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This thesis presents the results of experimental investigations of the vertical and lateral properties of polyelectrolyte multilayer films (PEMs) adsorbed on a solid support. PEMs are a new class of organic thin films based on self-assembly layer-by-layer (LbL) processes of oppositely charged polyelectrolytes (charged polymers). The LbL assembly technique allows precise control of film thickness within a few nanometers and makes PEM systems especially interesting for technical applications. Thin films are prepared by alternating exposure of a hydrophilic substrate to solutions of oppositely charged polyelectrolytes. In this work, synthetic polycation poly (allylamine hydrochloride) (PAH) and polyanion poly (styrene sulfonate) (PSS) have been used. Range and amplitude of the electrostatic force during PEM build-up, has been shielded by use of high salt concentration in the deposition solution. As a foundation of any theory, role of non-elecrostatic (secondary) forces is explored. Four complementary methods have been combined to investigate the properties and composition of PEMs. X-ray reflectivity is sensitive to electron density gradients, and therefore provides information about film thickness, average electron density and interfacial roughness between materials of different electron densities (like PEM and air). Neutrons are the unique probe that is sensitive to the internal order of the multilayers (scattering length density variation) due to selective deuteration of the layers (PSS replaced by PSS_d). Therefore neutron reflectivity at V6 beamline, at the research reactor BER II, Helmholtz Centre for Materials and Energy (former Hahn-Meitner-Institute), was used in this work. Ultraviolet-visible (UV-Vis) light induces the characteristic absorption peak of polyelectrolytes and metallic nanoparticles, therefore with UV-Vis absorption spectroscopy is possible to probe the aggregation of metallic nanoparticles embedded into PEM by measuring their absorption spectra (imaginary part of the refraction index). Atomic force microscopy (AFM) allows to observe lateral structures at nano-level and to obtain surface topology of the films. Application of only small forces (pN) is achieved by use of a intermittent contact (tapping) mode in air. Summarizing the main results, the unambiguous parametrization of the investigated system for neutron reflectivity measurements enables to obtain detailed information about internal interfaces. New approach for polyelectrolyte multilayer architectures consisting of thick protonated and deuterated blocks can be used in order to distinguish different zones of the thin film growth which can be described as precursor and core zones. Thus, almost no bound water is found in precursor layers at 0% relative humidity, which suggests that water is mobile and the precursor layer is not in the glassy state like in the central zone of the PEM. Swelling behaviour of the PEMs (reversibility of the swelling) can be understood in terms of equilibrium reactions. Explored influence of temperature and type of salt used during preparation contributes to a better understanding of the formation of PEMs. The dependence of the film thickness on preparation temperature, concentration and the type of salt can be described by the hydrophobic nature of the effect. Experimental observations demonstrate that it is possible to decrease both the range and the amplitude of the electrostatic force by using an ion concentration of at least 0.1 mol/L in the solution. The role of secondary interactions such as hydrophobic attraction of the chains that can overcome electrostatic repulsion and become the major contributing factor for the layer formation and resulting structures is emphasized.
A central point of this thesis is the investigation of surface structure and surface forces, which are created by single layers of linear polyelectrolytes (PE). In detail, the properties of cationic poly(allylamine)hydrochloride (PAH) and poly-l-lysine (PLL) and anionic sodium poly(styrene sulfonate) (PSS) are determined, which have been physisorbed onto oppositely charged silica surfaces in presence of a predefined salt concentration IAds. For these investigations, a new averaging method for colloidal probe (CP) force profiles is developed, which leads to an ultimate force resolution of 1 pN after the data processing, (signal to noise ratio of > 1000). Furthermore, a new kind of tapping mode imaging is presented (so called colloidal probe tapping mode, CPTM), which uses a CP instead of a sharp tip and hence which allows to resolve lateral inhomogeneously distributed surface forces. The basics to understand such-like obtained tapping mode images are developed. For adsorption from salt-free solution (IAds = 0) the dominance of an electrostatic double layer repulsion is observed, which is commonly attributed to the adsorption of the PE chains into a rather flat and compact layer and which is in full agreement with theoretical predictions and enormous experimental data available in literature. However, even a small addition of salt to the deposition solution (i.e. IAds > 1 mM NaCl) introduces a new contribution to the surface