. Another classification can be introduced by derivation origins – natural and synthetic. Some of the
examples of the polyelectrolytes of aforementioned classifications that has been used as construction materials
for the electrostatic layer-by-layer multilayering (on spherical templates) are presented in Table 7.
Table 7 – Common polyelectrolytes used for the electrostatic layer-by-layer assembly
CationicAbbreviation Origins
Poly(allylamine hydrochloride) [39, 42, 87, 88] PAH
Synthetic
Poly(diallyldimethylammonium chloride) [34, 42, 52, 89, 90, 69] PDADMAC
Poly(vinyl benzyl tri-methylammonium chloride) [91] PVBTAC
Poly(N-ethyl-4-vinylpyridinium bromide) [92] PEVP
Poly-L-lysine [52, 93, 94, 95] (originates from amino acid precursor) PLL
Poly-L-arginine [96, 97, 98] (originates from amino acid precursor) -
Chitosan [46, 99, 100] - Natural
AnionicPoly(sodium 4-styrenesulfonate) [39, 90, 69, 98, 101] PSS
SyntheticPoly(acrylic acid) [45, 102] PAA
Poly(vinyl sulfate) [103, 104, 105] PVS
Poly(vinylsulfonic acid) [106] PVSA
Carrageenan [52, 107] -
NaturalCarboxymethyl cellulose [88] CMC
Hyaluronic acid [46, 87, 93, 108] HA
Alginic acid (sodium alginate) [69, 109, 110, 111] AA
2. Underlying mechanisms of the electrostatic layer-by-layer assembly
The layer-by-layer assembly is a procedure that involves three distinct stages: adsorption of a polyelectrolyte
onto a substrate (polyelectrolyte at interface, first layer formation), adsorption of a second polyelectrolyte
layer (formation of the polyelectrolyte complex) and multi-layering (fabrication of more than two layers).
Each of these stages has unique underlying mechanisms and specifics which are discussed in the section
below.
2.1 Adsorption of polyelectrolyte onto a solid surface (polyelectrolyte at interface)
Let us consider a solid surface that possesses an electric charge eσ per unit area. This charge creates an
electric field closely around this surface which can be expressed as [83]
E=(kb T
e)(4 πσ lb) (15)
where lb is the Bjerrum length.
The electric field decays with the distance from the surface due to the screening effects induced by counter-
ions or by added salt ions if those are present [83]. If the decay trend is only influenced by counterions, which
exist in a proximity to the surface λ=1
2 πσ lb , the field can be defined by the following expression
E≅ 2z+ λ (16)
where z is any given distance from the surface.
In presence of the added salt, screening is mostly due to the added salt ions and the field decays as
E≅ 2λ
exp−κ z (17)
Polyelectrolyte chains in solutions of low added salt concentration, i.e. in conditions of low ionic strength,
adsorb onto the surface of the opposite charge due to electrostatic attraction; the condition for the
polyelectrolyte to be confined at the distance δ from the surface is the sufficient enough surface charge that is
able to move polyelectrolyte chain to a distance δ < λ. The relation between δ, polyelectrolyte properties and
the electrostatic force can be expressed as
δ ( a2
fσ lb)
13 (18)
By adding more salt into such solutions polyelectrolyte adsorption structure does not change unless δ, which
can be also described as the chain thickness, is larger than the Debye screening length. Once this condition is
no longer in place and if there is no short-range non-electrostatic interaction between the polyelectrolyte and
the surface, the chain desorbs [83].
Besides this general principle, adsorption of polyelectrolytes onto solid surfaces has a range of properties and
characteristic aspects that are important in terms of the electrostatic layer-by-layer assembly.
2.2 The nature of the adsorption process
Firstly, the nature of the polyelectrolyte adsorption process is essentially irreversible regardless of the
geometry of the selected substrate [112]. The process of adsorption includes two stages: at the first stage the
mass of the adsorbed polyelectrolyte increases linearly with time (indicating the rapid character of
adsorption), while the second stage is represented by a plateau indicating the saturation point at which no
more polyelectrolyte can be adsorbed to the surface even if some of it is still present in solution. Many studies
report that once coated, both flat [112, 113, 114, 115, 116] and particulate [112, 117, 118] substrates, if then
exposed to a polyelectrolyte-free solution containing low-molecular electrolytes, do not experience any
desorption which is evidence of the irreversibility of the adsorption process. There are, however, minor
exceptions from this behaviour – several studies have reported partial desorption of low molecular weight
polyelectrolytes; some high molecular weight polyelectrolytes have also been reported to desorb, however, the
desorption was induced by additional changes introduced in polyelectrolyte solutions =[112]=[112].
The polyelectrolyte adsorption process is most commonly described in terms of classical Random Sequential
Adsorption (RSA) model. This model is used for the explanation of adsorption of colloidal particles, proteins
and polyelectrolytes where all of these systems are modelled as circular disks that can adsorb to surfaces at
random empty locations with no permitted deposition overlap [112]. Taking these conditions into account, the
maximum achievable coverage (jamming limit) can only be θj ≅ 0.55 which is less than the regular hexagonal
packing (0.91). In relation to the number density of polyelectrolyte molecules Г, the surface coverage can be
expressed as
θ=π a2 Г (19)
where a is the radius of gyration of the polyelectrolyte.
The adsorption process can be approximated kinetically as
d Гdt
=ka cB(Г )
(20)
where d Гdt is the change of the adsorbed number density with time, ka is the polyelectrolyte adsorption rate
constant, c is the number concentration of the polyelectrolyte molecules in solution and B(Г) the so-called
blocking function that describes the available surface area
( Г )={1−ГГ 0
, for Г <Г0
0 , for Г ≥ Г 0
(21)
where Г0 is the adsorbed number density at saturation point (at the jamming limit) [112].
2.3 Characteristic phenomena of the polyelectrolyte adsorption process
The main properties of the adsorbed polyelectrolyte layer are the adsorbed mass, the morphology and the
distribution of charge (surface charge reversal upon the adsorption event). These properties and the conditions
that stipulate them are discussed below.
The adsorbed mass is the amount of the polyelectrolyte that is adsorbed onto a substrate surface while under
the influence of various parameters which include characteristics of the polyelectrolyte (for example,
molecular weight), the substrate (charge density) and the composition of adsorption medium solution
(concentration of added low-molecular weight electrolyte). General trends for the dependency of the
aforementioned factors on the adsorbed mass are summarised in Table 8 below.
Table 8 – Factors defining the adsorbed polyelectrolyte mass
Component Characteristic Influence on the adsorbed mass
Polyelectrolyte Molecular weight [112](at saturation conditions)
Linear polyelectrolytes: weak adsorbed mass – molecular weight dependency, can be described in terms of the RSA model asГ∝M−2 α f (22)where Г is the number density of polyelectrolyte molecules, M is the molecular mass, α f is the Flory exponent in the range 0.5-0.6.
Dendric or branched polyelectrolytes: stronger dependency due to α f being smaller in comparison to one of linear polyelectrolytes (the adsorbed mass increases with the increase of molecular weight)
Charge density [112, 114]
The adsorbed mass increases with the decrease of the charge density (the maximum of the mass can be achieved at very low charge densities). In the absence of the added salt, polyelectrolyte-polyelectrolyte repulsion is long-ranged and affects the coverage of the substrate (less material is needed to saturate the surface).This calls for modification of the RSA model as follows:1 – repulsion between electric double layer polyelectrolyte coils can be accounted by increasing the radius of the “disk” to an “effective radius” aeff
2 – modified surface coverage θ=θ j(aa eff
)2
3 – the interactions between two polyelectrolyte coils are expressed as
u (r )=kb T lb Zeff (eκ a
1+κ a)
2 e−κ r
r (23)
with r being the distance between centres of RSA “disks”
4 – the effective charge is given as Zeff=alb
(4 κ a+6), where lb is the
Bjerrum length and κ−1 is the Debye screening length
With an assumption that interaction energy between two polyelectrolyte coils would be in order of thermal energy u(2aeff )≅ kbT the “effective radius” can be estimated; analysis of the equation (23) in this case shows that the decrease of Zeff leads to the smaller aeff meaning a larger number of “disks”, i.e. polyelectrolyte mass is adsorbed.
Substrate Charge density [112, 116]
The adsorbed mass increases with the increase of the charge density.
This trend can be explained in terms of the modified RSA model proposed for polyelectrolytes above. Qualitatively, the higher the substrate charge density is the more counter-ions accumulated in the vicinity to the surface. A larger amount of surface counter-ions provides larger screening effects onto approaching polyelectrolyte chains resulting in the reduction of mutual repulsion, and, consequently, in the larger adsorbed mass.
Adsorption medium composition
Monovalent electrolyte concentration (added salt) [112, 116, 119, 120]
The adsorbed mass increases with the increase in added salt concentration. The 4-times increase in salt concentration results in 2 to 4 times increase in mass uptake.
The trend of the increasing adsorbed mass, in this case, can be understood using the same modified RSA model described above (polyelectrolyte charge density section). To recap briefly, since polyelectrolyte coils in aqueous solutions obtain electric double layer structure around them they repel each other increasing the aeff “disk” radius resulting in smaller adsorbed mass. However, introduction of monovalent salt provides screening of the long-ranged repulsion resulting in aeff decrease and higher mass uptake.
The reverse trend is only observed for very weak polyelectrolytes and very high salt concentrations. RSA model is not able to predict adsorption maximum in such cases since strong screening will prevent weak polyelectrolytes from adsorption due to decreased electrostatic attraction becoming smaller than thermal motion. If there are no other forces present polyelectrolyte will not adsorb.
The morphology of the adsorbed polyelectrolyte films can be generally described as laterally heterogeneous,
meaning that polyelectrolyte chains adsorb onto the surface individually. This morphology type can be
confirmed both theoretically, in terms of RSA model, and experimentally by using various techniques; among
others, Atomic Force Microscopy (AFM) provides the most conclusive evidence for the formation of the
aforementioned type of structure.
