Enhanced Mechanical Properties of Polymer ... - ACS Publications

Letter Cite This: ACS Macro Lett. 2018, 7, 962−967

pubs.acs.org/macroletters

Enhanced Mechanical Properties of Polymer Nanocomposites Using Dopamine-Modified Polymers at Nanoparticle Surfaces in Very Low Molecular Weight Polymers Na Kyung Kwon,† Hyunhong Kim,† Im Kyung Han,† Tae Joo Shin,‡ Hyun-Wook Lee,† Jongnam Park,*,† and So Youn Kim*,† School of Energy and Chemical Engineering and ‡UNIST Central Research Facilities and School of Natural Science, Ulsan National Institute of Science and Technology (UNIST), 50 UNIST-gil, Ulsan 44919, Republic of Korea

Downloaded via AUSTRALIAN NATL UNIV on July 25, 2018 at 08:03:47 (UTC). See https://pubs.acs.org/sharingguidelines for options on how to legitimately share published articles.

†

S Supporting Information *

ABSTRACT: While incorporation of nanoparticles in a polymer matrix generally enhances the physical properties, effective control of the nanoparticle/polymer interface is often challenging. Here, we report a dramatic enhancement of the mechanical properties of polymer nanocomposites (PNCs) using a simple physical grafting method. The PNC consists of low molecular weight poly(ethylene glycol) (PEG) and silica nanoparticles whose surfaces are modified with dopaminemodified PEG (DOPA-mPEG) brush polymers. With DOPAmPEG grafting, the nanoparticle surface can be readily altered, and the shear modulus of the PNC is increased by a factor of 105 at an appropriate surface grafting density. The detailed microstructure and mechanical properties are examined with small-angle X-ray scattering (SAXS) and oscillatory rheometry experiments. The attractive interactions between particles induced by DOPA-mPEG grafting dramatically improve the mechanical properties of PNCs even in an unentangled polymer matrix, which shows a much higher shear modulus than that of a highly entangled polymer matrix.

W

In this Letter, we investigate the microstructure and rheological properties of low MW PNC, where the dopamine-modified, brush-type polymer was employed as a physical grafting agent. Dopamine molecules are well-known to adsorb on many substrates via strong H-bonding, readily modifying the surface properties.20−23 Here we found that a simple physical grafting of dopamine-modified methylated poly(ethylene glycol) (DOPA-mPEG) polymer onto silica NPs can dramatically improve the mechanical properties of low MW PNCs. The detailed microstructure and rheological information on PNCs was obtained with small-angle X-ray scattering (SAXS) and oscillatory rheometry experiments, while the surface coverage density, σ, of dopamine-modified polymers was systematically varied. Our study revealed that the grafted dopamine-modified polymer can (i) increase the effective volume of NPs, (ii) bring strong interactions between grafted and matrix polymer at the interface, and thus, (iii) create networked superstructures. These combined effects tremendously increased the modulus of low MW PNCs comparable to that of high MW PNCs.

hile nanoparticles (NPs) are frequently incorporated into polymer matrix to enhance the mechanical, electrical, and rheological properties, controlling the interface of NP/polymer matrix is often challenging because of the intrinsic incompatibility between particle and polymer.1−7 Numerous studies have been dedicated to understanding the NP/polymer interactions at the interface and resulting NP dispersions8,9 and have found that physical/chemical grafting of polymer onto NPs can effectively tune particle interactions, where grafting density, size, and morphology of NPs and polymer molecular weights (MWs) are key parameters.2,10−19 Chemical grafting of polymers onto NPs seemed to be the most effective method to ensure a favorable interaction between NPs and polymers; however, it generally requires complicated synthesis and purifications, increasing the number of processing steps.1,17 Physical grafting can be an alternative; however, it is relatively weak, unstable and often difficult. In polymer nanocomposites (PNCs), the use of high MW polymer is generally preferred because polymer entanglements improve the mechanical property of PNC.3,14 While high MW polymers with entanglements may provide good adsorption stability onto NPs, the good dispersity and resulting enhanced properties are not always guaranteed because the increasing MW can drive additional bridging or depletion aggregation.12,19 Furthermore, the dramatic increase of viscosity with MW significantly decreases processability. © XXXX American Chemical Society

