Hydrophilically modified poly(dimethylsiloxane) (HPM-PDMS) bearing quaternized amino groups on the side chains was dissolved in mixtures of methanol (MeOH) and water with a water weight fraction from 0 to 1 and with 0.1 M sodium acetate added. The degree of substitution and the degree of polymerization of this ionomer sample were 16 mol% and 1050, respectively, and the polymer concentrations were mostly <1%. Although the solutions were almost transparent, they were in the two-phase region at , and HPM-PDMS formed random aggregates at . In the two-phase region, the coexisting concentrated phases formed colloidal particles with radii of gyration ranging from 100 to 300 nm just after dispersion. The colloidal particles, however, gradually coagulated, and the solutions became turbid when they were left standing for several days. The multiplet structure in the melt sample of HPM-PDMS may be responsible for the tentative dispersion of HPM-PDMS even in the two-phase region.
Amphiphilic polyelectrolytes are copolymers consisting of ionic and hydrophobic monomer units.1 Their properties strongly depend on the monomer content and sequence. When these copolymers are rich in ionic monomer units, they are often referred to as hydrophobically modified polyelectrolytes, whereas copolymers rich in hydrophobic monomer units are referred to as ionomers. When we consider statistical copolymers, the former copolymers (that is, those rich in ionic monomers) are soluble or dispersible in water and often form polymer micelles in aqueous solutions.2, 3, 4, 5, 6, 7, 8 The latter copolymers (that is, the ionomers), however, hardly dissolve in water, and their solution studies have thus far been carried out mostly in polar organic solvents.9, 10, 11, 12, 13, 14, 15
Poly(dimethylsiloxane) (PDMS) is a typical hydrophobic polymer that is used in release coating materials, adhesive compounds and so on. In recent years, PDMS has been modified by substitutions with various hydrophilic functional groups to impart unique solution, melt and surface properties.16, 17, 18 Such a hydrophilically modified PDMS (HPM-PDMS) is applicable to detergents, surface modifiers, cosmetics, personal skincare products and hair conditioners, metal corrosion inhibitors, and so on.
In this study, we investigated a cationic HPM-PDMS, the chemical structure of which is depicted in Scheme 1. The cationic side groups were introduced randomly, and the degree of substitution x was 0.16. Therefore, our HPM-PDMS sample is an ionomer. Although the hydrophobicity of the PDMS main chain is strong, we found that this HPM-PDMS sample is dispersible in water, methanol (MeOH) and MeOH–water mixtures all containing 0.1 M sodium acetate (NaAc), if the polymer concentration is dilute enough. We have studied the dispersion state as well as the aggregation and phase behaviors of this sample in these solutions using light scattering and small-angle X-ray scattering (SAXS). As expected for ionomers, the dispersion state was strongly dependent on the solvent composition, which is represented in terms of the weight fraction of water in the MeOH–water mixture in this paper. The polyelectrolyte character of the ionomer was much suppressed in our ionomer solutions because of the added salt.
Preparation of the polymer sample and its solutions
A random copolymer sample of dimethylsiloxane and 3-chloropropylmethylsiloxane was purchased from Gelest Inc. (Morrisville, PA, USA). The content of the latter monomer was 16 mol% (determined by 1H-NMR), and the degree of polymerization N0 was 1050 (determined by static light scattering; see below). This Cl-modified PDMS sample (3.95 g including 6.5 mmol of 3-chloropropyl groups) was dissolved in 4 cm3 of a n-butanol/N,N-dimethyleformamide mixture (7.5:2.5 v/v) along with 13.7 mmol of 2-dimethylaminoethanol (Wako Pure Chemical Industries, Ltd, Osaka, Japan), and the solution was heated at 110 °C for 11 h while stirring to quaternize the amino group with the chloropropyl group of the Cl-modified PDMS.18 After evaporation of the volatile fractions, the polymer sample was recovered by reprecipitation from acetone into n-hexane. To remove hydrophilic low-molar-mass impurities including excess amine, the sample was dialyzed against pure water at 25 °C for a week and freeze dried. The dried waxy HPM-PDMS sample that was obtained was dissolved in a small amount of MeOH and dried in a sample vial under vacuum. From the integrated intensities of the 1H-NMR peaks belonging to NCH3 (δ 2.8 p.p.m.) and SiCH3 (δ 0.2 p.p.m.), it was confirmed that all of the chloropropyl groups of the Cl-modified PDMS had reacted with 2-dimethylaminoethanol.
