Herein, we report a straightforward technique for the creation of nanoporous polystyrene (PS) films. By preparing PS blend samples with Mws of 600 000 and 600 g mol−1 followed by rinsing with n-heptane, the low Mw component was dissolved and removed to afford a low-density network of high Mw PS. Nanoscale pores are formed as a result of the miscibility and stability of the initial state. The resulting materials were characterized using ellipsometry, atomic force microscopy and scanning electron microscopy. Materials with an effective refractive index as low as 1.1 can be prepared using this approach. The effects of varying the size of the low Mw polymer and the application of low friction surfaces prepared with the nanoporous samples were investigated.
The intrinsically high surface area associated with the internal structure of nanoporous materials endows these materials with a number of desirable properties that, in many cases, can be tuned by varying the degree of porosity. Therefore, nanoporous materials find use in a number of real-world applications including thermal insulation, optical coatings,1 gas separation2/storage3 and chemical adsorption.4, 5 Traditional methods for their preparation include templating6/lithographic techniques,7, 8 the sol–gel method for creation of (extremely) low-density aerogels9 and leaching methods.10 Among these methods, leaching techniques are the most straightforward in their approach but are typically restricted to the use of immiscible materials due to the requirement that a single liquid (solvent) that is a solvent for one component cannot be a non-solvent for the other component. This restriction on immiscible materials leads to porous structures with pore sizes that are determined by the characteristic domain size of microscopic phase separation. A noteworthy exception is block copolymers where immiscible polymer species are grafted to one another through chemical bonds. In this case, the pore sizes are determined by the ordered structure of the copolymers (lamella, cylinder and gyroid), which have domain sizes comparable to the size of the chain.11 The extensive use of block copolymers is limited by their high production costs, and the process involves the destruction of chemical bonds and is not as simple as straightforward leaching methods.
Herein, we describe a novel method for the creation of nanoporous polystyrene (PS) films. The technique exploits the relatively high entropic gain of short chains compared with that of long chains upon dissolution. We choose a solvent where the enthalpic contributions to dissolution are (weakly) unfavorable. Entropic considerations allow for the dissolution of short chains while the long chains remain insoluble. We demonstrate that the morphologies can be tuned by the volume fraction and molecular weight of the low Mw components. In addition, the formation mechanism of the nanoporous structures is explained by the phase inversion model. The nanoporous films can be further combined with chemicals (for example, lubricating oil) to extend their application.
Materials and sample preparation
The polymers used in this study included monodisperse PSs of various different molecular weights (Table 1). First, each PS was dissolved in toluene (HPLC grade, Sigma-Aldrich, St Louis, MO, USA) to prepare PS/toluene solutions with concentrations ranging from 0.5 to 4 wt%. Second, the PS blend solutions were prepared by mixing low Mw and high Mw PS solutions with a low Mw PS solution with a volume fraction (φ) ranging from 0.1 to 0.9. The substrate was a silicon wafer (University Wafer Inc., South Boston, MA, USA, <100> orientation) with the native oxide intact, and this substrate was pre-cut into pieces that were 1 cm × 1 cm in size. Before spin-coating, the pre-cut silicon wafer pieces were rinsed and spin-washed using toluene at least five times.
The PS blend solutions were spin-coated onto pre-cut silicon wafer pieces at a speed of 2500 r.p.m. To avoid potential complications involving segregation of low Mw chains to the free air interface,12 measurements on the as-cast films were performed without prior annealing.
Nanoporous films were prepared by submerging the as-cast films into a 20-ml vial full of n-heptane (HPLC grade, Sigma-Aldrich) for 60 s to dissolve the low Mw PS. After 60 s in the n-heptane bath, the films were removed and rinsed gently with n-heptane five times to remove any low Mw PS that remained in the films. Then, the films were dried using a slow stream of dry N2 gas. The vials with 20 ml of n-heptane were discarded and replaced after being used for five films to limit the build-up of low Mw PS in the heptane bath. It is important to note that variations on this procedure (that is, thickness of blend film, volume of solvent and immersion time) do not result in strong variations in the observed morphology.