The RSA model described in the current section and Table 8 suggests [112] that polyelectrolyte chains adsorb
onto the substrate one by one at certain separation distances defined by the mutual electrostatic repulsion. The
chains are also flattened by strong attractive forces between the polyelectrolyte and the substrate, which leads
to the formation of very thin films (just a few nm [119, 120] thick while the typical diameter of a
polyelectrolyte chain is 20-100 nm). One of the factors that have an affect on both thickness and
morphological features of the adsorbed films is, as in the case with the adsorbed mass, the presence of added
salt in the adsorption medium. The thickness of the polyelectrolyte films depends on the added salt
concentration in the same way as the adsorbed mass does – it increases as more salt is added into solution
(adsorbed mass behaviour reasoning applies). High salt concentrations lead to the formation of swollen and
porous films [112].
Experimental AFM images supporting theoretical laterally heterogeneous morphology of polyelectrolyte films
are presented in Figure 8. It can be observed that even though the adsorbed layers are saturated, well-defined
polyelectrolyte chains are separated by an unoccupied space which is not and will not be filled in due to the
repulsive forces between the chains.
Figure 8 – AFM images of saturated polyelectrolyte layers of (a) - dendritic PAMAM layered on mica at
pH 4.0 with no added salt; (b) -- PSS layered on amidine latex particles in solution containing 1 mM
monovalent electrolyte [112] – Published by The Royal Society of Chemistry.
The process of adsorption of the polyelectrolyte onto the oppositely charged substrate is characterised by the
reversal of charge on the surface of the substrate. This process, which is also referred to as overcharging,
occurs in a “build-up” regime, meaning that at low polyelectrolyte concentrations the substrate keeps it charge
sign despite partial polyelectrolyte adsorption; the surface potential, however, decreases until a certain amount
of polyelectrolyte is adsorbed that compensates the substrate charge leading to surface neutralisation; if more
polyelectrolyte is added, the accumulation of polyelectrolyte-induced charge (opposite to one of the substrate)
continues until the saturation point is reached. In this regard, the adsorption process can produce unsaturated
films where all of the available polyelectrolyte chains are adsorbed onto the surface, but the saturation point is
not reached, or it can produce saturated films where even in the presence of excess polyelectrolyte no more
chains can be attached to the surface. The overcharging process can be theoretically described using the linear
superposition relationship model [118]
σ=σ 0+q Zeff Г (24)
where σ is the resulting charge density, σ 0 is the surface charge density of the bare substrate, Zeff is the
polyelectrolyte effective charge and Г is the number density of polyelectrolyte molecules.
The charge reversal process is observed both experimentally [121] and theoretically [112] in Figure 9. It can
be seen that the linear superposition relationship provides a good fit for experimental data.
Figure 9 – Overcharging process (a) deposition of PSS onto latex particles as measured by electrophoresis
and AFM (b) calculations based on linear superposition relationship model [112]. – Published by The
Royal Society of Chemistry.
It should be noted that neutralisation point can be achieved stoichiometrically, i.e. when polyelectrolyte
neutralises the substrate charge exactly, and super-stoichiometrically where polyelectrolyte counterions
significantly participate in the charge balance. The latter is characteristic to weakly charged polyelectrolytes
[112]; a higher dose of such polyelectrolyte is required to neutralise a given surface [112, 122]. The opposite
of that is also true – less given polyelectrolyte is needed to neutralise a surface with a smaller charge [112,
123].
The charge density profiles of the surface with an adsorbed polyelectrolyte layer in comparison to the bare
charged surface are presented in Figure 10. This surface charge density can be approximated using the Gouy-
Chapman relationship
σ=2 kbTϵ ϵ 0 κ
esinh (
q ψD
2k bT) (25)
where ψ D the potential of the diffuse layer (the layer of weakly associated ions around the surface), e is the
elementary charge, ϵ is the dielectric constant of the liquid.
The presented profiles indicate that the surface with an adsorbed saturated polyelectrolyte layer behaves much
like a bare surface with the only difference in a charge sign. Both surfaces generate a diffuse layer of attracted
counter-ions and depleted co-ions [112].
Figure 10 – Charge density profiles (schematic) – (a) bare surface; (b) surface coated with polyelectrolyte
of the opposite charge [112]. – Published by The Royal Society of Chemistry.
The degree of surface saturation plays an important role in interactions between both bare and coated with
polyelectrolytes particles. These interactions define the stability of the particles in dispersions (i.e. their
resistance to aggregation) which is, as stated before, one of the fundamental requirements of the layer-by-layer
multi-layering. The stability of the particles in aqueous dispersions can be addressed in terms of a balance of
attractive and repulsive forces between the particles, which is a basis for DLVO theory (named after its
authors, Derjaguin and Landau, Verwey and Overbeek). This theory describes [124] colloidal stability as a
competition between attractive van der Waals force which depends on the distance r between the particles of
radius R as
U vdW (r )=−A12 π
( Rr
)2
(26)
where A is the Hamaker constant (depends on number densities of interacting particles) [125], and repulsive
electrostatic force which also depends on the distance r as
U E (r )=4 πεap
2+ rap
ψ02 e−κr
(27)
where ψ0 is an electric potential on the surface of the particle, ap is a diameter of the particle, κ is the Debye –
Hückel constant
κ=¿ (28)
where e is the elementary charge, n0i is the concentration of i-ions near the particle, zi is the valence of i-ions,
ε is the dielectric constant of a solvent. The inverse to Debye – Hückel constant is called the Debye length
(screening or decay length).
The resulting balanced particle interaction can be expressed as a sum of attractive and repulsive forces as
U=U vdW+U E (29)
The influence of the balance between the forces on the stability of the particles can be visualised if U is
plotted as a function of r. The electric double layer structure which charged particle obtains is aqueous
solutions is presented in Figure 11 (a) as well as the interactions of two such particles in terms of DLVO
theory (b).
Figure 11 – DLVO theory: (a) – dispersed particle in aqueous solution (Stern layer – a layer of strongly
electrostatically bound oppositely charged ions; slipping plane – the boundary between the diffuse layer (of
weakly associated ions) and the medium potential at which is measured to determine stability of dispersions
(ζ-potential)); (b) force balance interactions between particles as a function of interparticle distance.
As can be seen from the U(r) graph, there are three “potential zones” that characterise particles behaviour.
Zone I is the potential well where an attractive force is dominant, zone II is the barrier that prevents particles
from aggregation, zone III is also an attractive potential well. When particles migrate towards each other, they
go through these “zones” in the reverse order, III→II→I. The relative positions of particles (whether they stay
at the distance within III, II or I) can be determined using the following general rules (with 32
k bT being an
average thermal energy of the particle) [126]:
1) – max (U ¿¿ II)≫ 32
kb T ¿ and min|U III|≤32
kb T– particles have enough energy go beyond zone III
but are not able to overcome the barrier II – dispersion is stable;
2) – max (U ¿¿ II)< 32
kbT ¿ and min|U III|<32
kb T– particles have enough energy go beyond zone III
and to overcome the barrier II – dispersion aggregates;
3) – max (U ¿¿ II)≫ 32
kb T ¿ and |min U III|≪32
kb T– particles enter zone III and are not able to
escape it, which results in connected dispersions (an example for such systems is gels).
Let us now compare interaction forces and aggregation stability for two types of particles – with a saturated
and unsaturated layer of adsorbed polyelectrolyte. The comparison of the forces is presented in Table 9 below.
Table 9 – Forces within coated colloid particle dispersions
Particles with saturated polyelectrolyte layer Particles with unsaturated polyelectrolyte layerForces Behave in terms of DLVO theory; thin
and highly charged polyelectrolyte layer produces surfaces interactions which are dominated by electrostatic repulsion [112, 127, 128, 129] (much like between uncoated particles).
Deviations from DLVO theory may be observed at short distances and are attributed to steric repulsion [130, 131] (entropic effect due to conformational entropy of polymer chains), patch-charge attraction [118, 121] (driven by lateral heterogeneity of the adsorbed layer; charged patches obtain preferential orientations in proximity to oppositely charged patches [112]), polyelectrolyte bridging [127, 132] (adsorption of polyelectrolyte chains of one layered surface onto another closely-located surface at the event of enough proximity [112]). These forces have a relatively minor impact.
Particles with homogeneous unsaturated polyelectrolyte layers behave in terms of DLVO theory. Since ``unsaturated" layer means that adsorption process is stopped for analysis at some point of overcharging process, forces between particles can be categorised by stages: electrostatic repulsion at pre-neutralisation adsorption (decreasing with the increase in amount of adsorbed polyelectrolyte), van der Waals attraction at neutralisation point, and electrostatic repulsion beyond neutralisation (increasing until saturation point) [112].
Particles with heterogeneous unsaturated polyelectrolyte layers experience additional, non-DLVO forces (same as saturated layer particles, but more pronounce) the most influential being patch-charge attraction force. Interaction force equation, in this case, is expanded with an extra addend [112, 121](30) U =U vdW+U E+U pcThis force is stronger than van der Waals force of the same segment and is assumed to be exponential(31) U pc=−A e−eh
The origin of this force is, as has already been stated, lateral heterogeneity of the adsorbed layer that leads to preferential orientations of charged patches [112]. The decay length for this force can be expressed as [133]
(32) q−1=κ2+( 2 πb l
)2
where bl is the spacing in patch “lattice”, κ−1 is the Debye length. At low added salt concentrations the decay is driven by spacing, at high concentrations it is screened as an electrostatic force [112].