Received: June 27, 2018 Accepted: July 20, 2018

962

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967

Letter

ACS Macro Letters DOPA-mPEG grafted silica NPs were first prepared by mixing DOPA-mPEG with silica NPs in aqueous solutions with vigorous stirring for several hours, where σ of DOPAmPEG was controlled by changing the mixing ratio. Then, PNCs were prepared by adding the necessary amount of PEG (average Mn = 400 g/mol), followed by annealing at 70 °C in a vacuum oven for 2 days. The particle diameter, D, was around 35 nm and the particle volume fraction, ϕc, was varied from 0 to 0.48. More experimental details are provided in the Supporting Information (SI). Figure 1a shows the surface chemistry of bare and DOPAmPEG grafted silica NPs. The grafting of DOPA-mPEG on

Figure 2. Experimental scattering intensity, I(qD), of silica NPs in PNCs are plotted as a function of normalized wavevector, qD, with varying rσ of DOPA-mPEG at (a) ϕc = 0.07, (b) 0.17, and (c) 0.38. Insets are the corresponding structure factor, S(qD). (d) The change of the first peak positions, q*D, is plotted with rσ for different ϕc. All samples were measured at 75 °C.

electron density of silica than that of DOPA-mPEG and PEG matrix. The details of the SAXS analysis are found in the SI. At ϕc = 0.07, no substantial change of particle structures was found with DOPA-mPEG grafting; all scattering intensities resemble the particle form factor, P(qD), shown in Figure 2a, and thus, the structure factors, S(qD), approach unity, as shown in the inset. At ϕc = 0.17, NPs without DOPA-mPEG were welldispersed without aggregation showing the first order peak at qD ∼ 4.5. As rσ increases, particles were gradually less ordered and aggregated, as indicated by the peak disappearance and upturns at low qD.26−28 At higher ϕc of 0.38, particle dispersions with DOPA-mPEG grafting abruptly changed and showed aggregations. Noting the position of the first peaks indicates the average center-to-center distance of particles, the change in position of the first peak to q*D ∼ 7 implies that particles came into contact and aggregated with increasing rσ. To capture the particle aggregation with DOPA-mPEG grafting, the positions of the first peaks are plotted for different ϕc in Figure 2d. While the DOPA-mPEG grafting had no impact on particle dispersion at low ϕc, the shift in q*D implies that DOPA-mPEG grafting makes particles more attractive, bringing them in contact, and its effect is more significant at higher ϕc. The abrupt change of particle microstructures with DOPAmPEG grafting also influences the physical properties of PNCs. To explore the effect of DOPA-mPEG grafting on mechanical properties, the complex shear modulus, G*, is measured in the linear viscoelastic regime with frequency sweep at 0.1% strain, as shown in Figure 3. G* is defined as G* = G′ + iG″, where G′ and G″ are the storage and loss shear modulus, respectively.29 When ϕc = 0.07, where the surface-to-surface distance between NPs is far apart (about 40 nm), no change of modulus is observed, as shown in Figure S5, consistent with the scattering result. When ϕc = 0.17, where the surface-to-surface distance between NPs decreases to about 16 nm, a rapid modulus

Figure 1. (a) Surface chemical structures of silica NPs without (top) and with (bottom) DOPA-mPEG grafting. (b) Adsorption isotherm for DOPA-mPEG on silica NPs (left y-axis, black squares) and the surface coverage rate, rσ (right y-axis, red triangles). The fitting curve is drawn from the experimental results.

silica surfaces was confirmed by TGA (Figure S2) and FT-IR results (Figure S3), and we found DOPA-mPEG was strongly grafted on silica via H-bonding between catechol groups of DOPA-mPEG and silanol groups of silica surfaces with ∼2 nm of thickness (Figure S4).24,25 In Figure 1b, the monolayer21 of adsorption isotherm increases with the addition of DOPAmPEG and reaches 90% of maximum coverage at 0.13 w/w of DOPA-mPEG to silica weight ratio. The corresponding surface coverage rate, rσ, of silica NPs is calculated and varied from 0 to 0.99 by adjusting the amount of DOPA-mPEG added (Table S1). Particle microstructure and dispersion stability in polymer melt with varying rσ were analyzed with SAXS, with results shown in Figure 2. The experimental scattering intensity, I(q), was considered to arise only from silica NPs due to the greater 963

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967

Letter

ACS Macro Letters

limit.31 The low shear viscosity of PNC at low ϕc was measured and fitted to the equation ηr,0 = 1 + 2.5kϕc + B(kϕc)2, where ηr,0 is the relative shear viscosity close to the zero-shear rate and k is the particle intrinsic viscosity factor; thus, ϕeff is defined as kϕc and B is the pair-interaction coefficient.32 At low ϕc, B can be neglected, and thus, k can be estimated as k = (ηr,0 − 1)/2.5ϕc. The values of k are plotted as a function of particle volume fraction for ϕc < 0.05 and fitted to the equation in Figure 4. As