To prepare slippery surfaces from nanoporous films, the nanoporous film was prepared on top of the silicon wafer. Then, the lubricating oil was added to the surface of the nanoporous film, and the substrate was tilted to remove excess lubrication oil. Some of the lubrication oil becomes trapped by the nanoporous structure and forms a stable layer. The mass of the substrate was recorded before and after the addition of the lubricating oil to calculate the amount of lubricating oil per area. The lubricating oil was a perfluorinated fluid (that is, DuPont Krytox 100, Dupont, Wilmington, DE, USA, density=1.87 g ml−1 at 0 °C, kinematic viscosity=0.12 cm2 s−1 at 20 °C).
For this measurement, the high Mw polymer that was mentioned above was substituted with a high Mw fully deuterated (d8) chain (PS, Mw=627 000 g mol−1, PDI=1.09). To separate the substrate contributions from the Raman signal of the polymer, quartz windows were used rather than silicon wafers. Aside from these distinctions, which have no effect on the leaching process, the sample preparation was the same as that described above. The Raman spectra were acquired using a Horiba Jobin Yvon HR800 series spectrometer (Horiba, Kyoto, Japan) with an excitation wavelength of 532 nm and a spectral resolution of 0.4 cm−1.
Quartz crystal microbalance
The Quartz crystal microbalance (QCM) measurements were carried out using a Q-Sense D300 system that was equipped with an axial flow chamber (QAFC 302, Q-Sense, Stockholm, Sweden) and an Au sensor (Q-Sense). The PS blend solutions consisted of 600 g mol−1 mixed with 600K g mol−1 (600/600K) with a φ value ranging from 0.1 to 0.9 were spin-coated onto the QCM sensors, resulting in an ~180-nm-thick 600/600K PS blend film on the top of each sensor. The solvent volume in the chamber above the film was 100 μl. The mass change in the PS blend film that was on the top of the sensor was calculated using the Sauerbrey equation:13 Δm=−CΔf, where C is the constant (C=17.7 ng Hz−1 cm−2) for the 5 MHz sensor crystal. The leached mass was determined in situ by the Δf that resulted in a new stable plateau (that is, the frequency no longer changes). Therefore, the measurement time was not limited to the 1 min leaching time used for the samples described above.
Nulling ellipsometry (Exacta 2000 self-nulling ellipsometer; Waterloo Digital Electronics, Waterloo, ON, Canada) was used to measure the optical properties of the nanoporous films. Six or more PS blend films were prepared for each volume fraction with a range of thickness (that is, 30–300 nm) by varying the concentration of the PS blend solutions from 0.5 to 4 wt%. For a single film, the ellipsometry measurement provides two zone-averaged angles (that is, polarizer (P) and analyzer (A)), which are calculated from a simple model using the film thickness and index of refraction. To unequivocally determine the index of refraction for a given volume fraction, P and A are required from films of varying thicknesses (that is, ideally over a wide range of thickness). The single value of the refractive index that best describes all P and A values for a given volume fraction is the index of refraction for that volume fraction.
Atomic force microscopy (AFM, JPK Nanowizard 3, JPK, Berlin, Germany) and scanning electron microscopy (SEM, Zeiss Merlin and ULTRA plus, Zeiss, Oberkochen, Germany) were employed to investigate the surface morphologies (AFM) and cross-sectional structures (SEM). For the SEM sample, a bare silicon wafer was scored on the non-polished side before preparing the sample. After the nanoporous film was prepared on top of the silicon wafer, the sample was immersed in liquid nitrogen. Then, the sample was removed from the liquid nitrogen and cleaved along the scratch line.
Results and Discussion
We investigated the efficiency of the leaching process using two approaches. First, selective deuteration and Raman spectroscopy were employed to determine the efficiency of the leaching process. Deuteration of the high Mw chains shifts their characteristic Raman peaks relative to the non-deuterated chains and provides a method of spectroscopic contrast between the low and high Mw species. In particular, the peak located at 3050 cm−1 in normal PS (associated with phenyl C-H stretch14, 15) shifted to 2290 cm−1 upon deuteration. The relative intensities of these two peaks provide a measure of the relative amounts of the high and low Mw materials. The intensity of the deuterated signal at 2290 cm−1 normalized to the combined intensities of the 2290 and 3050 cm−1 peaks is shown (Figure 1). The as-cast films exhibited a straight line with a slope of 1, as expected. For the leached films, the hydrogenated component was not observed in the Raman spectra for φ larger than 0.3 (see inset for the case of φ=0.5). However, for a low φ of 0.2 and 0.3, a reduced leaching efficiency was observed, and for φ=0.1, no detectable change in the relative intensities of the deuterated/hydrogenated components was observed. Therefore, the low Mw PS at such a low φ is not as easily leached out in the 1 min time frame used for the sample preparation as it is at higher volume fractions.