Theory predicts two aggregation regimes: the fast regime (diffusion controlled aggregation, typical for high
added salt concentration and small charge densities) and the slow regime (characteristic for systems with high
UII barrier (Figure 11): low added salt concentration or large charge densities). The transition point between
the slow and the fast regime is called “Critical Coagulation Concentration” or CCC. The rate of aggregation is
generally reported as the stability ratio [134]
W =k fast
k (33)
where kfast is the aggregation rate in the fast regime of the chosen reference system, k is the rate for the system
of interest.
The stability ratio increases with the slowdown of the aggregation process [112]. The comparison of the
aggregation behaviour of particles with a saturated and unsaturated layer of adsorbed polyelectrolyte is
presented in Table 10.
Table 10 – Aggregation behaviour of coated colloid particle dispersions
Particles with saturated polyelectrolyte layer Particles with unsaturated polyelectrolyte layer
Aggregation behaviour
Both fast and slow aggregation regimes are possible [112, 135].The fast regime is in place at high added salt concentrations, W =const≅ 1
In the slow regime W increases with the decrease in added salt concentration.
Saturated films typically have high charge density meaning that CCC point is shifted to higher salt concentrations.
Deviation from the behaviour described by DLVO, which predicts a stronger dependency of W with a salt concentration that it is in experiments, is most likely related [136] to lateral charge-patch attractions mentioned in Table 8 above.
Aggregation trend in particles with homogeneous unsaturated polyelectrolyte layers is in agreement with DLVO theory and forces described in Table 8 (main reason for the agreement being the homogeneity of the film). Dispersion is stable at low polyelectrolyte coverage (above neutralisation), followed by the decrease of the stability ratio on the way to neutralisation point where it reaches W =1beyond which dispersion is stable again. Deviation from experimental data is again observed in DLVO predictions at high salt levels possibly due to other non-DLVO contributions [112].
Aggregation of particles with heterogeneous unsaturated polyelectrolyte layers is influenced by the molecular mass of the adsorbed polyelectrolyte due to pronounce non-DLVO patch-charge interaction forces introduced by lateral heterogeneity. The larger is the molecular weight, the larger is the size of charge patches meaning that patch-charge attraction force becomes more long-range. The stability ratio decreases with the decrease of added salt concentration; this effect becomes quite major with a simultaneous increase in molecular weight [112].
2.4 Polyelectrolyte interactions and multilayering
2.4.1 Complexation of polyelectrolytes in solutions
When solutions of two oppositely charged polyelectrolytes are mixed poly-ions tend to form polyelectrolyte
complexes, which are dense phases that separate from the medium [83]. Formation of such complexes is
mainly driven by electrostatic interactions between polyelectrolyte chains; other interactions that can be
involved in this process include hydrogen bonding, van der Waals, hydrophobic and dipole interactions [80].
Polyelectrolyte-polyelectrolyte interactions in the absence of any other phase (particles, droplets), strictly
speaking, are not a part of the electrostatic layer-by-layer procedure on their own. The description of such
interactions, however, cannot be excluded, since, firstly, it is believed that polyelectrolytes within multi-layers
exhibit local behaviour identical to complexes formed by the same polyelectrolytes in bulk [137], and
secondly, in conditions of polyelectrolytes excess (which, in the conventional layer-by-layer procedure, can
happen as a result of incomplete washing steps) the fabrication of multi-layers on templates might be affected
by formation of polyelectrolyte complexes in solution.
Polyelectrolyte complexes can be generally divided into stoichiometric and non-stoichiometric depending on
the difference in molecular weights of the participating polymers.
Polyelectrolytes composed with weakly charged ionic groups and with a large difference in molecular
weights, if mixed in non-stoichiometric ratio, produce water-soluble sequential complexes with the structure
presented in Figure 12 (c) [80]. The “guest” polyelectrolyte, which in this structure is a short chain polymer
(with a much lower molecular weight), is able to migrate along the “host”, high molecular weight polymer
chain. The water-soluble character for these complexes is possible up to some critical guest/host concentration
ratio, which, when exceeded, leads to the formation of insoluble complexes co-existing with soluble ones
[80].
If polyelectrolytes with similar molecular weights are mixed the resulting complexes are generally
characterised by 1:1 stoichiometry and are formed as ladders (fixed ionic cross-links) or chaotic scrambled-
egg structures (Figure 12 (a) and (b)) [80].
Figure 12 – Stoichiometric (a and b) and non-stoichiometric (c) polyelectrolyte complexes
This classification approach, though phenomenologically correct, is rather simplified. Complexation of
polyelectrolytes in solutions can be described more comprehensively by using phase diagrams, which can
predict the formation of complexes of different shapes at different conditions (concentration ratios, added salt,
pH and others).
The simplest case of polyelectrolyte complexation diagrams is encountered when both participating polymers
have the same large molecular weights Mw, same fraction of charged groups f, and the same concentrations c.
Under these conditions, polyelectrolytes form dense complexes in water easily and their critical complex
formation concentrations are low [83]. Generally, when two polyelectrolyte solutions are mixed, there are two
possible outcomes: solution separates into two parts each containing one polyion species, or polyelectrolyte
complexes are formed. Polyelectrolyte mixture behaviour route is determined by the fraction of charged
groups in both polymers. When f is low, the interaction between polyelectrolytes becomes much like the
interaction between uncharged polymers and is dominated by low mixing entropy (order of 1/N where N is the
number of monomers per chain) which causes solution segregation. The parameter that is used to characterise
the degree of such repulsive polymer mismatch is called the Flory-Huggins parameter χ [138]; it is used in
the calculation of the free energy of complex formation (enthalpic), and generally, if positive, means that the
selected polymer pair is incompatible and will phase separate in solution [139]. When f is high
polyelectrolytes form complexes due to the attractive electrostatic interactions that dominate over entropic
chain repulsion [83]. The diagrams for both low and high f cases are presented in Figure 13.
Figure 13 – Typical phase diagrams for (a) low charge density polyelectrolyte solutions (b) high charge
density solutions. The thick lines indicate co-existing phases. Reproduced from [139] with permission of
Springer.
The concentration of monomers inside the polyelectrolyte complex is influenced by electrostatic interactions
as follows:
ccf 2
a2nw43 (1− f 2
n32 lb
12 a2 w
23 )∗¿
(34)
where a is the size of a monomer, n is the concentration of counterions, w is the calculational coefficient of
the order of monomer volume a3, lb is the Bjerrum length.
* This formula was derived in terms of the Random Phase Approximation (a generalisation of the Debye –
Hückel theory of strong electrolytes) and Mean Field Theory combined. Details for approximations and a full
list of equations can be found elsewhere [139].
More complex charge density-volume fraction polyelectrolyte complexation phase diagrams have been
developed by Oskolkov and Potemkin [140]. They show the formation of different types of complexes
between N linear flexible poly-ion molecules, where N=N +¿¿ (number of polycations) +N−¿¿ (number of
polyanions) and were built for systems with slight asymmetry of charge, meaning that all polyelectrolyte
molecules have the same length and same absolute charge density, but the number of charged chains in
polycation and polyanion molecules is different, N+¿>N−¿ ¿¿. This asymmetry of charge is represented as an
asymmetry parameter Aasexpressed as
Aas=N+¿− N−¿
N≪1¿
¿
(35)
Each molecule consists of m segments, each segment has the size aand a small fraction of charged groups
f =1σ
≪1. Counterions coming from polyelectrolyte chains themselves are treated as non-influential; the only
“excess” counterions are produced from N+¿−N−¿¿ ¿ symmetry [140].
Diagrams are built by equating the chemical potentials of the phases, μi (ф1 )=μ j ( ф2) and osmotic pressures
π i ( ф1)=π j (ф2 ) where i, j = polycation + globules, spheres, cylinders, lamellae and macrophase (precipitated
globules). Chemical potentials and osmotic pressures are calculated as
μi (ф )=∂ F i
∂ ф, π i (ф )=ф μ i ( ф)−Fi (36)
where F i is a free energy which is calculated by using different formulae for different diagram regions
(different phases) [140].
The resulting diagram is presented in Figure 14 and shows the regions of stability for various complexes. The
lined regions correspond to co-existence of the connected phases.
Figure 14 – Complexation phase diagrams for polyelectrolyte with asymmetric charges. Reprinted [140] with
permission – Copyright 2017 American Chemical Society.
2.4.2 Polyelectrolyte multilayering
Formation of polyelectrolyte multi-layers, as mentioned before, includes adsorption of the first polyelectrolyte
layer onto a substrate, adsorption of the second layer via complexation and further polycation-polyanion
complexation based layering steps. This procedure, up to the 3rd layer (which can be extrapolated to explain
all consecutive layers), is well presented in the widely-accepted theory developed by J.F. Joanny and M.
Castelnovo [83] which describes layer-by-layer polyelectrolyte deposition based on electrostatics and can be
summarised into an example-based diagram presented below (Figure 15). This theory is mostly applicable for
weakly charged polyelectrolytes and is built on following assumptions: polymers have the same large
molecular weights M w, same fraction of charged groups f , and the same concentrations c.
Note: in formulas included in the Figure 15 a is the size of a polyelectrolyte monomer, n is the concentration
of counterions, w is the calculational coefficient of the order of monomer volume a3, lb is the Bjerrum length,
f is the fraction of charged groups.
At low added salt concentrations, the growth of polyelectrolyte multilayers can be described by two regimes –
linear, where the thickness increment is constant for each deposited bilayer, and exponential, in which
thickness increment increases with the number of layers [1, 141]. Any multilayer assembled via the
electrostatic layer-by-layer procedure can be characterised by a general growth profile that contains both
linear and exponential parts with a switch point where the transition from one regime to another occurs
(Figure 16A). If the film grows linearly, the exponential part of the profile is short and almost cannot be
distinguished; exponential growing films have a large well pronounced exponential part of the profile [141].
Figure 15 – Polyelectrolyte multilayering in terms of theory by J.F. Joanny and M. Castelnovo [83].
