- NANO PERSPECTIVES
- Open Access
Nanoparticle Network Formation in Nanostructured and Disordered Block Copolymer Matrices
© The Author(s) 2010
- Received: 23 July 2010
- Accepted: 23 August 2010
- Published: 14 September 2010
Incorporation of nanoparticles composed of surface-functionalized fumed silica (FS) or native colloidal silica (CS) into a nanostructured block copolymer yields hybrid nanocomposites whose mechanical properties can be tuned by nanoparticle concentration and surface chemistry. In this work, dynamic rheology is used to probe the frequency and thermal responses of nanocomposites composed of a symmetric poly(styrene-b-methyl methacrylate) (SM) diblock copolymer and varying in nanoparticle concentration and surface functionality. At sufficiently high loading levels, FS nanoparticle aggregates establish a load-bearing colloidal network within the copolymer matrix. Transmission electron microscopy images reveal the morphological characteristics of the nanocomposites under these conditions.
- Block copolymer
- Colloidal network
- Nanostructured polymer
- Fumed silica
- Colloidal silica
Block copolymers remain one of the most extensively studied classes of polymers due to their innate ability to infuse the dissimilar properties of homopolymers into a single material by spontaneously self-organizing at the molecular level. Molecular self-assembly is a direct consequence of thermodynamic incompatibility between the contiguous sequences comprising a block copolymer and results in the formation of (a)periodic nanoscale morphologies that can be tailored for diverse (nano)technologies [1, 2]. Ordered morphologies observed in simple AB diblock copolymers include A(B) spheres on a body- or face-centered cubic lattice in a B(A) matrix, A(B) cylinders on a hexagonal lattice in a B(A) matrix, triply periodic bicontinuous channels or alternating lamellar sheets. Targeted addition of a selective low-molar-mass solvent or relatively low-molecular-weight homopolymer to an ordered block copolymer can be used to preferentially swell one of the domains comprising the copolymer nanostructure and ultimately yield tunable transitions to morphologies with specific mechanical or spatial properties [3–8]. Recent studies have extended this general design paradigm by modifying ordered block copolymers with surface-functionalized inorganic nanoparticles to achieve hybrid nanocomposites. Unlike conventional nanocomposites prepared from homopolymers, block copolymer nanocomposites rely on the existing copolymer nanostructure to template—that is, spatially modulate—the nanoparticles.
Previous experimental studies [8–12] of block copolymer nanocomposites have focused on the precise positioning of nanoparticles within the copolymer nanostructure for use in optics, such as waveguides. Such efforts have demonstrated that, if sufficiently small with respect to the host copolymer molecules (i.e., the characteristic size of the copolymer nanostructure), nonselective nanoparticles tend to distribute uniformly throughout the copolymer matrix in much the same fashion as nonselective solvent molecules. Selective nanoparticles, on the other hand, tend to locate along the interface separating adjacent domains within the copolymer nanostructure due to interfacial energy considerations, which result in fewer contacts between A and B repeat units. Larger selective nanoparticles are enthalpically driven to the core of the compatible domains to minimize repulsive contacts with incompatible blocks. Surface-functionalized nanoparticles have likewise been incorporated into ordered block copolymers to promote changes in morphology [13–15], as well as changes in phase behavior [16–18] discerned from the order–disorder transition (ODT). We have recently demonstrated  that the ODT of a poly(styrene-b-methyl methacrylate) (SM) diblock copolymer modified with surface-functionalized fumed silica (FS) or native (hydroxyl-terminated) colloidal silica (CS) decreases monotonically with increasing nanoparticle loading. If, however, oligostyrene-functionalized CS is added to the copolymer, the ODT increases slightly before dropping, in qualitative agreement with self-consistent field predictions.
The objective of the present work is to examine how the mechanical properties of such block copolymer nanocomposites evolve as the concentration of surface-functionalized FS and native CS is systematically increased. Dynamic melt rheology is employed to investigate the mechanical properties, and transmission electron microscopy (TEM) is used to examine the morphology of one of the nanocomposites.