A second technique to measure the leaching efficiency involves direct mass loss detection with the QCM. QCM is a straightforward method for measuring the efficiency of the leaching process (Figure 2). In this case, the contrast between the low and high Mws is provided by their differential solubility in n-heptane. Upon exposure to n-heptane, the low Mw component of the PS blend film dissolves, and the resulting mass of the PS film changes. This mass change can be directly monitored by the change in the resonance frequency of the QCM sensor. The low Mw PS leached fraction can be determined by combining the bulk PS density of 1.05 g ml−1,18 the thickness of the PS blend film before leaching, and the mass change in the PS blend film after leaching. The low Mw PS leached fraction increases with increasing φ and follows the trend of the ideal leached fraction. Therefore, n-heptane can penetrate into the PS blend film to dissolve the low Mw PS. An interesting difference was observed between these two measures of the leaching efficiency. For the ex situ films measured using Raman spectroscopy, less than ideal leaching efficiency was obtained for low values of φ but the QCM measurements indicate ideal efficiency over the entire range of φ. This difference can be explained by examining the dissolution kinetics. The inset of Figure 2 shows the average lifetime for the dissolution of the low Mw component as a function of φ. For smaller values of φ, the lifetime is significantly larger than the 1 min time used in the first method. Therefore, the blend samples in Figure 1 are not exposed to n-heptane sufficiently long for complete dissolution of the low Mw component.
The AFM images (Figure 3) show the surface morphologies with increasing φ values. All these surface structures exhibit significant differences from a clean PS surface. In all cases, the surface appears porous but with no monotonic changes in the structure observed as φ changes. Although AFM provides a wealth of information regarding the surface structure of the film, it provides little to no information on the depth, extent or connectivity of the internal porous structures. However, the pore structure does appear on a length scale that is much smaller than the wavelength of optical light. This result suggests that we should observe specular reflection rather than scattering of light; therefore, ellipsometric techniques can be employed.
The average index of refraction of the film can be determined using ellipsometry. From the index of refraction, the Lorentz–Lorenz relationship (Equation 1) can be used to calculate the average density of the film and infer the amount of free space in the internal structure. Here, ρ is the density and n is the index of refraction. All ellipsometric measurements were performed within the context of an approximation where we assume that the film has a uniform thickness and uniform refractive index. In practice, this assumption will hold for internal structures on a length scale that is significantly smaller than the wavelength used in this study (that is, 633 nm).
In Figure 4a, the measured index of refraction is plotted as a function of φ for both the cast and leached films. For all φ, the cast films are described by a single value of the index of refraction (that is, ~1.57). Because no porous structures formed inside the cast films, the average densities are the same as that of neat PS and exhibit the same index of refraction. For the leached films, the index of refraction decreased with increasing φ, which indicates that the average density decreased. In the simplest picture, when the low Mw PS is leached from the PS blend, the volume that had been occupied by the low Mw PS is replaced by air, which results in the formation of porous structures. The details of the pore shapes and sizes are determined by the diffusive processes that occur while the film is immersed in heptane. As a result of this decrease in the density and refractive index, the measured P and A values of the leached film will exhibit significantly different behavior from that of the cast film (Figure 4b). In particular, for φ>0.3, significant changes in the apparent refractive index were observed. Notably, for the highest volume fraction (that is, φ=0.9), the refractive index was only n=1.15. In addition, these highly porous structures can be quite fragile. For example, after submerging the cast film into the n-heptane bath, the film should be gently rinsed with the n-heptane. If the sample is spin-washed at high speeds, the porous structures collapse.