force, which is attributed to PE chains that are non-flatly physisorbed. Using scaling considerations, it is shown for all investigated PE that this non-flat conformation can be described by brush-like chain adsorption (cf. Section 3.3.5); other conformations like mushroom or pancake are excluded (cf. Section 5.3). Interestingly, these non-flatly physisorbed chains combine properties of neutral and PE brushes: (i) The force is very well described by the theory of Alexander and de Gennes (AdG, cf. Section 5.4). By fitting the AdG force law to the data, it is possible to determine the (brush) thickness L of the PE layer and the average distance s between brush-like physisorbed chains. Although the chains are charged the electrostatic contribution to the surface forces is too small to be noticeable (cf. Section 5.4.2). (ii) The thickness L of this PE layer is much larger compared to the compact layer (observed for salt-free adsorption) and is also subject to a pronounced swelling and shrinking if the bulk salt concentration I is decreased or increased, respectively. Surprisingly, all measurements indicate that L follows a scaling law known for salted end-grafted PE brushes, i.e. L ~ N (I s^2)^(-1/3) (with N denoting the degree of polymerization). Furthermore, the osmotic brush phase is never observed in the experiments, but chain stretching up to 1 / 3 of the contour length is regularly achieved. CPTM imaging applied to PSS shows that the brush-like physisorbed chains are not homogenously distributed over the surface, but form brush domains which coexist with flatly physisorbed chains (cf. sections 5.5 and 5.6). This clearly shows that PSS generally physisorbs in two distinct phases, which differ in conformation (flat vs. brush) and the surface force caused (electrostatic vs. steric repulsion). The force profile of the two phase system is in good approximation simply the superposition of a steric and an electrostatic repulsion, whereby their respective contribution to the composed force profile is given by their area fraction. The quantitative analysis reveals that L and s of the brush phase are independent on IAds. This is remarkable, as a change in IAds is known to induce a continuous transition between a stretched (low IAds) and coiled chain conformation (high IAds) in the deposition solution (cf. [Fleer1993, Yashiro2002]). Hence, one can conclude that the conformation in solution does not necessarily correspond to the conformation after adsorption. It is also shown that the area fraction A of the brush domains strongly depends on N and IAds. For example, for constant N the scaling relation A ~ sqrt(IAds) is determined, which is very similar to the common observation that the surface coverage %Gamma of adsorbed PE layers increases also with %Gamma ~ sqrt(IAds) [Schmitt1996, Cosgrove1986, Ahrens2001, Yim2000, Gopinadhan2007, Cornelson2010]. This suggest that brush-like physisorbed PE chains are responsible for the increase in %Gamma. In fact, Section 5.6 shows that the mass of the brush phase is approx. 0.5 mg/m² which is comparable to the increase in %Gamma reported in literature for IAds = 1 M NaCl [Cosgrove1986, Schmitt1996, Ahrens2001]. As a change in IAds does not affect L and s, but solely the brush area fraction A, it is argued in Section 5.6 that an increase in IAds can be understood as a phase transition from the (disordered) flat phase towards the (ordered and extended) brush phase. Here, further theoretical considerations would be desirable.
The layer-by-layer method is a robust way of surface functionalization using a wide range of materials, e.g. synthetic and natural polyelectrolytes (PEs), proteins and nanoparticles. Thus, this method yields films with applications in diverse areas including biology and medicine. Sequential adsorption of different oppositely charged macromolecules can be used to prepare tailored films with controlled molecular organization. In biomedical research, electrically conductive coatings are of interest. In manuscript 1, we investigated films sequentially assembled from the polycation poly (diallyldimethyl-ammonium) (PDADMA) and modified carbon nanotubes (CNTs), with CNTs serving as the electrically conductive material. We assume that charge transport occurs through CNT contacts. We showed that with more than four CNT/PDADMA bilayers, the electrical conductivity is constant and independent of the number of CNT/PDADMA bilayers. A conductivity up to 4∙10^3 S/m was found. It is possible to control the conductivity with the CNT concentration of the CNT deposition suspension. A higher CNT concentration resulted in thicker CNT/PDADMA bilayers, but in a lower conductivity per bilayer. We suspect that an increased CNT concentration leads to a rapid CNT adsorption without the possibility to rearrange themselves. If PDADMA then adsorbs on the disordered CNTs in the next deposition step, the average thickness of the polymer layer is thicker than on the more ordered CNT layer from the dilute solution. This leads to an increased PE monomer/CNT ratio and lower conductivity. More polycations between the CNT layers leads to less CNT contacts. Thus, the controlled composition of films can be used to fulfill specific requirements.