Figure 4. Intrinsic viscosity factor, k, of silica NPs in PEG400 melt for different rσ was measured at 25 °C. The fitted k are drawn with dashed lines with error bars. The raw data for shear viscosity, ηr,0, is given in the inset.

rσ increases from 0 to 0.51, k increases from 1.18 to 1.47, suggesting an increase of ϕeff with DOPA-mPEG by 25%. While the increase of k confirms a thicker layer of DOPAmPEG grafting than mere PEG chains, the degree of increment is not sufficient to explain the dramatic change of particle microstructures and modulus enhancement. For example, the effective particle radius is only larger by 1.6 nm at rσ = 0.51, increasing ϕc by 25% over bare NPs. If DOPA-mPEG grafting on silica surface merely increased the effective volume of NPs, G* of PNC at ϕc = 0.17 with rσ = 0.51 (ϕeff = 0.21) would have a modulus equivalent to PNC at ϕc = 0.21 without DOPAmPEG grafting. However, we found that PNC without DOPAmPEG remains liquid-like even up ϕc = 0.28 (Figure S7), whereas PNC at ϕc = 0.17 with rσ = 0.51 with DOPA-mPEG shows solid-like behavior at most frequencies. Thus, the increased effective volume of particles cannot be enough to explain the large modulus enhancement. Based on the scattering structure results, we predict that grafting DOPA-mPEG on the silica surface induces particle agglomeration, possibly creating percolating networks, which results in dramatic reinforcement of the polymer matrix. DOPA-mPEG chains can attract each other because of their internal ability to H-bond, thus, residual DOPA-mPEG in bulk and on NPs induces additional attractions for NPs. Indeed, the networked superstructure of PNCs with DOPA-mPEG grafting is found in Figure S8. To reveal the origin of mechanical property enhancement and detailed interfacial structures between grafted DOPAmPEG and matrix polymer, strain-induced structure deformation was observed with strain sweep experiments, as shown in Figure 5.

Figure 3. Complex shear modulus, G*, as a function of angular frequency, ω, at 0.1% strain for PEG400 at (a) ϕc = 0.17 and (b) 0.38 for varying rσ. All samples were measured at 75 °C.

change occurs as rσ increases. G* is as low as 0.01 Pa and exhibits liquid-like properties (G′ ∼ ω2 and G″ ∼ ω1) until rσ reaches 0.32 (Figure S6a), but when rσ = 0.51, G* increases to 10 Pa and a liquid-to-glass transition occurs.26 With full grafting (rσ = 0.99), the system becomes fully solid-like and G* increases to 3000 Pa, 105 times higher than that of bare NP PNC. At higher particle loadings such as ϕc = 0.38, the modulus enhancement is observed much more easily. Despite partial grafting (rσ ∼ 0.16), G* is more than 102 times greater than that of bare PNCs (rσ = 0). However, at larger rσ (>0.51), a slight reduction in G* was found, possibly due to the crowding and stretching of grafted chains, which could result in increased entropic repulsion.12,30 All frequency-dependent G′ and G″ behavior with varying rσ is provided in Figure S6b. In principle, the mechanical properties of PNC can be enhanced with adding inorganic NPs (fillers), while the degree of enhancement can be dependent on the nature of particle− polymer interactions. Therefore, we suspect that the modulus enhancement can be derived from increased effective volume of particles with DOPA-mPEG grafting. Due to the Newtonian behavior of unentangled PEG melts and the large particle-topolymer size ratio, the effective particle volume, ϕeff, can be estimated with the intrinsic viscosity in the dilute particle 964

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967

Letter

ACS Macro Letters

Thus, the unique existence of second yield was considered to be associated with grafting-induced particle aggregations. When particles are close enough, the grafted DOPA-mPEGs can mediate entanglements by intrinsic attractions; thus, even short matrix chains are also trapped, bringing particles in contact.26,35 While Baeza et al. showed that bridging aggregations with entangled polymers is critical to increase mechanical strength of PNC, aggregations with low MW PNC was not reported.39 The breakage of this association requires strong strain, around 280%, independent of rσ and a slight strain hardening was observed with a localized G″ maximum at the second yield (Figure S9b). This was caused by increased internal stress due to stretching during the disentanglement between grafted DOPA-mPEGs and trapped polymers before they are separated.26,35 One considers that increasing composition ratio of DOPAmPEG simply alters the physical properties of PNC irrespective of whether or not it is grafted. For comparison, we prepared another type of PNC with DOPA-mPEG where DOPA-mPEG is mixed later, so it is expected to remain in bulk. When the DOPA-mPEG is in bulk, not at the particle interface, the modulus and its texture are rather similar to that of PNC with bare NPs over a year (Figure S10). Therefore, the enhanced shear modulus and existence of two-step yielding can be regarded as arising from the grafted DOPA-mPEG mediated aggregations near particle interfaces. The proposed microstructure of PNCs with and without DOPA-mPEG is drawn in Scheme 1. Scheme 1. Interface Microstructure of PNCs: Silica NPs in PEG 400 Matrix Without (left) and With (right) DOPAmPEG Grafting Figure 5. Complex shear modulus, G*, for (a) ϕc = 0.17 at 0.01 Hz and (b) ϕc = 0.38 at 1 Hz with varying rσ, is plotted as a function of complex shear strain, γ. All measurements were conducted at 75 °C.