One of the most important aspects of these profiles is the switch point, and how the switch from one growth
regime to another can be induced.
The switch from exponential to linear growth can be explained by two growth regime models – the
“roughness” model and the “diffusion” model.
The “roughness” model (Figure 16B) describes the formation of multi-layers starting from formation of
isolated islands, which grow in height and diameter with the number of layers leading to the exponential
increase in covered surface area [141]. These isolated islands grow up to a point of coagulation with the
neighbouring islands producing at multi-layer that then grows linearly. This model provides an explanation
for the deviation from linear growth for the first several layers in films that have a pronounced linear growth
regime otherwise [141].
Figure 16 – A – Growth profile of HA/PLL multi-layer showing a switch from exponential to linear growth
regimes. B – Scheme of “roughness” model representing a coalescence of initially formed islands at the
switch point during the multi-layer build-up. C – Scheme of “diffusion" model representing a formation of
restructuring zone (polymer diffusion is restricted) underneath the diffusion zone at the switch point.
Reprinted [141] with permission from Elsevier.
The “diffusion" model describes the growth of multilayers based on the possibility of diffusion of component
polyelectrolyte chains in and out of the fabricated multi-layer [141, 142]. If polyelectrolyte chains are not able
to diffuse into the multilayer the film grows linearly, otherwise – exponentially. In the process of adsorption
of the oppositely charged polyelectrolyte, the excess amount of the polyelectrolyte within the film moves to
the interface and produces complexes with the newly adsorbing oppositely charged polyelectrolyte. In this
case, the increase in the multi-layer thickness leads to the increase in polymer uptake of the each freshly
adsorbed layer – the growth is exponential. Within this model, the switch from exponential to linear regimes
can be explained by the formation of so-called “forbidden zone”, or “restructuring” zone within the multi-
layer that forms between the first several layers and the outer layers. This zone is formed with the increase in
a number of polyelectrolyte layers and is a consequence of the relative rearrangement of the polyelectrolyte
chains within the multi-layer; such rearrangement takes place close to substrate creating the structure
impenetrable to polyelectrolyte chain diffusion, leading to the switch to the linear growth regime [1, 141,
142]. This model provides a good fit for experiments with polyelectrolytes of high molecular weight but does
not explain low molecular weight multilayer growth behaviour which still switches from exponential to linear
even though short chain polyelectrolytes are able to diffuse into the multi-layer easily [143]. The possible
solution for this contradiction is that low molecular weight polyelectrolytes can diffuse out of the multilayer
completely and form complexes outside the film thus removing the excess polymer that could have led to the
exponential growth maintenance [143]. Another possible cause is the formation of an electrostatic barrier on
top of the film that prevents mobile polyelectrolyte chains from diffusing through the surface (meaning that
excess polyelectrolyte would be trapped within the multi-layer) [141].
Since complexation of polyelectrolytes is mostly driven by electrostatic interactions, it is assumed that linear
multilayer growth is common for polyelectrolyte complexes with intrinsically-induced charge compensation
(strong polyelectrolytes), while exponential growth is based on both intrinsic and extrinsic charge
compensation types [141] (weaker polyelectrolytes). The comparison of outcome multi-layers for both growth
regimes is shown in Figure 17.
Figure 17 – Linearly and exponentially grown multi-layers. Adapted [141] with permission from Elsevier.
Growth regimes can be induced/prevented by external factors such as temperature, pH and added salt content
of the multi-layering medium. The effects of these factors are summarised in Table 11.
Table 11 – Factors influencing polyelectrolyte multilayer growth regime
Factor Effect on growth regimeTemperature Polyelectrolyte complexation occurs spontaneously when the change in associated free Gibbs
energy ∆ G is negative
(37) ∆ G=∆ H−T ∆ S
Free Gibbs energy contains two contributions, enthalpic ∆ H and entropic T ∆ S.
As it has been mentioned earlier, polyelectrolyte complex formation is influenced by entropy, which is, if low, prevents weakly charged polyelectrolytes from the complex formation. Interaction of oppositely charged polyelectrolytes leads to some of the counterions escaping into a solution which causes the increase in entropy [144] and favours complex formation [141, 145] and thus to linear multilayer growth.
Enthalpy, which is equal to the heat exchanged by the system (in this case, polyelectrolyte complex at its formation) and its surrounding medium, plays important role in multilayer growth regime outcome as well. It is also the only parameter that can be measured directly by calorific experiments [144]. Linearly growing films are produced if the complexation process is exothermic (∆ H ≤−1000 J ∙mol−1) with negative change in enthalpy (positive in entropy); endothermic complexation accompanied by counteractive positive gain both in enthalpy (∆ H ≥−500 J ∙mol−1) and entropy leads to exponentially growing multilayers.
Thus, the temperature has a larger effect on exponentially growing films: the pronounced increase in multilayer thickness with increase in temperature [141] is observed, while linearly growing films show no or a very small thickness increase [144].
pH The changes in pH of the complexation medium result in changes in polyelectrolyte multilayer growth mechanism since pH can be used to alter the density of charged groups (in weak polyelectrolytes) leading to strengthening or weakening of polyelectrolyte interactions.
General growth regime-pH dependency trend was clearly illustrated by Peter Bieker and Monika Schönhoff [146] who have reported growth behaviour of PAH/PAA multilayers at five different pH values and have got the following results:
pH Influence on polyelectrolyte Growth regime
3-4.5 PAA (acid) 50% charged, PAH (base) nearly fully charged
Linear, rigid asymmetric film.
4.5-6 Increase in PAA charge density, decrease in PAH
Exponential, 4.5 switch point, rigid but not compact film (allows for diffusion of chains into multilayer).
6.5-7.5 Both PAA and PAH are nearly fully charged
Linear as both polymers behave like strong polyelectrolytes with strong polyion interaction (no interlayer diffusion allowed). Symmetric film.
8-10 Further increase in PAA charge density, decrease in PAH
Exponential (same behaviour as pH 4.5-6 regime, non-compact multilayer with allowed diffusion)
10-12 PAA is nearly fully charged, PAH very weakly charged
Linear, rigid asymmetric film.
Therefore, when one or both of polyelectrolytes are fully charged (which can be accomplished by tuning the pH of the solution) one can expect linear film growth due to strong electrostatic interactions; otherwise, exponential growth is observed [1, 146].
It should also be noted that the stability of the resulting film can be affected by the pH
variation. In both flat [Hoogeveen, Cohen Stuart, Fleer] and spherical [DOI: 10.1021/la049934h] multi-layered films, fabricated using at least one weak polyelectrolyte, noticeable softening of the structures is observed under the pH change. It has also been shown that the number of layers, or, from another perspective, type of the outer layer, changes the response of the film to the medium change [Hoogeveen, Cohen Stuart, Fleer]. Partial pH-induced desorption occurs in case of the top layer being composed of a weak polyelectrolyte (odd number of layers), while strong polyelectrolyte layer on the top traps weak polyelectrolyte layers enough to make the structure stable [Hoogeveen, Cohen Stuart, Fleer]. pH-induced softening is believed to be the consequence of the change in the charge density of weak polyelectrolytes caused by the presence of the titrable groups that can be protonated/deprotonated by the pH-changing agent thus influencing the number of charges present on the polymer molecules [Simulation of weak polyelectrolytes:A comparison between the constant pHand the reaction ensemble method]. Impact of the pH on dissociation behaviour of polyelectrolytes is formalised in section 1.2.
The stability of the films assembled using a pair of strong polyelectrolytes is not affected by the pH.
Ionic strength (added salt content)
Additional counterions (added salt) introduced into complexation medium screen polyelectrolyte charges which results in reduced number density of complexed polyion pairs within the multilayer. This leads to non-compact films and facilitates the diffusion of polyelectrolyte chains into the multilayer resulting in exponential growth regime. By introducing additional salt ions one can switch growth regime from linear to exponential and grow thicker films [141]. The effect of salt concentration onto growth regimes and the behaviour of the resulting films are summarised in the picture below (Reprinted [141] with permission from Elsevier).
In both flat [Hoogeveen, Cohen Stuart, Fleer] and spherical [DOI: 10.1021/la049934h] multi-layered films,
fabricated using at least one weak polyelectrolyte, noticeable softening of the structures is observed under the
pH change. It has also been shown that the number of layers, or, from another perspective, type of the outer
layer, changes the response of the film to the medium change [Hoogeveen, Cohen Stuart, Fleer]. Partial pH-
induced desorption occurs in case of the top layer being composed of a weak polyelectrolyte (odd number of
layers), while strong polyelectrolyte layer on the top traps weak polyelectrolyte layers enough to make the
structure stable [Hoogeveen, Cohen Stuart, Fleer]. pH-induced softening is believed to be the consequence of
the change in the charge density of weak polyelectrolytes caused by the presence of the titrable groups that
can be protonated/deprotonated. The stability of the films assembled using a pair of strong polyelectrolytes is
not affected by the pH or the ionic strength.
Conclusion
A wide range of multi-layered structures can be fabricated using the electrostatic layer-by-layer method,
making it a very important production technique for a number of industries including medical, cosmetics,
wastewater treatment, and any other area that involves using encapsulated or layered materials. In this review,
we have comprised a summative description of the current understanding of the materials (templates and
polyelectrolytes) and processes involved in the layer-by-layer procedure, including polyelectrolyte adsorption
process (polyelectrolyte behaviour at the interface, characterised by such parameters as
completion/incompletion (saturation/unsaturation) of the layer, adsorbed mass and morphology of the formed
layer), interactions between polyelectrolytes and the external factors that control them (temperature, pH, ionic
strength), as well as the impact of the interactions themselves on the multi-layering process outcomes
(polyelectrolyte complexation). We have also presented a list of construction materials that can be and have
been successfully used with the layer-by-layer procedure for fabrication of a wide range of structures of
different sizes and structures. This review, thus, can serve as a starting guide for working with the electrostatic
layer-by-layer method and is a reference for selection of the materials and conditions of the multi-layering
procedure for the desired production outcome.