Light scattering and SAXS measurements were made on the HPM-PDMS sample dissolved in MeOH, water and MeOH–water mixtures, all of which included added salt to reduce strong intermolecular electrostatic interactions. To select the proper salt to be added to the HPM-PDMS solutions, solubility tests of various salts were conducted in MeOH, water and an MeOH–water mixture with the water weight fraction . Solubility tests of HPM-PDMS in the three solvents with 0.1 M solutions of various salts added were also conducted. Table 1 summarizes the results of the solubility tests, in which the cation of the salts examined was sodium. Some salts did not dissolve in MeOH, and HPM-PDMS did not dissolve in MeOH or water solutions of some of the salts. On the basis of the results of these solubility tests, NaAc was selected as the added salt for our HPM-PDMS solution study.
The HPM-PDMS sample was directly dissolved in MeOH–water mixtures with different solvent compositions () and containing 0.1 M NaAc and stirred by a magnetic stirrer for 24 h at room temperature. The original solutions, most of which had a polymer concentration of 1.0 wt%, were diluted with the same MeOH–water mixtures containing 0.1 M NaAc to prepare test solutions of different polymer concentrations. The test solutions were filtrated with a 0.50 μm poly(tetrafluoroethylene) membrane filter before the measurements.
Static and dynamic light scattering measurements were performed on the HPM-PDMS solutions at 25 °C using an ALV/SLS/DLS-5000 light scattering instrument (ALV, Langen, Germany) with a Nd:YAG laser operating at 532 nm. All the solutions were almost transparent, and light scattering measurements were carried out within 30 h after preparation. The scattered light intensity did not depend on time during the measurements.
When the solution is dilute enough, the excess Rayleigh ratio Rθ at the scattering angle θ is related to the weight-average molar mass Mw, the z-average particle scattering function P(k) in which k is the magnitude of the scattering vector and the second virial coefficient A2 of the solute by Yamakawa19
where K is the optical constant, c is the polymer mass concentration, and Q(k) is the intermolecular interference factor. From this equation, we have the following relations:
Furthermore, P(k) is related to the z-average radius of gyration 〈S2〉z1/2 by
The refractive index increment ∂n/∂c of HPM-PDMS that is needed to calculate K was determined to be 0.108 (), 0.0869 (0.1), 0.0726 (0.3), 0.0462 (0.5), 0.0531 (0.6), 0.0579 (0.7), 0.0831 (0.9) and 0.0928 (1) cm3 g−1 using differential refractometry at 25 °C. These results were obtained for non-dialyzed solutions. As the refractive indices of water and MeOH are very close and because the composition dependence of the solvent refractive index is weak enough ( is <4%), the preferential adsorption effect on the light scattering results was disregarded.19
Intensity autocorrelation functions obtained using dynamic light scattering were analyzed by the CONTIN method to obtain the hydrodynamic radius RH.
Small-angle X-ray scattering
SAXS measurements were conducted on HPM-PDMS dissolved in MeOH–water mixtures with , 0.7 and 0.9 (all including 0.1 M NaAc) at the BL40B2 beamline of SPring-8 (Hyogo, Japan, proposal no. 2012B1452). The polymer concentration was fixed to be 2 × 10−3 g cm–3, and the SAXS measurements were performed on the solutions ca 5 days after solution preparation. The wavelength of the X-ray, the camera length and the accumulation time were set to be 0.10 nm, 3000 mm and 180 s, respectively. A capillary made of quartz that contained test solutions was set in a heating block set at 25 °C, and the intensity of the scattered X-ray was measured using an imaging plate detector. SAXS measurements were also made on the HPM-PDMS and Cl-modified PDMS samples in melt, injected into capillaries, at the BL-10C beamline in KEK-PF (Tsukuba, Japan, proposal no. 2011G557). A wavelength of 0.15 nm, a camera length of 2000 mm and an accumulation time of 100 s were chosen for this study.