Although AFM can determine the surface structure on small length scales and ellipsometry provides insight into properties averaged over large length scales, neither of these techniques is able to provide details regarding the nature of the pores throughout the sample. SEM was used to investigate and compare the leached films at φ=0.2, 0.5 and 0.8 (Figure 5). As previously mentioned, the samples used for the SEM studies were cleaved to provide a real cross-sectional image of the nanoporous sample. Based on the cross-sectional SEM images (Figure 5), porous structures were formed in all the leached films for φ=0.2, 0.5 and 0.8. The average size of the pores decreased as φ increased. The porous structures for φ=0.5 and 0.8 were more uniform than the porous structures at φ=0.2. For the film with φ=0.2, pores with size greater than 1 μm were observed. For samples with these pores, any incident light was strongly scattered. Therefore, in this case, ellipsometry is not a useful tool for investigating the film properly, and the same index of refraction for the cast and leached films is obtained. In addition, the reduced leaching efficiency (Figure 1) at low φ does not completely inhibit the formation of nanoporous structures (Figure 5a). As φ increased, the size of the pores decreased, and for φ=0.8, the pores were ~100 nm in size.
The solubility of PS in n-heptane strongly depends on the Mw of the polymer. This may have a significant impact on the ability of these binary blends to form nanoporous structures. Therefore, we investigated the effect of varying the molecular weight of the low Mw component (Figure 6) while maintaining a fixed volume fraction at φ=0.5. These samples were studied with ellipsometry in the same manner as those in Figure 4, where multiple films over a range of thickness were used to determine the refractive index of the nanoporous material. For each Mw, these measurements were performed on both the as-cast and leached films. The resulting measured P and A values were used to calculate the refractive index of that particular blend. As expected, the indices of refraction for all the as-cast films were consistent with that of bulk PS. Leached films with low Mw <2000 g mol−1 possessed a refractive index of ~1.3. At a Mw of ~2000 g mol−1, the apparent refractive index abruptly changes to the bulk value. Analogous to the case for small φ, which also exhibits a bulk-like apparent refractive index, SEM was employed to study the samples. The cross-sectional SEM images (Figure 7) show a dense layer near the free surface which is gradually formed with the molecular weight of low Mw component increasing and the rest of the films with pores, some of them larger than 1 μm. For the 2500/600K PS blend films, both the dense layer and porous structure layer with a thickness of ~100 nm were observed in the leached film (Figure 7c). The four-layer model (that is, silicon wafer/SiO2/porous PS/dense PS layer) consisted of a 100-nm-thick dense layer with a refractive index of 1.57 and a porous layer with a refractive index of 1.30, and a varying thickness was applied to simulate the ellipsometric results. The model with an additional dense layer exhibited a similar refractive index as that of the bulk PS in the leached film (that is, 2500/600K) (Figure 6, inset). Therefore, the porous microstructures prevent the use of ellipsometry. In the first case, for micron size pores, the amount of scattering may lead to unreliable ellipsometry measurements. Second, even if ellipsometry measurements were possible, modeling indicated that it may not be possible to distinguish between a porous layer with a bulk-like coating and a simple bulk-like film (with a smaller thickness).
In the preceding sections, we introduced a simple method for the creation of nanoporous PS films and characterized the resulting structures. This technique exploits the much larger entropic gain for the dissolution of short chains relative to long chains. By choosing an initial blend system consisting of low and high Mw PSs, our initial system was completely miscible and stable under ambient conditions. By subsequently exposure to a weakly unfavorable solvent (that is, n-heptane), the low Mw material was removed from the system, leaving behind a porous high Mw film. The method can be generally classified as a leaching technique for producing porous systems. The novel aspect of this technique is that the initial system is miscible and stable, and nanoscale pores are found as a result. The technique is similar to phase inversion methods that are commonly used for the production of gas separation membranes.19, 20 There, the underlying principle is to induce microphase separation upon exposure of a polymer/solvent film to a non-solvent. Depending upon the relative volatilities, (non)solvent quality and details of the non-solvent exposure, a range of porous structures can be produced.21, 22 In fact, extensive theoretical studies have been focused on understanding the processes that lead to pore formation in phase inversion processes.23, 24 In particular, Cohen et al.24 developed a diffusion-based model considering the flux of solvent/non-solvent molecules upon immersion of a polymer/solvent film in a non-solvent bath. As the concentration gradient of the solvent/non-solvent molecules equilibrates, the system moves along a trajectory within the polymer/solvent/non-solvent ternary phase space. Upon crossing the spinodal line, a single-phase system is no longer stable, and phase separation spontaneously occurs, leading to pore formation. Our system is the same in principle, with stable low Mw chains serving as the solvent component and n-heptane acting as the non-solvent.