References
[1] J. Borges and J. F. Mano, “Molecular interactions driving the layer-by-layer assembly of multilayers,”
Chemical reviews, vol. 114, no. 18, pp. 8883–8942, 2014.
[2] R. Iler, “Multilayers of colloidal particles,” Journal of colloid and interface science, vol. 21, no. 6, pp.
569–594, 1966.
[3] G. Decher and J.-D. Hong, “Buildup of ultrathin multilayer films by a self-assembly process, 1
consecutive adsorption of anionic and cationic bipolar amphiphiles on charged surfaces,” in Makromolekulare
Chemie. Macromolecular Symposia, vol. 46, no. 1. Wiley Online Library, 1991, pp. 321–327.
[4] G. Decher and J. Hong, “Buildup of ultrathin multilayer films by a self-assembly process: Ii.
consecutive adsorption of anionic and cationic bipolar amphiphiles and polyelectrolytes on charged surfaces,”
Berichte der Bunsengesellschaft für physikalische Chemie, vol. 95, no. 11, pp. 1430–1434, 1991.
[5] J. F. Quinn, A. P. Johnston, G. K. Such, A. N. Zelikin, and F. Caruso, “Next generation, sequentially
assembled ultrathin films: beyond electrostatics,” Chemical Society Reviews, vol. 36, no. 5, pp. 707–718,
2007.
[6] E. Guzmán, A. Mateos-Maroto, M. Ruano, F. Ortega, and R. G. Rubio, “Layer-by-layer
polyelectrolyte assemblies for encapsulation and release of active compounds,” Advances in colloid and
interface science, 2017.
[7] C. Jiang, S. Markutsya, Y. Pikus, and V. V. Tsukruk, “Freely suspended nanocomposite membranes
as highly sensitive sensors,” Nature materials, vol. 3, no. 10, pp. 721–728, 2004.
[8] A. A. Mamedov and N. A. Kotov, “Free-standing layer-by-layer assembled films of magnetite
nanoparticles,” Langmuir, vol. 16, no. 13, pp. 5530–5533, 2000.
[9] D. W. Kim, A. Blumstein, J. Kumar, L. A. Samuelson, B. Kang, and C. Sung, “Ordered multilayer
nanocomposites prepared by electrostatic layer-by-layer assembly between aluminosilicate nanoplatelets and
substituted ionic polyacetylenes,” Chemistry of materials, vol. 14, no. 9, pp. 3925–3929, 2002.
[10] Y.-H. Lin, C. Jiang, J. Xu, Z. Lin, and V. V. Tsukruk, “Sculptured layer-by-layer films,” Advanced
Materials, vol. 19, no. 22, pp. 3827–3832, 2007.
[11] S. J. Gates and A. Shukla, “Layer-by-layer assembly of readily detachable chitosan and poly (acrylic
acid) polyelectrolyte multilayer films,” Journal of Polymer Science Part B: Polymer Physics, vol. 55, no. 2,
pp. 127–131, 2017.
[12] A. L. Larkin, R. M. Davis, and P. Rajagopalan, “Biocompatible, detachable, and free-standing
polyelectrolyte multilayer films,” Biomacromolecules, vol. 11, no. 10, pp. 2788–2796, 2010.
[13] J. M. Silva, A. R. C. Duarte, S. G. Caridade, C. Picart, R. L. Reis, and J. F. Mano, “Tailored
freestanding multilayered membranes based on chitosan and alginate,” Biomacromolecules, vol. 15, no. 10,
pp. 3817–3826, 2014.
[14] J. L. Lutkenhaus, K. D. Hrabak, K. McEnnis, and P. T. Hammond, “Elastomeric flexible free-standing
hydrogen-bonded nanoscale assemblies,” Journal of the American Chemical Society, vol. 127, no. 49, pp.
17228–17234, 2005.
[15] T. Serizawa, M. Yamaguchi, and M. Akashi, “Alternating bioactivity of polymeric layer-by-layer
assemblies: anticoagulation vs procoagulation of human blood,” Biomacromolecules, vol. 3, no. 4, pp. 724–
731, 2002.
[16] A. M. Ferreira, P. Gentile, S. Toumpaniari, G. Ciardelli, and M. A. Birch, “Impact of collagen/heparin
multilayers for regulating bone cellular functions,” ACS Applied Materials & Interfaces, vol. 8, no. 44, pp.
29923–29932, 2016.
[17] P. Gentile, M. E. Frongia, M. Cardellach, C. A. Miller, G. P. Stafford, G. J. Leggett, and P. V. Hatton,
“Functionalised nanoscale coatings using layer-by-layer assembly for imparting antibacterial properties to
polylactide-co-glycolide surfaces,” Acta biomaterialia, vol. 21, pp. 35–43, 2015.
[18] H. Gao, M. Zhang, J. Zhao, L. Gao, and M. Li, “In vitro and in vivo degradation and mechanical
properties of ZEK100 magnesium alloy coated with alginate, chitosan and mechano-growth factor,” Materials
Science and Engineering: C, vol. 63, pp. 450–461, 2016.
[19] H. Ai, Y. M. Lvov, D. K. Mills, M. Jennings, J. S. Alexander, and S. A. Jones, “Coating and selective
deposition of nanofilm on silicone rubber for cell adhesion and growth,” Cell biochemistry and biophysics,
vol. 38, no. 2, pp. 103–114, 2003.
[20] H. Ai, S. A. Jones, and Y. M. Lvov, “Biomedical applications of electrostatic layer-by-layer nano-
assembly of polymers, enzymes, and nanoparticles,” Cell biochemistry and biophysics, vol. 39, no. 1, pp. 23–
43, 2003.
[21] K. Katagiri, S.-i. Yamazaki, K. Inumaru, and K. Koumoto, “Anti-reflective coatings prepared via
layer-by-layer assembly of mesoporous silica nanoparticles and polyelectrolytes,” Polymer Journal, vol. 47,
no. 2, pp. 190–194, 2015.
[22] S. Roy and A. J. Pal, “Sequentially adsorbed layer-by-layer self assembled films: light-emitting
devices based on evans blue,” Materials Science and Engineering: C, vol. 18, no. 1, pp. 65–70, 2001.
[23] C. Lu, H. Möhwald, and A. Fery, “Large-scale regioselective formation of well-defined stable
wrinkles of multilayered films via embossing,” Chemistry of Materials, vol. 20, no. 22, pp. 7052–7059, 2008.
[24] K. Halász, Y. Hosakun, and L. Csóka, “Reducing water vapor permeability of poly (lactic acid) film
and bottle through layer-by-layer deposition of green-processed cellulose nanocrystals and chitosan,”
International Journal of Polymer Science, vol. 2015, 2015.
[25] G. Shen, X. Hu, G. Guan, and L. Wang, “Surface modification and characterisation of silk fibroin
fabric produced by the layer-by-layer self-assembly of multilayer alginate/regenerated silk fibroin,” PloS one,
vol. 10, no. 4, p. e0124811, 2015.
[26] Y. Serfert, J. Schröder, A. Mescher, J. Laackmann, S. Drusch, and K. Schwarz, “Characterization of
spray-dried layer-by-layer emulsions,” in Proceedings of ICEF 11-International Congress on Engineering
and Food, Athen, GR, 2011.
[27] C. Kantak, S. Beyer, L. Yobas, T. Bansal, and D. Trau, “A ‘microfluidic pinball’ for on-chip
generation of layer-by-layer polyelectrolyte microcapsules,” Lab on a Chip, vol. 11, no. 6, pp. 1030–1035,
2011.
[28] G. Bortnowska, “Multilayer oil-in-water emulsions: formation, characteristics and application as the
carriers for lipophilic bioactive food components – a review,” Polish Journal of Food and Nutrition Sciences,
vol. 65, no. 3, pp. 157–166, 2015.
[29] E. M. Shchukina and D. G. Shchukin, “Layer-by-layer coated emulsion microparticles as storage and
delivery tool,” Current opinion in colloid & interface science, vol. 17, no. 5, pp. 281–289, 2012.
[30] M. Adamczak, G. Para, C. Simon, and P. Warszynski, “Natural oil nanoemulsions as cores for layer-
by-layer encapsulation,” Journal of microencapsulation, vol. 30, no. 5, pp. 479–489, 2013.
[31] T. Ramasamy, Z. S. Haidar, T. H. Tran, J. Y. Choi, J.-H. Jeong, B. S. Shin, H.-G. Choi, C. S. Yong,
and J. O. Kim, “Layer-by-layer assembly of liposomal nanoparticles with pegylated polyelectrolytes enhances
systemic delivery of multiple anticancer drugs,” Acta biomaterialia, vol. 10, no. 12, pp. 5116–5127, 2014.
[32] G. A. Kaminski, M. R. Sierakowski, R. Pontarolo, L. A. dos Santos, and R. A. de Freitas, “Layer-by-
layer polysaccharide-coated liposomes for sustained delivery of epidermal growth factor,” Carbohydrate
polymers, vol. 140, pp. 129–135, 2016.
[33] K. Ariga, Y. Yamauchi, G. Rydzek, Q. Ji, Y. Yonamine, K. C.-W. Wu, and J. P. Hill, “Layer-by-layer
nanoarchitectonics: invention, innovation, and evolution,” Chemistry Letters, vol. 43, no. 1, pp. 36–68, 2013.
[34] I. S. Elizarova and P. F. Luckham, “Layer-by-layer encapsulated nano-emulsion of ionic liquid loaded
with functional material for extraction of Cd 2+ ions from aqueous solutions,” Journal of colloid and interface
science, vol. 491, pp. 286–293, 2017.