Figure 1 shows the dependence of (Kc/R0)1/2 on polymer mass concentration c in MeOH–water mixtures of different solvent compositions with 0.1 M NaAc added. The data points for (that is, MeOH), 0.1 and 0.3 follow concave curves with negative initial slopes, and the (Kc/R0)1/2 values are lower than the value of 1/M1 1/2, as indicated by the arrow in the figure, where M1 is the molecular weight of the HPM-PDMS sample. (M1=1.04 × 105, calculated from the degree of polymerization of the original Cl-modified PDMS sample). These data indicate that HPM-PDMS forms aggregates in these solvents and that the degree of aggregation increases with (cf. equation (2)) because of the lower affinity of the HPM-PDMS main chain with water. However, at , the data points follow almost straight lines with positive slopes and very small intercepts; this demonstrates the existence of very large aggregates of HPM-PDMS in the MeOH–water mixtures.
The particle scattering functions P(k) of HPM-PDMS in MeOH–water mixtures at and at infinite dilution of the polymer (cf. equation (3)) are shown in Figure 2. (Owing to difficulty in the concentration extrapolation, P(k) were not obtained at .) Strong angular dependences of P(k) at also indicate the existence of large aggregates of HPM-PDMS in the MeOH–water mixtures.
From the intercepts and initial slopes of the plots shown in Figures 1 and 2, we determined the weight-average molar masses Mw, the second virial coefficients A2 and the z-average root-mean-square radii of gyration 〈S2〉z1/2 of the HPM-PDMS aggregates in MeOH–water mixtures with (cf. equations (2) and (4)). The results as well as the weight-average aggregation number mw=Mw/M1 and the hydrodynamic radius RH obtained by dynamic light scattering are listed in Table 2. The ratios 〈S2〉z1/2/RH, which range from 0.9 to 1.3, are larger than that expected for the uniform density sphere, but the deviation may arise from the high dispersity in the molar masses of the aggregates, which increases the ratio.20 If the HPM-PDMS aggregates at exist as uniform density spheres, then we can calculate the polymer mass concentration cin inside the sphere using
The concentration cin at each is listed in the last column of Table 2. The HPM-PDMS aggregate still contains much solvent.
After the light scattering measurements were performed, the test solution of (c=0.01 g cm–3) was kept standing at room temperature. As shown in Figure 3, the turbidity of the solution increased slowly with time. This implies that the phase separation takes place in the solution but that the separated concentrated phase grows very slowly. However, HPM-PDMS solutions of (c=0.01 g cm–3) remained transparent for a long time after the solution preparation.
Figure 4 shows SAXS profiles of HPM-PDMS solutions with , 0.7 and 0.9 in which the polymer concentration was fixed at 2 × 10−3 g cm–3. Excess SAXS intensities I(k) at are much stronger than those at and 0.9. From Guinier’s plots of the I(k) data at and at 0.14 nm−1<k<0.3 nm−1 (data not shown), the radii of gyration without correction of the intermolecular interference effect were estimated to be 3.2–6.5 nm, which were much smaller than that (100 nm) estimated by light scattering. If the solution contains two scattering components of extremely different sizes, then scattering from the larger component and from the smaller component is predominant in the k regions of light scattering and SAXS, respectively. Therefore, from the light scattering and SAXS data, we conclude that the solution with includes not only large aggregates but also a component of HPM-PDMS with small sizes. However, in the solutions with and 0.9, the large aggregates of HPM-PDMS that were detected by light scattering may be the predominant scattering component, and there is no appreciable amount of the small-size component.