The SM copolymer was synthesized via sequential living anionic polymerization of the S block in cyclohexane at 60°C, followed by the M block in tetrahydrofuran at −78°C, with sec-butyllithium as the initiator. According to proton nuclear magnetic resonance (1H NMR) spectroscopy and size-exclusion chromatography (SEC), the block masses measured 13,000 each, with an overall polydispersity of 1.05. Three grades of functionalized FS were obtained in powder form from Degussa Corp. (Parsippany, NJ) and probed the effects of hydrophilicity versus hydrophobicity and block selectivity: hydroxyl-terminated (OH), methacrylate-terminated (MA) and octyl-terminated (C8). According to the manufacturer, the primary particle size in each case was ~12 nm. The CS nanoparticles with an average diameter of 10–15 nm were provided as a suspension (20% solids) in dimethylacetamide by Nissan Chemicals (Houston, TX). Specimens for dynamic melt rheology were produced by ultrasonicating the nanoparticles (at a specimen-specific concentration relative to the copolymer) for 30 min in toluene to achieve a satisfactory dispersion, followed by copolymer dissolution and further ultrasonication, and then air- and vacuum-drying, all performed at ambient temperature. No copolymer degradation due to ultrasonication was detected according to SEC analysis of the resultant films.
Dynamic rheology was performed on an ARES strain-controlled rheometer equipped with serrated 8 mm parallel plates and operated at 2% strain amplitude to ensure linear viscoelasticity. Disks measuring 8 mm in diameter and 1 mm thick were melt-pressed at 150°C and heated to 220°C under nitrogen. Frequency (ω) spectra were acquired at discrete temperatures above and below the ODT, while isochronal temperature sweeps were performed at ω = 1 rad/s and a cooling rate of 1°C/min under a nitrogen purge to avoid oxidative degradation. Specimens for TEMT were prepared by sectioning the glassy nanocomposites at ambient temperature. Electron-transparent sections measuring ca. 150 nm thick were subjected to the vapor of 0.5% RuO4(aq) to selectively stain the styrenic units. Serial TEM tilt images were collected on a Gatan UltraScan 4000 CCD camera at a resolution of 0.76 nm/pixel and tilt angles ranging from −69° to +69° at an angular interval of 1.5° on a Technai T20 microscope operated at 200 kV. While the full tilt series was aligned using a pre-calibrated geometric model based on a high-precision goniometer stage , only representative images acquired at 0°, 15° and 30° are reported herein.
These results immediately indicate that the fumed nanoparticles, which exist as branched aggregates commonly measuring on the order of hundreds of nanometers, have a more pronounced effect on the SM copolymer than do CS nanoparticles. Specifically, G′ measured for the nanocomposites with FS consistently exceeds the dynamic loss modulus (G″) over the entire temperature interval examined, even though the copolymer exists as a structureless melt. In contrast, G′ for the CS-containing nanocomposite increases beyond G″ only at low temperatures. Close examination of the data in this figure also reveals that (1) the ODT of the copolymer in the SM/CS nanocomposite persists in the vicinity of 172°C, which constitutes a 14°C reduction in the ODT of the copolymer and (2) a second, less pronounced event appears to occur in the SM/FS nanocomposites at ca. 204°C. This second event is absent in the neat copolymer, as well as in the system modified with CS, whereas neither SM/FS nanocomposite exhibits a discernible ODT. Similar disappearance of the ODT is observed  in the case of nanocomposites modified with C60 buckyballs. Over the range from 160 to 200°C, the dynamic moduli measured from the SM-based nanocomposites described in Fig. 1 are well behaved and permit direct assessment of modulus enhancement as functions of nanoparticle concentration and surface chemistry below and above the copolymer ODT.
In Fig. 2b, tanδ, a direct measure of liquid- versus solid-like behavior, is provided as a function of nanoparticle concentration and shows that, up to the concentration where G′ suddenly increases in Fig. 2a, tanδ is, for the most part, greater than unity. Since tanδ = G″/G′, this observation indicates that the nanocomposite behaves liquid-like. At higher nanoparticle concentrations, tanδ decreases below unity, and the material behaves more solid-like. While there is little systematic variation among the three surface-functionalized FS grades, the SM/CS nanocomposites exhibit the greatest liquid-like tendency, marginally behaving solid-like at 20 wt% CS. As before, similar results are seen in Fig. 2d, which displays tanδ as a function of nanoparticle concentration at 200°C, above the copolymer ODT. Solid-like behavior becomes evident at nanoparticle loading levels that correspond to the sharp rise in G′. The one series that deviates from the data previously discussed with regard to Fig. 2b consists of the SM/FS-C8 nanocomposites. According to Fig. 2d, tanδ for this series attains the highest tanδ value measured (15.5 at 0.1 wt%) in this study and thus exhibits the greatest liquid-like behavior of all the nanocomposites investigated. As the concentration of FS-C8 is increased, however, values of tanδ for this series become comparable to those measured for the other FS, as well as CS, series.