[35] T. Cosgrove, Colloid science: principles, methods and applications. John Wiley & Sons, 2010.
[36] J. Gregory, Particles in water: properties and processes. CRC Press, 2005.
[37] “Isoelectric points of Nanomaterials Q&A,” https://bit.ly/2n4ERXx, Accessed: 2018-08-02.
[38] “Clay Minerals,” http://bit.ly/2w7oxdO, Accessed: 2017-06-28.
[39] X. Yang, X. Han, and Y. Zhu, “(PAH/PSS) 5 microcapsules templated on silica core: Encapsulation
of anticancer drug DOX and controlled release study,” Colloids and Surfaces A: Physicochemical and
Engineering Aspects, vol. 264, no. 1, pp. 49–54, 2005.
[40] X. Shi, A. L. Briseno, R. J. Sanedrin, and F. Zhou, “Formation of uniform polyaniline thin shells and
hollow capsules using polyelectrolyte-coated microspheres as templates,” Macromolecules, vol. 36, no. 11,
pp. 4093–4098, 2003.
[41] J. J. Richardson, K. Liang, K. Kempe, H. Ejima, J. Cui, and F. Caruso, “Immersive polymer assembly
on immobilized particles for automated capsule preparation,” Advanced Materials, vol. 25, no. 47, pp. 6874–
6878, 2013.
[42] M. Björnmalm, A. Roozmand, K. F. Noi, J. Guo, J. Cui, J. J. Richardson, and F. Caruso, “Flow-based
assembly of layer-by-layer capsules through tangential flow filtration,” Langmuir, vol. 31, no. 33, pp. 9054–
9060, 2015.
[43] Y. Wang, A. S. Angelatos, and F. Caruso, “Template synthesis of nanostructured materials via layer-
by-layer assembly,” Chemistry of Materials, vol. 20, no. 3, pp. 848–858, 2007.
[44] Q.-L. Li, Y. Sun, Y.-L. Sun, J. Wen, Y. Zhou, Q.-M. Bing, L. D. Isaacs, Y. Jin, H. Gao, and Y.-W.
Yang, “Mesoporous silica nanoparticles coated by layer-by-layer self-assembly using cucurbit [7] uril for in
vitro and in vivo anticancer drug release,” Chemistry of Materials, vol. 26, no. 22, pp. 6418–6431, 2014.
[45] H.-Y. Zhang, Y.-F. Sun, Y.-L. Sun, and M. Zhou, “pH-responsive mesoporous silica nanocarriers
based on layer-by-layer self-assembly,” Bio-medical materials and engineering, vol. 24, no. 6, pp. 2211–
2218, 2014.
[46] M. D. Yilmaz, “Layer-by-layer hyaluronic acid/chitosan polyelectrolyte coated mesoporous silica
nanoparticles as pH-responsive nanocontainers for optical bleaching of cellulose fabrics,” Carbohydrate
polymers, vol. 146, pp. 174–180, 2016.
[47] Y. Hu, K. Cai, Z. Luo, and K. D. Jandt, “Layer-by-layer assembly of β-estradiol loaded mesoporous
silica nanoparticles on titanium substrates and its implication for bone homeostasis,” Advanced Materials,
vol. 22, no. 37, pp. 4146–4150, 2010.
[48] W. Tong, S. She, L. Xie, and C. Gao, “High efficient loading and controlled release of low-molecular-
weight drugs by combination of spontaneous deposition and heat-induced shrinkage of multilayer capsules,”
Soft Matter, vol. 7, no. 18, pp. 8258–8265, 2011.
[49] A. G. Skirtach, A. M. Yashchenok, and H. Möhwald, “Encapsulation, release and applications of LbL
polyelectrolyte multilayer capsules,” Chemical Communications, vol. 47, no. 48, pp. 12736–12746, 2011.
[50] F. Caruso, R. A. Caruso, and H. Möhwald, “Nanoengineering of inorganic and hybrid hollow spheres
by colloidal templating,” Science, vol. 282, no. 5391, pp. 1111–1114, 1998.
[51] “Polysterene Latex Beads – Sigma-Aldrich Product Sheet,” http://bit.ly/2vgLVa7, Accessed: 2017-
06-28.
[52] I. S. Elizarova and P. F. Luckham, “Fabrication of polyelectrolyte multilayered nano-capsules using a
continuous layer-by-layer approach,” Journal of colloid and interface science, vol. 470, pp. 92–99, 2016.
[53] W. S. Choi, H. Y. Koo, J.-H. Park, and D.-Y. Kim, “Synthesis of two types of nanoparticles in
polyelectrolyte capsule nanoreactors and their dual functionality,” Journal of the American Chemical Society,
vol. 127, no. 46, pp. 16136–16142, 2005.
[54] H. Dong and J. D. Brennan, “Rapid fabrication of core – shell silica particles using a multilayer-by-
multilayer approach,” Chemical Communications, vol. 47, no. 4, pp. 1207–1209, 2011.
[55] M. Barisik, S. Atalay, A. Beskok, and S. Qian, “Size dependent surface charge properties of silica
nanoparticles,” The Journal of Physical Chemistry C, vol. 118, no. 4, pp. 1836–1842, 2014.
[56] K. S. Mayya, D. I. Gittins, and F. Caruso, “Gold-titania core-shell nanoparticles by polyelectrolyte
complexation with a titania precursor,” Chemistry of materials, vol. 13, no. 11, pp. 3833–3836, 2001.
[57] D. I. Gittins and F. Caruso, “Multilayered polymer nanocapsules derived from gold nanoparticle
templates,” Advanced Materials, vol. 12, no. 24, pp. 1947–1949, 2000.
[58] D. I. Gittins I and F. Caruso, “Tailoring the polyelectrolyte coating of metal nanoparticles,” The
Journal of Physical Chemistry B, vol. 105, no. 29, pp. 6846–6852, 2001.
[59] G. Schneider, G. Decher, N. Nerambourg, R. Praho, M. H. Werts, and M. Blanchard-Desce,
“Distance-dependent fluorescence quenching on gold nanoparticles ensheathed with layer-by-layer assembled
polyelectrolytes,” Nano letters, vol. 6, no. 3, pp. 530–536, 2006.
[60] I. I. Slowing, J. L. Vivero-Escoto, C.-W. Wu, and V. S.-Y. Lin, “Mesoporous silica nanoparticles as
controlled release drug delivery and gene transfection carriers,” Advanced drug delivery reviews, vol. 60,
no. 11, pp. 1278–1288, 2008.
[61] F. Tang, L. Li, and D. Chen, “Mesoporous silica nanoparticles: synthesis, biocompatibility and drug
delivery,” Advanced Materials, vol. 24, no. 12, pp. 1504–1534, 2012.
[62] D. V. Volodkin, A. I. Petrov, M. Prevot, and G. B. Sukhorukov, “Matrix polyelectrolyte
microcapsules: new system for macromolecule encapsulation,” Langmuir, vol. 20, no. 8, pp. 3398–3406,
2004.
[63] L. Qi, J. Li, J. Ma et al., “Biomimetic morphogenesis of calcium carbonate in mixed solutions of
surfactants and double-hydrophilic block copolymers,” advanced materials, vol. 14, no. 4, p. 300, 2002.
[64] J. Leßig, B. Neu, and U. Reibetanz, “Influence of Layer-by-Layer (LbL) assembled CaCO3-carriers
on macrophage signaling cascades,” Biomacromolecules, vol. 12, no. 1, pp. 105–115, 2010.
[65] B. G. De Geest, A. G. Skirtach, T. R. De Beer, G. B. Sukhorukov, L. Bracke, W. R. Baeyens,
J. Demeester, and S. C. De Smedt, “Stimuli-responsive multilayered hybrid nanoparticle/polyelectrolyte
capsules,” Macromolecular rapid communications, vol. 28, no. 1, pp. 88–95, 2007.
[66] W. Yuan, Z. Lu, and C. M. Li, “Controllably layer-by-layer self-assembled
polyelectrolytes/nanoparticle blend hollow capsules and their unique properties,” Journal of Materials
Chemistry, vol. 21, no. 13, pp. 5148–5155, 2011.
[67] M.-Y. Ma, Y.-J. Zhu, L. Li, and S.-W. Cao, “Nanostructured porous hollow ellipsoidal capsules of
hydroxyapatite and calcium silicate: preparation and application in drug delivery,” Journal of Materials
Chemistry, vol. 18, no. 23, pp. 2722–2727, 2008.
[68] T. F. Tadros, Emulsion formation and stability. John Wiley & Sons, 2013.
[69] K. Szczepanowicz, D. Dronka-Góra, G. Para, and P. Warszynski, “Encapsulation of liquid cores by
layer-by-layer adsorption of polyelectrolytes,” Journal of microencapsulation, vol. 27, no. 3, pp. 198–204,
2010.
[70] K. Szczepanowicz, H. Hoel, L. Szyk-Warszynska, E. Bielanska, A. Bouzga, G. Gaudernack,
C. Simon, and P. Warszynski, “Formation of biocompatible nanocapsules with emulsion core and pegylated
shell by polyelectrolyte multilayer adsorption,” Langmuir, vol. 26, no. 15, pp. 12592–12597, 2010.
[71] X. Teng, D. G. Shchukin, and H. Möhwald, “Encapsulation of water-immiscible solvents in
polyglutamate/polyelectrolyte nanocontainers,” Advanced Functional Materials, vol. 17, no. 8, pp. 1273–
1278, 2007.
[72] P. Thanasukarn, R. Pongsawatmanit, and D. J. McClements, “Utilization of layer-by-layer interfacial
deposition technique to improve freez e-thaw stability of oil-in-water emulsions,” Food research
international, vol. 39, no. 6, pp. 721–729, 2006.