Aggregation of HPM-PDMS at
HPM-PDMS has a strongly hydrophobic main chain and quaternary ammonium ions on hydrophilically modified side chains. Therefore, the conformation and aggregation behavior of the HPM-PDMS chain should be determined by the balance between the hydrophobicity of the main chain and the hydrophilicity of the side chains. As demonstrated in Figure 1, HPM-PDMS forms aggregates in MeOH and MeOH–water mixtures with and 0.3 that have 0.1 M NaAc added. This aggregation may occur because of the hydrophobic main chain, but the degree of aggregation may be suppressed by the hydrophilically modified side chains.
As the hydrophobicity is uniform along the main chain of HPM-PDMS, we may not expect the formation of star-like or brush-like polymer micelles by HPM-PDMS. The flower-like micelle may also be excluded because of the difficulty in the formation of its hydrophobic core by the PDMS main chain.
Each HPM-PDMS chain in the aggregate exists as a loose coil or collapsed globule in which ammonium groups may be distributed more or less heterogeneously. In the coil or globule, sections that are poor in ammonium groups may act as binding sites to form aggregates. Here, we assume that HPM-PDMS undergoes the random aggregation in which each chain behaves on average as an f-functional unimer. For such a random aggregate, the weight-average molar mass Mw and the z-average square radius of gyration 〈S2〉z can be written in the forms5, 21
where α is the reacted fraction of the functional groups and b and 〈S2〉1 are the distance between the nearest neighbor unimers and the square radius of gyration of the unimer, respectively, in the aggregate. Assuming the unimers in the aggregate are a uniform density sphere, we use the relation b=2 × [(5/3)〈S2〉1]1/2.
The dependence of the reacted fraction α on the polymer concentration is given by Sato and Matsuda21
where φ is the polymer volume fraction (φ=c where is the polymer partial specific volume: 0.855 cm3 g–1 for PDMS) and Δɛ is the free energy change per single bond formation divided by the thermal energy. (In Sato and Matsuda,21 Δɛ includes a concentration-dependent term, but at the dilute solutions examined in this study this term is negligible.)
Using Mw and 〈S2〉z given by equation (6) as well as the second virial coefficient A2, Kc/Rθ may be calculated using equation (1), in which the third and higher virial terms are neglected. First, we try to fit equation (2) at k=0 to the experimental c dependence of (Kc/R0)1/2 shown in Figure 1. To do so, we need to select three parameters: f, Δɛ and A2. As Mw must be positive, A2 must be smaller than (Kc/R0)/2c (cf. equation (1)); from this equation, the maximum values of A2 were estimated to be 9.1 × 10−5, 1.4 × 10−4 and 8 × 10−6 mol cm3 g–2 at , 0.1 and 0.3, respectively. To obtain the best fit to the experimental c dependence of (Kc/R0)1/2, we had to select slightly smaller values of A2 and then suitable values of f and Δɛ. The best fit of the theoretical (Kc/R0)1/2 is indicated by the solid curves at , 0.1 and 0.3 in Figure 1, and values of f, Δɛ and A2 are listed in Table 3. The negative initial slopes of the three solid curves arise from the increase in Mw (as calculated by equation (6)) with increasing c, which is caused by the aggregation.
Furthermore, angular dependences of (Kc/Rθ)1/2 for solutions with , 0.1 and 0.3, which are shown in Figure 5, are fitted to equation (1) by selecting suitable values of f, Δɛ, A2 and 〈S2〉11/2. The solid lines in Figure 5 are drawn using values of f, Δɛ and A2 that are the same as or similar to those used in the fitting of Figure 1, as well as newly selected values of 〈S2〉11/2 (see Table 3).
In Table 3, the absolute value of Δɛ increases and 〈S2〉11/2 decreases with increasing water content in the solvent. These changes occur because the intermolecular and intramolecular hydrophobic interactions of the HPM-PDMS main chain become stronger with increasing water content. As a result, the mass concentration cin,1 inside the polymer chain forming the aggregate, which is calculated using
increases with the water content (cf. the last column of Table 3). On the other hand, the f values are close to 2, indicating that the branch density of the random aggregate formed by the HPM-PDMS chains is rather low, irrespective of , which may be due to the intermolecular electrostatic repulsion. Ammonium groups may be distributed more on the periphery of the HPM-PDMS chain unimer so that the electrostatic interaction may affect A2 in a different way than it affects 〈S2〉11/2.