For many applications of polyelectrolyte multilayers (PEMs), cheap PEs with a broad distribution of molecular weights are used. It was unknown whether the distribution of molecular weights of the PE in the adsorption solution is maintained during the adsorption process and hence in the film. To investigate this, the PSS adsorption solution in article 2 consisted of a binary mixture of short and long poly (styrene sulfonate) (PSS). A good model system to study layered films in terms of composition are PDADMA/PSS multilayers. Neutron reflectivity and in-situ ellipsometry measurements were carried out to determine the PSS composition in the film and the growth regimes. At a mole fraction of long PSS of 5 % or more in solution, the exponential growth (which is characteristic of short PSS) is totally suppressed, and only long PSS is deposited in the resulting multilayer. Variation of adsorption time of PSS showed that short PSS first adsorbs to the surface but is displaced by long PSS. Between 0 and 5 % of long PSS in the adsorption solution exponential growth occurs. The fraction of short PSS in the film continuously decreases with the increase of long PSS in the adsorption solution. In the assembly of films prepared from binary PSS mixtures, the short PSS leaves the film through adsorption/desorption steps both during PSS adsorption and during PDADMA adsorption (as PDADMA/PSS complexes). Both techniques show that the composition of the film does not correspond to that of the deposition solution. The composition and thus the properties of the resulting multilayer are influenced by the choice of adsorption time. Moreover, we conclude that a multilayer grown from a polydisperse polyelectrolyte contains fewer mobile low molecular weight polymers than the deposition solution.
In manuscript 1 and article 2, the composition of multilayers was studied. In manuscript 1 adsorption kinetics were important for the arrangement of CNTs on the surface. In article 2, the adsorption kinetics, i.e. the diffusion of the polyelectrolytes to the surface, was also investigated. In article 3, we investigated the influence of the composition of the film as well as the preparation condition on the mobility of PEs in the film. The molecular weight of the polycation PDADMA and the NaCl concentration of the deposition solution were varied. The vertical PSS diffusion constant D_PSS within the PDADMA/PSS multilayers was measured using neutron reflectivity. The salt concentration of the preparation solution defines the polymer conformation during deposition. The molecular weight of the polycation determines the degree of intertwining. Together, both parameters determine the polyanion-polycation coupling and thus the PSS mobility within the network. Log−log display of D_PSS vs the molecular weight of PDADMA and fits to two power laws (D_PSS ∝ X_n(PDADMA)^(-m) ∝ M_w(PDADMA)^(-m)) reveals for films built from 10 or 200 mM NaCl a kink. Below and above the kink, the dependence of D_PSS on M_w(PDADMA) can be described by different power laws. For Χ_n(PDADMA) < X_n,kink(PDADMA) ≈ 288, the exponents are consistent with the predictions of the sticky reptation model. X_n(PDADMA) ≈ 288 is the entanglement limit. For Χ_n(PDADMA) > X_n,kink(PDADMA) ≈ 288, the decrease of D_PSS with M_w(PDADMA) is larger than below the entanglement limit, which is indicative of sticky reptation and entanglement. The PSS diffusion constant of films built from 100 mM NaCl drops three orders of magnitude when increasing the molecular weight of PDADMA from 45 kDa to 72 kDa. To figure out if an immobile PSS fraction exists in the film built from 72 kDa PDADMA (beyond the entanglement limit), the film was annealed at different conditions in article 4: both temperature and salt concentration were varied. For data analysis, the simplest model with two PSS fractions with different diffusion constants was used. These diffusion constants increase as the temperature of the surrounding solution is increased. As assumed in article 3, an immobile PSS fraction exists when annealing at room temperature. At higher annealing temperatures, at least two diffusion processes must be distinguished: the diffusion of the highly mobile PSS fraction through the entire film and a slow PSS fraction, mowing in a limited way. The choice of preparation conditions determines whether a polyelectrolyte multilayer can intermix completely. It is not clear if complete intermixing will ever occur for films built with PDADMA beyond the entanglement limit. It is possible that the diffusion is more complex. Long-term measurements will clarify this question. Calculating scattering length density profiles with subdiffusive behavior would be interesting and is a challenge for the future. Furthermore, immobile fractions are only visible with long annealing times. We hypothesize that an immobile or nearly immobile fraction is present whenever the dependence of D_PSS on the molecular weight of PDADMA cannot be described by the sticky reptation. To verify this hypothesis, further studies are necessary.
All results presented and discussed in the manuscript and articles show that by varying the preparation conditions, tailored films can be built. The composition of the film is also determined by the adsorption kinetics. In addition, the mobility of the PEs within the multilayers can be controlled by varying the conformation, mingling and entanglement of the chains within the film. The influence of the salt concentration in the preparation solution on the growth regimes during film formation is part of our future research. It is planned to investigate films built of different PDADMA molecular weights under varied annealing conditions to better understand the mobile and immobile fractions.