As an example of the general applicability of nanoporous polymers and a test of this particular process, we investigated the formation of ‘slippery surfaces’. In general, two factors are employed to characterize slippery surfaces including (1) a very low contact angle hysteresis, which is the difference between the advancing and receding contact angles and (2) a very low sliding angle, which is the surface tilt required for drop motion.25, 26 The contact angle hysteresis of water and ethylene glycol droplets is much smaller on our slippery surface (substrate 1) than that on substrates 2 and 3 (Figure 8 and Table 2). The results in Figure 9 indicate that the droplet sliding angle on our slippery surface follows the trend of unit lubricant amount dependent sliding angle reported in the literature.27 These results demonstrate the nanoporous film can trap the lubricating oil and form a slippery surface.25, 26
In summary, we demonstrated that our novel method can easily provide nanoporous structures for most volume fraction (φ) values in a short period of time. The effective material properties due to the porosity of the nanoporous films were investigated using ellipsometry and discussed in terms of the index of refraction. As the value of φ increased, the index of refraction decreased and reached a value as low as 1.1 for the high φ samples. The morphologies of the internal structures can be tuned by changing the φ or the molecular weight of the low Mw component. The as-prepared nanoporous films can be treated with lubricating oil to form ‘slippery surfaces’. Although we have presented the technique using PS/n-heptane, we believe our approach can be applied to almost any polymer system for which a solvent can be found for the low Mw version, which is a non-solvent for the same polymer at high Mw.
Foss, C. A., Hornyak, G. L., Stockert, J. A. & Martin, C. R. Optical-properties of composite membranes containing arrays of nanoscopic gold cylinders. J. Phys. Chem. 96, 7497–7499 (1992).
de Vos, R. M. & Verweij, H. High-selectivity, high-flux silica membranes for gas separation. Science 279, 1710–1711 (1998).
Germain, J., Fréchet, J. M. J. & Svec, F. Nanoporous polymers for hydrogen storage. Small 5, 1098–1111 (2009).
Schneider, K. & van Gassel, T. J. Membrandestillation. Chemie Ing. Tech. 56, 514–521 (1984).
Eustache, H. & Histi, G. Separation of aqueous organic mixtures by pervaporation and analysis by mass spectrometry or a coupled gas chromatograph-mass spectrometer. J. Memb. Sci. 8, 105–114 (1981).
Hulteen, J. C. & Martin, C. R. A general template-based method for the preparation of nanomaterials. J. Mater. Chem. 7, 1075–1087 (1997).
Chu, S.-Z., Wada, K., Inoue, S., Isogai, M. & Yasumori, A. Inside Front Cover: Fabrication of Ideally Ordered Nanoporous Alumina Films and Integrated Alumina Nanotubule Arrays by High-Field Anodization (Adv. Mater. 17/2005). Adv. Mater. 17, 2115–2119 (2005).
Lee, W., Ji, R., Gösele, U. & Nielsch, K. Fast fabrication of long-range ordered porous alumina membranes by hard anodization. Nat. Mater. 5, 741–747 (2006).
Tillotson, T. M. & Hrubesh, L. W. Transparent ultralow-density silica aerogels prepared by a two-step sol-gel process. J. Non Cryst. Solids 145, 44–50 (1992).
Lee, J., Hirao, A. & Nakahama, S. Polymerization of monomers containing functional silyl groups. 5. Synthesis of new porous membranes with functional groups. Macromolecules 21, 274–276 (1988).
Zhao, D., Feng, J., Huo, Q., Melosh, N., Fredrickson, G., Chmelka, B. & Stucky, G. Triblock copolymer syntheses of mesoporous silica with periodic 50 to 300 angstrom pores. Science 279, 548–552 (1998).
Hariharan, A., Kumar, S. K. & Russell, T. P. A lattice model for the surface segregation of polymer chains due to molecular weight effects. Macromolecules 23, 3584–3592 (1990).