Phase separation in the solutions at
As shown in Figure 1, the light scattering behavior of dilute HPM-PDMS solutions is very different at and at . The molar mass and aggregation number of the HPM-PDMS aggregates are very large at (cf. Table 2), implying that a liquid–liquid phase separation takes place in such dilute HPM-PDMS solutions in which the separated concentrated phase may exist as colloidal particles.
When a polymer solution of volume V and mass concentration c is demixed into dilute and concentrated phases with volumes Vd and Vc and mass concentrations cd and cc, respectively, we equate Vd/V and Vc/V to (cc−c)/(cc−cd) and (c−cd)/(cc−cd), respectively, using the lever rule. If the coexisting concentrated phase is dispersed as colloidal particles in the solution, there are two scattering components, the polymer component (component S) in the coexisting dilute phase and the colloidal particles of the coexisting concentrated phase (component L). The mass concentrations cS and cL of the components S and L, respectively, in such a phase-separated solution are given by
and the excess Rayleigh ratio Rθ of a solution that includes the two components is given by Sato et al.22
Here, K is the optical constant, wi, Mi and Pi(k) are the weight fraction of the total polymer (wi=ci/c), the weight-average molar mass, and the z-average particle scattering function of the component i, respectively, and Aij is the second virial coefficient between the components i and j (i, j=S, L).
Colloidal particles of the concentrated phase may be regarded as uniform density spheres with a log-normal distribution of the molar mass M. The particle scattering function PL(k) of the component L is then calculated using23, 24
where RM is the radius of the sphere with the molar mass M, and x is defined by
with σ and M° being defined as
Here, Mw and Mn are the weight-average molar mass (Mw=ML) and number-average molar mass of the colloidal particles, respectively. The radius RM is calculated using
If the polymer chain in the dilute phase takes a random coil conformation, PS(k)∝k−2 in high k regions;25 but the SAXS profile in Figure 4 shows a much stronger k dependence in the intermediate k region (cf. the dotted line with a slope of −6), which indicates that the component S exists also as spherical particles with a size dispersity. Thus, the particle scattering function PS(k) is calculated from equations (11), (12), (13), (14), similarly to PL(k), but with cc in equation (14) replaced by the concentration inside a particle of component S, cin,S. The concentration cin,S may be different from cc in the concentrated phase and may correspond to cin,1 of the aggregate at , defined by equation (8).
At high k, PL(k) diminishes to zero and we can reduce equation (10) to
We determined MS, (Mw/Mn)S, and cin,S by fitting the SAXS data at high k to equation (10′). The thin dashed curve in Figure 4 shows the result, and the parameters chosen are listed in Table 4. As c (=2 × 10−3 g cm–3) was low enough, the dashed curve was not affected by the second virial term in equation (10′); wS cannot be determined because we did not determine the absolute value of I(k) in the SAXS experiment.
The dashed thin curve deviates from the experimental data only at k<0.2 nm−1. Thus, it is difficult to determine uniquely the parameters for component L in equation (10) from only the SAXS profile. We obtained the solid curve in Figure 4 at using the parameter values for the S and L components that are listed in Table 4 and by neglecting the virial terms (that is, ASS=ALL=ASL=0). Although the fit of the solid curve is reasonably good, the parameter values for the component L in Table 4 are not decisive. It is noted, however, that the value of cc used to calculate wL in Table 4 is identical with the value of cin at in Table 2, which was determined from the light scattering results of Mw and RH. (Although Mw in Table 2 is the average molar mass of components S and L, it should be close to the molar mass of component L because wS is considerably small.)