When the concentration of FS-C8 is increased to 10 wt%, the frequency spectra change dramatically from the one displayed in Fig. 3a. In Fig. 3b, G′ is greater than G″ over the entire ω range examined, although both are frequency dependent. These data are reminiscent of weak gel-like materials possessing a long relaxation time [24–27]. In the disordered SM copolymer matrix at 200°C (Fig. 3c), we notice a remarkable behavior: G′ continues to exceed G″, remaining parallel at high ω (with G′ and G″ scaling as ω0.35) but starting to show evidence of a plateau at low ω. The presence of a low frequency plateau in G′ suggests that this material is more gel-like than any of the others [25, 27–29]. Interestingly, the modulus of this sample is lower than that of the specimen portrayed in Fig. 3b. These results taken together suggest the presence of a sample-spanning, self-supporting network within the disordered copolymer melt. In the ordered state, the nanocomposite possesses a higher modulus, but an apparently weaker FS network (due possibly to network disruption upon copolymer ordering). Since this is the least effective modifier of the FS family, it immediately follows that the other additives exhibit comparable, if not more pronounced, network behavior at nanoparticle concentrations of 10 wt% or more.
It is apparent, however, from the tilt images corresponding to the nanocomposite with 5 wt% FS-MA that the copolymer lamellae are not highly oriented due, in large part, to the presence of the nanoparticles. Moreover, in several locations throughout the field of view, the lamellae appear distorted or even discontinuous (cf. the circled region at 30° tilt), which is consistent with our previous phase study  indicating that the stability of the copolymer nanostructure (discerned from the magnitude of the ODT) in this nanocomposite is lower than that of the neat copolymer. In the case of the nanocomposite containing 20 wt% FS-MA, however, the lamellar nanostructure of the copolymer is altogether eliminated, replaced by a continuous background of nearly constant optical density, whereas the FS-MA nanoparticles form a continuous network that extends throughout the material. These results agree with our findings from dynamic rheology: (1) no ODT is discernible from isochronal temperature sweeps of this nanocomposite and (2) this nanocomposite exhibits solid-like behavior both at low and high temperatures in the melt. Thus, we provide experimental evidence to demonstrate that incorporation of nanoparticles in block copolymer melts can induce sufficient molecular frustration via nanoscale confinement to completely thwart the ability of the copolymer molecules to form a periodic nanostructure.
Addition of native and surface-functionalized siliceous nanoparticles varying in hydrophobicity and inherent aggregation to a nanostructured block copolymer melt has little effect on the rheological properties at low nanoparticle concentrations, but promotes an abrupt increase in G′ and a corresponding decrease in tanδ (below unity) at high nanoparticle loading levels. In this latter regime, the nanocomposite melt behaves solid-like at temperatures above and below the copolymer ODT, suggesting that a colloidal network composed of nanoparticles develops. Existence of such a network is confirmed from mechanical frequency spectra acquired at different nanoparticle concentrations and temperatures. Transmission electron microscopy provides direct visual evidence of a clustered nanoparticle network  within the ordered copolymer nanostructure and establishes that two dissimilar nanostructures, both capable of imparting solid-like behavior to soft materials, can coexist in block copolymer nanocomposite melts .
This work was supported by the Research Council of Norway under the NANOMAT Program. M. K. G. expresses her gratitude for a GEM Fellowship and a NOBCChE Procter & Gamble Fellowship.
This article is distributed under the terms of the Creative Commons Attribution Noncommercial License which permits any noncommercial use, distribution, and reproduction in any medium, provided the original author(s) and source are credited.
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