Sauerbrey, G. Verwendung von Schwingquarzen zur Wagungdiinner Schichten und zur Mikrowagung. Z. Phys. 155, 206–222 (1959).
Köhler, A., Khan, A. L. T., Wilson, J. S., Dosche, C., Al-Suti, M. K., Shah, H. H. & Khan, M. S. The role of C-H and C-C stretching modes in the intrinsic non-radiative decay of triplet states in a Pt-containing conjugated phenylene ethynylene. J. Chem. Phys. 136 (2012).
Holinga, G. J., York, R. L., Onorato, R. M., Thompson, C. M., Webb, N. E., Yoon, A. P. & Somorjai, G. A. An SFG study of interfacial amino acids at the hydrophilic SiO2 and hydrophobic deuterated polystyrene surfaces. J. Am. Chem. Soc. 133, 6243–6253 (2011).
Prystupa, D., Anderson, A. & Torrie, B. H. Raman and infrared study of solid benzyl alcohol. J. Raman Spectrosc. 25, 175–182 (1994).
Bergner, G., Albert, C. R., Schiller, M., Bringmann, G., Schirmeister, T., Dietzek, B., Niebling, S., Schlücker, S. & Popp, J. Quantitative detection of C-deuterated drugs by CARS microscopy and Raman microspectroscopy. Analyst 136, 3686–3693 (2011).
Brandrup, J. & Immergut, E. H. Polymer Handbook, (John Wiley and Sons, New York, NY, USA, 1989).
Koros, W. J. & Fleming, G. K. Membrane-based gas separation. J. Memb. Sci. 83, 1–80 (1993).
Guillen, G. R., Pan, Y., Li, M. & Hoek, E. M. V. Preparation and characterization of membranes formed by nonsolvent induced phase separation: a review. Ind. Eng. Chem. Res. 50, 3798–3817 (2011).
Smolders, C. A., Reuvers, A. J., Boom, R. M. & Wienk, I. M. Microstructures in phase-inversion membranes. Part 1. Formation of macrovoids. J. Memb. Sci. 73, 259–275 (1992).
Radovanovic, P., Thiel, S. W. & Hwang, S.-T. Formation of asymmetric polysulfone membranes by immersion precipitation. Part II. The effects of casting solution and gelation bath compositions on membrane structure and skin formation. J. Memb. Sci. 65, 231–246 (1992).
Altena, F. W. & Smolders, C. A. Calculation of liquid liquid-phase separation in a ternary-system of a polymer in a mixture of a solvent and a nonsolvent. Macromolecules 15, 1491–1497 (1982).
Cohen, C., Tanny, G. B. & Prager, S. Diffusion-controlled formation of porous structures in ternary polymer systems. J. Polym. Sci. Polym. Phys. Ed. 17, 477–489 (1979).
Wong, T.-S., Kang, S. H., Tang, S. K. Y., Smythe, E. J., Hatton, B. D., Grinthal, A. & Aizenberg, J. Bioinspired self-repairing slippery surfaces with pressure-stable omniphobicity. Nature 477, 443–447 (2011).
Chen, W., Fadeev, A. Y., Hsieh, M. C., Öner, D., Youngblood, J. & McCarthy, T. J. Ultrahydrophobic and ultralyophobic surfaces: some comments and examples. Langmuir 15, 3395–3399 (1999).
Yao, X., Hu, Y., Grinthal, A., Wong, T.-S., Mahadevan, L. & Aizenberg, J. Adaptive fluid-infused porous films with tunable transparency and wettability. Nat. Mater. 12, 529–534 (2013).
Financial support from the Natural Sciences and Research Council of Canada is gratefully acknowledged. The research at the Perimeter Institute is supported by the Government of Canada through Industry Canada and the Province of Ontario through the Ministry of Economic Development and Innovation. JAF is grateful for the funding provided by the Paris Sciences Chair of the ESPCI, Paris, France.
The authors declare no conflict of interest.
About this article
Cite this article
Lin, FY., Daley, C., Flannery, J. et al. Nanoporous polystyrene prepared via the selective removal of the low Mw component in polystyrene blends. Polym J 48, 983–990 (2016). https://doi.org/10.1038/pj.2016.68