If the HPM-PDMS solution contains the two scattering components S and L at , the c dependence of (Kc/R0)1/2 at , shown in the insert of Figure 1, as well as the experimental result of 〈S2〉z1/2=100 nm at that is listed in Table 2 should be compared with equation (10) combined with equation (9). These light scattering results were reproduced using ML=1.8 × 108 g mol–1, (Mw/Mn)L=2, cd=1 × 10−4 g cm–3, and cc=0.1 g cm–3 as well as ASS=−1.0 × 10−5, ALL=1.3 × 10−7, and ASL=1.0 × 10−5 (in units of mol cm3 g−2), although the fitting results are not shown. As the polymer concentration and the time elapsed after solution preparation were different for the test solutions used in light scattering and in SAXS, the ML is largely different from that listed in Table 4, but the other parameters determined by light scattering and SAXS are consistent. The solid curve in Figure 4 did not change when the A2 values used to fit the light scattering results were substituted into equation (10).
Phase diagram of the ternary system of a polymer, solvent and non-solvent
Many years ago, Tompa26 calculated the ternary phase diagram of a system containing a polymer, solvent and non-solvent using the Flory–Huggins theory.27 His result is schematically illustrated in Figure 6 with the composition of the ternary system specified by the polymer mass concentration c and the weight fraction of the non-solvent (that is, water) in the mixed solvent of our system. A ternary solution with the original polymer concentration coriginal is in the one-phase region of the ternary phase diagram at a low such as 0.3, but it goes into the two-phase region at a of 0.5 or 0.7. At , the original solution indicated by the small filled circle in the phase diagram is separated into the dilute and concentrated phases with the polymer concentrations cd and cc, respectively, indicated by the two small unfilled circles in Figure 6. When increases to 0.7 and 0.9, cd on the bimodal curve in Figure 6 becomes very dilute, which is consistent with the disappearance of the polymer component S in the SAXS profile at and 0.9.
In Table 4, the weight fraction wS of the component S in the dilute phase is as low as 0.15 at and c=2 × 10−3 g cm–3. We can expect an even lower wS at . Therefore, Mw, 〈S2〉z1/2 and RH, which is obtained by light scattering and listed in Table 2, are regarded as good approximations of the values for component L, and cin in the last column of the table can be equated with cc of the coexisting concentrated phase. The polymer concentration cd of the coexisting dilute phase, however, was estimated at by the combination of the SAXS and light scattering data (see above) but was not able to be estimated at because of the essential lack of contribution of component S to the SAXS profile.
Figure 7 shows the dependence of cc on the solvent composition at (filled circles) as well as cd at (a triangle). The filled circles at are actually the results for cin listed in Table 2, which can be equated with cc as mentioned above. From Tompa’s phase diagram (Figure 6), we can expect that cc is a monotonically increasing function of the non-solvent composition but that cc of our ternary system is essentially independent of . Tompa used the Flory–Huggins theory on a system in which the polymer is a non-ionic homopolymer that does not aggregate in the coexisting dilute phase and assumed the three interaction parameters in the ternary system to be constant. In our system, the intermolecular hydrophobic and electrostatic interactions among HPM-PDMS, MeOH and water should depend on the solvent composition, so the interaction parameters may not be constant. As we do not have enough information about the interaction parameters for our ternary system at present, we must postpone the discussion of the disagreement between theory and experiment that is shown in Figures 6 and 7.
At , the HPM-PDMS chain (that is, component S) in the dilute phase of the phase-separated solution aggregates slightly (the aggregation number MS/M1=3) and takes a compact globular conformation with cin,S=0.53 g cm–3 (cf. Table 4). This internal concentration is higher than the concentration inside the unimer in the random aggregate that forms at (cf. Table 3 and unfilled circles in Figure 7) and almost comparable to those for globular proteins (≈0.7 g cm–3).2, 28 The strong hydrophobic interaction of the HPM-PDMS chain at makes cin,S higher.
However, the aggregation number of three of component S at is much lower than the aggregation number Mw/M1 at that is calculated using equations (6) and (7) and the parameters listed in Table 3; for example, Mw/M1=21 at and c=0.002 g cm–3. In the globular state, HPM-PDMS main chains and cationic side chains may be located inside and outside the globule, respectively, as they are in globular proteins in which a ternary structure prevents random aggregation of the chains.