First at ϕc = 0.17 (Figure 5a), up to rσ = 0.32, a general liquid-like strain dependency is found (G′ ∼ γ−2 and G″ ∼ γ−1), and strain-dependency is gradually decreased with increasing rσ (Figure S9a). At high coverage (rσ > 0.50), the formed agglomerations exhibited linear viscoelastic response at low strain with the significant modulus enhancement and became nonlinear at high strain, implying a weak glass structure.33,34 At higher ϕc of 0.38 (Figure 5b), the effect of DOPA-mPEG grafting was greater because grafted chains can interact each other in a shorter distance. First, the plateau modulus was elevated by 3 orders of magnitude, resulting from the percolated particle agglomeration.35 The degree of modulus elevation is indeed exceptional considering the low MW of the polymer matrix. Second, two yield strains were observed. The first yield strain was associated with initial distortion of particle microstructure, which occurs when glassy networks are deformed and does not change with rσ.33 However, the second yield and an intermediate strain softening regime only existed in DOPA-mPEG grafted PNCs. It is also noteworthy that even though the second yielding is a typical characteristic of entangled PNC,33,36 it is observed with a relatively low ϕc and unentangled polymers. Furthermore, its effective particle volume fraction is ϕeff = 0.384 for rσ = 0.16, still well below the random close packing particle volume fraction of 0.64.37,38

In conclusion, we showed that the state of particle dispersion of PNCs can be readily controlled with simple polymer-grafted NPs. The appropriate level of polymer-grafting can provide the ability to control the interparticle and grafted-matrix polymer interactions such that attractive grafted polymer chains can mediate liquid-to-solid transitions and particle agglomerations forming glassy superstructures, resulting in dramatic modulus enhancement. We note that Jouault et al. employed adsorbed block copolymers as an effective control of interparticle interactions and unlike the current research, particle agglomeration was found at low adsorption density. In addition, the agglomeration was produced with high MW polymer and did not yield a homogeneous gel-like network.40 Akcora et al. reported formation of superstructures with spherical polymer-grafted NPs;41 however, this remarkable improvements (more than 105 times) was not reported at low 965