[73] B. S. Sekhon, “Surfactants: pharmaceutical and medicinal aspects,” Journal of Pharmaceutical
Technology, Research and Management, vol. 1, no. 1, 2014.
[74] X. R. Teng, D. G. Shchukin, and H. Möhwald, “A novel drug carrier: lipophilic drug-loaded
polyglutamate/polyelectrolyte nanocontainers,” Langmuir, vol. 24, no. 2, pp. 383–389, 2008.
[75] Y. P. Patil and S. Jadhav, “Novel methods for liposome preparation,” Chemistry and physics of lipids,
vol. 177, pp. 8–18, 2014.
[76] A. Akbarzadeh, R. Rezaei-Sadabady, S. Davaran, S. W. Joo, N. Zarghami, Y. Hanifehpour,
M. Samiei, M. Kouhi, and K. Nejati-Koshki, “Liposome: classification, preparation, and applications,”
Nanoscale research letters, vol. 8, no. 1, p. 102, 2013.
[77] A. Yadav, M. Murthy, A. Shete, and S. Sakhare, “Stability aspects of liposomes,” Indian Journal Of
Pharmaceutical Education And Research, vol. 45, no. 4, pp. 402–413, 2011.
[78] Q. Yin, B. Ke, X. Chen, Y. Guan, P. Feng, G. Chen, Y. Kang, W. Zhang, and Y. Nie, “Effects of
liposomes charge on extending sciatic nerve blockade of N-ethyl bromide of lidocaine in rats,” Scientific
reports, vol. 6, p. 38582, 2016.
[79] A. Perico, “Polyelectrolyte fundamentals,” Ionic Interactions in Natural and Synthetic
Macromolecules, pp. 49–90, 2012.
[80] J. Koetz and S. Kosmella, Polyelectrolytes and nanoparticles. Springer Science & Business Media,
2007.
[81] K. Saldadze and V. Kopilova-Valova, Chelating resins (complexities). Khimiia Publ., 1980.
[82] G. S. Manning, “Counterion binding in polyelectrolyte theory,” Accounts of Chemical Research,
vol. 12, no. 12, pp. 443–449, 1979.
[83] J.-F. Joanny and M. Castelnovo, “Polyelectrolyte adsorption and multilayer formation,” Multilayer
Thin Films: Sequential Assembly of Nanocomposite Materials, 2006.
[84] P.-G. d. De Gennes, P. Pincus, R. Velasco, and F. Brochard, “Remarks on polyelectrolyte
conformation,” Journal de physique, vol. 37, no. 12, pp. 1461–1473, 1976.
[85] A. V. Dobrynin, R. H. Colby, and M. Rubinstein, “Scaling theory of polyelectrolyte solutions,”
Macromolecules, vol. 28, no. 6, pp. 1859–1871, 1995.
[86] R. M. Fuoss, A. Katchalsky, and S. Lifson, “The potential of an infinite rod-like molecule and the
distribution of the counter ions,” Proceedings of the National Academy of Sciences, vol. 37, no. 9, pp. 579–
589, 1951.
[87] A. Szarpak, D. Cui, F. Dubreuil, B. G. De Geest, L. J. De Cock, C. Picart, and R. AuzeÌly-Velty, �“Designing hyaluronic acid-based layer-by-layer capsules as a carrier for intracellular drug delivery,”
Biomacromolecules, vol. 11, no. 3, pp. 713–720, 2010.
[88] J. Tripathy and A. M. Raichur, “Designing carboxymethyl cellulose based layer-by-layer capsules as a
carrier for protein delivery,” Colloids and Surfaces B: Biointerfaces, vol. 101, pp. 487–492, 2013.
[89] N. de Acha, C. Elosúa, D. Martnez, M. Hernáez, I. R. Matás, and F. J. Arregui, “Comparative study of
polymeric matrices embedding oxygen-sensitive fluorophores by means of layer-by-layer nanosassembly,”
Sensors and Actuators B: Chemical, vol. 239, pp. 1124–1133, 2017.
[90] M. Heiwagei, “Synthesis of PDADMAC/PSS Nanocapsules Using Calcium Phosphate Templates,”
Master’s thesis, Imperial College London, 2010.
[91] A. Voigt, E. Donath, and H. Möhwald, “Preparation of microcapsules of strong polyelectrolyte
couples by one-step complex surface precipitation,” Macromolecular Materials and Engineering, vol. 282,
no. 1, pp. 13–16, 2000.
[92] A. Sybachin, O. Zaborova, V. Orlov, P. Semenyuk, M. Ballauff, E. Kesselman, J. Schmidt,
Y. Talmon, F. Menger, and A. Yaroslavov, “Complexes between anionic liposomes and spherical
polycationic brushes. An assembly of assemblies,” Langmuir, vol. 30, no. 9, pp. 2441–2447, 2014.
[93] H. Lee, Y. Jeong, and T. G. Park, “Shell cross-linked hyaluronic acid/polylysine layer-by-layer
polyelectrolyte microcapsules prepared by removal of reducible hyaluronic acid microgel cores,”
Biomacromolecules, vol. 8, no. 12, pp. 3705–3711, 2007.
[94] S. V. Bhujbal, B. De Haan, S. P. Niclou, and P. De Vos, “A novel multilayer immunoisolating
encapsulation system overcoming protrusion of cells,” Scientific reports, vol. 4, 2014.
[95] J. Jing, A. Szarpak-Jankowska, R. Guillot, I. Pignot-Paintrand, C. Picart, and R. AuzeÌly-Velty, �“Cyclodextrin/paclitaxel complex in biodegradable capsules for breast cancer treatment,” Chemistry of
Materials, vol. 25, no. 19, pp. 3867–3873, 2013.
[96] D. B. Trushina, T. V. Bukreeva, and M. N. Antipina, “Size-controlled synthesis of vaterite calcium
carbonate by the mixing method: aiming for nanosized particles,” Crystal Growth & Design, vol. 16, no. 3,
pp. 1311–1319, 2016.
[97] Y. Kashcooli, K. Park, A. Bose, M. Greenfield, and G. D. Bothun, “Patchy layersomes formed by
layer-by-layer coating of liposomes with strong biopolyelectrolytes,” Biomacromolecules, vol. 17, no. 11, pp.
3838–3844, 2016.
[98] H. Gao, O. A. Goriacheva, N. V. Tarakina, and G. B. Sukhorukov, “Intracellularly biodegradable
polyelectrolyte/silica composite microcapsules as carriers for small molecules,” ACS applied materials &
interfaces, vol. 8, no. 15, pp. 9651–9661, 2016.
[99] M. Paini, B. Aliakbarian, A. A. Casazza, P. Perego, C. Ruggiero, and L. Pastorino, “Chitosan/dextran
multilayer microcapsules for polyphenol co-delivery,” Materials Science and Engineering: C, vol. 46, pp.
374–380, 2015.
[100] L. Sun, X. Xiong, Q. Zou, P. Ouyang, C. Burkhardt, and R. Krastev, “Design of intelligent
chitosan/heparin hollow microcapsules for drug delivery,” Journal of Applied Polymer Science, vol. 134,
no. 5, 2017.
[101] A. S. Angelatos, A. P. Johnston, Y. Wang, and F. Caruso, “Probing the permeability of
polyelectrolyte multilayer capsules via a molecular beacon approach,” Langmuir, vol. 23, no. 8, pp. 4554–
4562, 2007.
[102] Y. Sun, Y.-L. Sun, L. Wang, J. Ma, Y.-W. Yang, and H. Gao, “Nanoassembles constructed from
mesoporous silica nanoparticles and surface-coated multilayer polyelectrolytes for controlled drug delivery,”
Microporous and Mesoporous Materials, vol. 185, pp. 245–253, 2014.
[103] K. Yoshida, T. Ono, Y. Kashiwagi, S. Takahashi, K. Sato, and J.-i. Anzai, “pH-Dependent release of
insulin from layer-by-layer-deposited polyelectrolyte microcapsules,” Polymers, vol. 7, no. 7, pp. 1269–1278,
2015.
[104] K. Katagiri, A. Matsuda, and F. Caruso, “Effect of UV- irradiation on polyelectrolyte multilayered
films and hollow capsules prepared by layer-by-layer assembly,” Macromolecules, vol. 39, no. 23, pp. 8067–
8074, 2006.
[105] S. Tomita, K. Sato, and J.-i. Anzai, “Preparation of dendrimer-loaded microcapsules by a layer-by-
layer deposition of polyelectrolytes,” Materials Science and Engineering: C, vol. 29, no. 6, pp. 2024–2028,
2009.
[106] A. Biswas, A. T. Nagaraja, and M. J. McShane, “Fabrication of nanocapsule carriers from multilayer-
coated vaterite calcium carbonate nanoparticles,” ACS applied materials & interfaces, vol. 6, no. 23, pp.
21193–21201, 2014.
[107] Y. Liu, J. Yang, Z. Zhao, J. Li, R. Zhang, and F. Yao, “Formation and characterization of natural
polysaccharide hollow nanocapsules via template layer-by-layer self-assembly,” Journal of colloid and
interface science, vol. 379, no. 1, pp. 130–140, 2012.
[108] C. Y. Yoo, J. S. Seong, and S. N. Park, “Preparation of novel capsosome with liposomal core by
layer-by-layer self-assembly of sodium hyaluronate and chitosan,” Colloids and Surfaces B: Biointerfaces,
vol. 144, pp. 99–107, 2016.
[109] S. Ye, C. Wang, X. Liu, Z. Tong, B. Ren, and F. Zeng, “New loading process and release properties
of insulin from polysaccharide microcapsules fabricated through layer-by-layer assembly,” Journal of
controlled release, vol. 112, no. 1, pp. 79–87, 2006.