The globular state or the collapsed conformation of a polymer chain in a poor solvent, particularly the system of thermosensitive poly(N-isopropylacrylamide) in hot water, has been studied by many researchers.29, 30, 31 However, the collapse of the polymer chain is usually accompanied by a phase separation that makes it difficult to investigate the globular state of the chain. In this study, we investigated the globular state of the HPM-PDMS chain in the phase-separated solution using SAXS such that the scattering from the concentrated phase droplets was minor because of intra-particle interference.
Dispersibility of HPM-PDMS in MeOH–water mixtures
Test solutions for light scattering and SAXS measurements were prepared by mixing the HPM-PDMS melt sample directly with MeOH–water mixtures. The dispersibility of HPM-PDMS was quite good. However, the solutions with slowly became turbid as time elapsed after dissolution (see Figure 3) and did not return to a transparent state with stirring. This means that the concentrated phase in the solutions at exists as colloidal particles just after dissolution but that the particles coagulate into larger particles and that the coagulation process is irreversible. Thus, we should discuss the origin of the dispersibility of the HPM-PDMS melt sample into MeOH–water mixtures even in the two-phase region.
We examined the bulk structure in the HPM-PDMS melt sample used for the above solution study. Figure 8 shows the SAXS profiles I(k) of the melt samples of HPM-PDMS and Cl-modified PDMS before the hydrophilic modification. Although I(k) for the Cl-modified PDMS is a sharply decreasing function of the magnitude of the scattering vector k, the profile for HPM-PDMS has a peak at k=1.27 nm−1 that corresponds to a characteristic spacing of ca 5.0 nm in the melt sample. Similar SAXS peaks have been observed for many ionomers in the bulk state.32, 33, 34 Eisenberg35 proposed that ions of ionomers exist as multiplets in hydrophobic polymer media and look like reverse flower micelles or flower necklaces.36
When this HPM-PDMS sample is mixed with MeOH–water mixtures, the multiplet and hydrophobic polymer domains may be swollen by water and MeOH, respectively, although the swelling of the hydrophobic polymer domain is not expected at ; the swollen two-domain structure may then be destroyed by stirring to give a colloidal dispersion. As the original multiplet structure in the HPM-PDMS melt sample is nanometers in size, we expect the colloid size just after dispersion to be similar. In other words, the formation of small colloidal particles just after dissolution may reflect the nanometer-sized multiplet structure in the HPM-PDMS melt sample, as demonstrated by the SAXS profile shown in Figure 8.
The colloidal particles of the concentrated phase coagulate slowly to form larger particles. The slowness of the coagulation may be due to the electrostatic repulsion between the colloidal particles.
Dilute solutions of HPM-PDMS dissolved in MeOH–water mixtures with different water weight fractions and with 0.1 M NaAc added were investigated using static and dynamic light scattering and SAXS. At , the system is in the one-phase region, but the HPM-PDMS forms random aggregates in solution. The aggregation number increases with increasing polymer concentration and . However, at , although the solutions are still transparent, they are in the liquid–liquid two-phase region. The phase behavior of the solutions qualitatively obeys the ternary phase diagram of the system of a polymer, a solvent and a non-solvent (cf. Figure 6), but the separated concentrated phase exists as colloidal particles of which the radius of gyration ranges from 100 to 300 nm, and the solutions maintain their transparency for several days. The SAXS profile demonstrates that the melt sample of HPM-PDMS takes on the multiplet structure of ionic groups that is often observed in ionomer samples. This nanometer-size multiplet structure may provide colloid-size droplets of the concentrated phase when the HPM-PDMS melt sample is dissolved in MeOH–water mixtures, even in the two-phase region.
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We thank Professor Yo Nakamua at Kyoto University and Mr K Uramoto and M Kondo at Osaka University for helping with SAXS measurements. This work was partly supported by JSPS KAKENHI grant no. 23350055.
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Okuhara, T., Hashidzume, A., Terao, K. et al. Aggregation and phase separation of hydrophilically modified poly(dimethylsiloxane) in methanol–water mixtures. Polym J 46, 264–271 (2014). https://doi.org/10.1038/pj.2014.3
- colloidal particle
- hydrophilically modified poly(dimethylsiloxane)
- light scattering
- phase separation
- small-angle X-ray scattering