[110] B. Mu, P. Liu, P. Du, Y. Dong, and C. Lu, “Magnetic-targeted pH-responsive drug delivery system
via layer-by-layer self-assembly of polyelectrolytes onto drug-containing emulsion droplets and its controlled
release,” Journal of Polymer Science Part A: Polymer Chemistry, vol. 49, no. 9, pp. 1969–1976, 2011.
[111] H. Chen, X. H. Wang, D. Li, Y. Z. Guo, and R. C. Sun, “Preparation and characterization of
quaternary chitosan/sodium alginate self-assembled microcapsules,” in Advanced Materials Research, vol.
554. Trans Tech Publ, 2012, pp. 263–267.
[112] I. Szilagyi, G. Trefalt, A. Tiraferri, P. Maroni, and M. Borkovec, “Polyelectrolyte adsorption,
interparticle forces, and colloidal aggregation,” Soft Matter, vol. 10, no. 15, pp. 2479–2502, 2014.
[113] M. Jiang, I. Popa, P. Maroni, and M. Borkovec, “Adsorption of poly (l-lysine) on silica probed by
optical reflectometry,” Colloids and Surfaces A: Physicochemical and Engineering Aspects, vol. 360, no. 1,
pp. 20–25, 2010.
[114] I. Popa, B. P. Cahill, P. Maroni, G. Papastavrou, and M. Borkovec, “Thin adsorbed films of a strong
cationic polyelectrolyte on silica substrates,” Journal of colloid and interface science, vol. 309, no. 1, pp. 28–
35, 2007.
[115] N. G. Hoogeveen, M. A. C. Stuart, and G. J. Fleer, “Polyelectrolyte adsorption on oxides: II.
Reversibility and exchange,” Journal of colloid and interface science, vol. 182, no. 1, pp. 146–157, 1996.
[116] B. P. Cahill, G. Papastavrou, G. J. Koper, and M. Borkovec, “Adsorption of poly (amido amine)
(PAMAM) dendrimers on silica: Importance of electrostatic three-body attraction,” Langmuir, vol. 24, no. 2,
pp. 465–473, 2008.
[117] J. Kleimann, C. Gehin-Delval, H. Auweter, and M. Borkovec, “Super-stoichiometric charge
neutralization in particle-polyelectrolyte systems,” Langmuir, vol. 21, no. 8, pp. 3688–3698, 2005.
[118] I. Popa, G. Papastavrou, and M. Borkovec, “Charge regulation effects on electrostatic patch-charge
attraction induced by adsorbed dendrimers,” Physical Chemistry Chemical Physics, vol. 12, no. 18, pp. 4863–
4871, 2010.
[119] E. Seyrek, J. Hierrezuelo, A. Sadeghpour, I. Szilagyi, and M. Borkovec, “Molecular mass dependence
of adsorbed amount and hydrodynamic thickness of polyelectrolyte layers,” Physical Chemistry Chemical
Physics, vol. 13, no. 28, pp. 12716–12719, 2011.
[120] M. Porus, P. Maroni, and M. Borkovec, “Structure of adsorbed polyelectrolyte monolayers
investigated by combining optical reflectometry and piezoelectric techniques,” Langmuir, vol. 28, no. 13, pp.
5642–5651, 2012.
[121] I. Popa, G. Gillies, G. Papastavrou, and M. Borkovec, “Attractive electrostatic forces between
identical colloidal particles induced by adsorbed polyelectrolytes,” The Journal of Physical Chemistry B, vol.
113, no. 25, pp. 8458–8461, 2009.
[122] M. Ashmore, J. Hearn, and F. Karpowicz, “Flocculation of latex particles of varying surface charge
densities by chitosans,” Langmuir, vol. 17, no. 4, pp. 1069–1073, 2001.
[123] I. Szilágyi, D. Rosická, J. Hierrezuelo, and M. Borkovec, “Charging and stability of anionic latex
particles in the presence of linear poly (ethylene imine),” Journal of colloid and interface science, vol. 360,
no. 2, pp. 580–585, 2011.
[124] R. López-Esparza, B. Altamirano, E. Pérez, and A. Gama Goicochea, “Importance of molecular
interactions in colloidal dispersions,” Advances in Condensed Matter Physics, vol. 2015, 2015.
[125] H. Hamaker, “The London – van der Waals attraction between spherical particles,” physica, vol. 4,
no. 10, pp. 1058–1072, 1937.
[126] T. A. Savitskaya and D. A. Kotikov, Colloid chemistry. Mn.: BGU, 2008.
[127] L. J. Kirwan, P. Maroni, S. H. Behrens, G. Papastavrou, and M. Borkovec, “Interaction and structure
of surfaces coated by poly (vinyl amines) of different line charge densities,” The Journal of Physical
Chemistry B, vol. 112, no. 46, pp. 14609–14619, 2008.
[128] M. Finessi, P. Sinha, I. Szilágyi, I. Popa, P. Maroni, and M. Borkovec, “Charge reversal of sulfate
latex particles by adsorbed linear poly (ethylene imine) probed by multiparticle colloidal probe technique,”
The Journal of Physical Chemistry B, vol. 115, no. 29, pp. 9098–9105, 2011.
[129] S. M. Notley, S. Biggs, V. S. Craig, and L. Wågberg, “Adsorbed layer structure of a weak
polyelectrolyte studied by colloidal probe microscopy and QCM-D as a function of pH and ionic strength,”
Physical Chemistry Chemical Physics, vol. 6, no. 9, pp. 2379–2386, 2004.
[130] V. Bosio, F. Dubreuil, G. Bogdanovic, and A. Fery, “Interactions between silica surfaces coated by
polyelectrolyte multilayers in aqueous environment: comparison between precursor and multilayer regime,”
Colloids and Surfaces A: Physicochemical and Engineering Aspects, vol. 243, no. 1, pp. 147–155, 2004.
[131] T. Abraham, D. Christendat, Z. Xu, J. Masliyah, J.-F. Gohy, and R. Jérôme, “Role of polyelectrolyte
charge density in tuning colloidal forces,” AIChE journal, vol. 50, no. 10, pp. 2613–2626, 2004.
[132] P. M. Claesson, E. Poptoshev, E. Blomberg, and A. Dedinaite, “Polyelectrolyte-mediated surface
interactions,” Advances in colloid and interface science, vol. 114, pp. 173–187, 2005.
[133] S. Miklavic, D. Chan, L. White, and T. Healy, “Double layer forces between heterogeneous charged
surfaces,” The Journal of Physical Chemistry, vol. 98, no. 36, pp. 9022–9032, 1994.
[134] S. Behrens, M. Borkovec, and P. Schurtenberger, “Aggregation in charge-stabilized colloidal
suspensions revisited,” Langmuir, vol. 14, no. 8, pp. 1951–1954, 1998.
[135] J. Hierrezuelo, A. Sadeghpour, I. Szilagyi, A. Vaccaro, and M. Borkovec, “Electrostatic stabilization
of charged colloidal particles with adsorbed polyelectrolytes of opposite charge,” Langmuir, vol. 26, no. 19,
pp. 15109–15111, 2010.
[136] M. Schudel, S. Behrens, H. Holthoff, R. Kretzschmar, and M. Borkovec, “Absolute aggregation rate
constants of hematite particles in aqueous suspensions: a comparison of two different surface morphologies,”
Journal of colloid and interface science, vol. 196, no. 2, pp. 241–253, 1997.
[137] M. Castelnovo and J.-F. Joanny, “Formation of polyelectrolyte multilayers,” Langmuir, vol. 16,
no. 19, pp. 7524–7532, 2000.
[138] W. H. Briscoe, “Chapter 5 - polymers and nanoscience,” in Colloidal Foundations of Nanoscience,
D. Berti and G. Palazzo, Eds. Amsterdam: Elsevier, 2014, pp. 107 – 133.
[139] M. Castelnovo and J.-F. Joanny, “Complexation between oppositely charged polyelectrolytes: Beyond
the Random Phase Approximation,” The European Physical Journal E, vol. 6, no. 1, pp. 377–386, 2001.
[140] N. N. Oskolkov and I. I. Potemkin, “Complexation in asymmetric solutions of oppositely charged
polyelectrolytes: Phase diagram,” Macromolecules, vol. 40, no. 23, pp. 8423–8429, 2007.
[141] D. Volodkin and R. von Klitzing, “Competing mechanisms in polyelectrolyte multilayer formation
and swelling: Polycation-polyanion pairing vs. polyelectrolyte-ion pairing,” Current Opinion in Colloid &
Interface Science, vol. 19, no. 1, pp. 25–31, 2014.
[142] C. Porcel, P. Lavalle, V. Ball, G. Decher, B. Senger, J.-C. Voegel, and P. Schaaf, “From exponential
to linear growth in polyelectrolyte multilayers,” Langmuir, vol. 22, no. 9, pp. 4376–4383, 2006.
[143] C. Porcel, P. Lavalle, G. Decher, B. Senger, J.-C. Voegel, and P. Schaaf, “Influence of the
polyelectrolyte molecular weight on exponentially growing multilayer films in the linear regime,” Langmuir,
vol. 23, no. 4, pp. 1898–1904, 2007.
[144] N. Laugel, C. Betscha, M. Winterhalter, J.-C. Voegel, P. Schaaf, and V. Ball, “Relationship between
the growth regime of polyelectrolyte multilayers and the polyanion/polycation complexation enthalpy,” The
Journal of Physical Chemistry B, vol. 110, no. 39, pp. 19443–19449, 2006.
[145] Z. Ou and M. Muthukumar, “Entropy and enthalpy of polyelectrolyte complexation: Langevin
dynamics simulations,” The Journal of chemical physics, vol. 124, no. 15, p. 154902, 2006.
[146] P. Bieker and M. Schönhoff, “Linear and exponential growth regimes of multilayers of weak
polyelectrolytes in dependence on pH,” Macromolecules, vol. 43, no. 11, pp. 5052–5059, 2010.
, 1987.