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967

Letter

ACS Macro Letters

(3) Souier, T.; Santos, S.; Al Ghaferi, A.; Stefancich, M.; Chiesa, M. Enhanced Electrical Properties of Vertically Aligned Carbon Nanotube-Epoxy Nanocomposites with High Packing Density. Nanoscale Res. Lett. 2012, 7, 1−8. (4) Tian, G. F.; Zhang, H. P.; Liu, J. N.; Qi, S. L.; Wu, D. Z. Enhanced Conductivity and Mechanical Properties of Polyimide Based Nanocomposite Materials with Carbon Nanofibers via Carbonization of Electrospun Polyimide Fibers. Polym. Sci., Ser. A 2014, 56 (4), 505−510. (5) Kumar, S. K.; Ganesan, V.; Riggleman, R. A. Perspective: Outstanding Theoretical Questions in Polymer-Nanoparticle Hybrids. J. Chem. Phys. 2017, 147 (2), 020901. (6) Lee, H.; Lee, B. P.; Messersmith, P. B. A Reversible Wet/Dry Adhesive Inspired by Mussels and Geckos. Nature 2007, 448 (7151), 338−341. (7) Ranka, M.; Varkey, N.; Ramakrishnan, S.; Zukoski, C. F. Impact of Small Changes in Particle Surface Chemistry for Unentangled Polymer Nanocomposites. Soft Matter 2015, 11 (8), 1634−1645. (8) Zheng, Z.; Song, Y. H.; Xu, H. L.; Zheng, Q. Thickening of the Immobilized Polymer Layer Using Trace Amount of Amine and Its Role in Promoting Gelation of Colloidal Nanocomposites. Macromolecules 2015, 48 (24), 9015−9023. (9) Kwon, N. K.; Lee, T. K.; Kwak, S. K.; Kim, S. Y. AggregationDriven Controllable Plasmonic Transition of Silica-Coated Gold Nanoparticles with Temperature-Dependent Polymer-Nanoparticle Interactions for Potential Applications in Optoelectronic Devices. ACS Appl. Mater. Interfaces 2017, 9 (45), 39688−39698. (10) Hasegawa, R.; Aoki, Y.; Doi, M. Optimum Graft Density for Dispersing Particles in Polymer Melts. Macromolecules 1996, 29 (20), 6656−6662. (11) Sunday, D. F.; Green, D. L. Thermal and Rheological Behavior of Polymer Grafted Nanoparticles. Macromolecules 2015, 48 (23), 8651−8659. (12) Kumar, S. K.; Jouault, N.; Benicewicz, B.; Neely, T. Nanocomposites with Polymer Grafted Nanoparticles. Macromolecules 2013, 46 (9), 3199−3214. (13) Tauban, M.; Delannoy, J. Y.; Sotta, P.; Long, D. R. Effect of Filler Morphology and Distribution State on the Linear and Nonlinear Mechanical Behavior of Nanofilled Elastomers. Macromolecules 2017, 50 (17), 6369−6384. (14) Zhao, D.; Ge, S. F.; Senses, E.; Akcora, P.; Jestin, J.; Kumar, S. K. Role of Filler Shape and Connectivity on the Viscoelastic Behavior in Polymer Nanocomposites. Macromolecules 2015, 48 (15), 5433− 5438. (15) Klonos, P.; Kulyk, K.; Borysenko, M. V.; Gun’ko, V. M.; Kyritsis, A.; Pissis, P. Effects of Molecular Weight below the Entanglement Threshold on Interfacial Nanoparticles/Polymer Dynamics. Macromolecules 2016, 49 (24), 9457−9473. (16) Voylov, D. N.; Holt, A. P.; Doughty, B.; Bocharova, V.; Meyer, H. M.; Cheng, S. W.; Martin, H.; Dadmun, M.; Kisliuk, A.; Sokolov, A. P. Unraveling the Molecular Weight Dependence of Interfacial Interactions in Poly(2-vinylpyridine)/Silica Nanocomposites. ACS Macro Lett. 2017, 6 (2), 68−72. (17) Holt, A. P.; Bocharova, V.; Cheng, S. W.; Kisliuk, A. M.; White, B. T.; Saito, T.; Uhrig, D.; Mahalik, J. P.; Kumar, R.; Imel, A. E.; Etampawala, T.; Martin, H.; Sikes, N.; Sumpter, B. G.; Dadmun, M. D.; Sokolov, A. P. Controlling Interfacial Dynamics: Covalent Bonding versus Physical Adsorption in Polymer Nanocomposites. ACS Nano 2016, 10 (7), 6843−6852. (18) Hattemer, G. D.; Arya, G. Viscoelastic Properties of PolymerGrafted Nanoparticle Composites from Molecular Dynamics Simulations. Macromolecules 2015, 48 (4), 1240−1255. (19) Sunday, D.; Ilavsky, J.; Green, D. L. A Phase Diagram for Polymer-Grafted Nanoparticles in Homopolymer Matrices. Macromolecules 2012, 45 (9), 4007−4011. (20) Liu, Y.; Meng, H.; Konst, S.; Sarmiento, R.; Rajachar, R.; Lee, B. P. Injectable Dopamine-Modified Poly(ethylene glycol) Nanocomposite Hydrogel with Enhanced Adhesive Property and Bioactivity. ACS Appl. Mater. Interfaces 2014, 6 (19), 16982−16992.

MW without entanglements. Furthermore, the modulus enhancement of low MW PNC found in this study is even comparable to that of highly entangled PNCs. It is interesting to note that our observations are in agreements with the computational prediction by Hattemer et al.,18 which explains the modulus enhancement of PNCs via high affinity between grafted/host matrix chains and shear distortion effects caused by grafted polymer. DOPA-mPEG grafting provides a new strategy for controlling intrinsic particle interactions, and the ability to change the mechanical property of PNCs with low MW polymers can greatly extend the PNC’s processability. Finally, we emphasize that a detailed understanding of interfacial structures of polymer chains can always provide more opportunity to explore the micro- and macroscopic structures and properties of polymeric materials, including PNCs.

■

ASSOCIATED CONTENT

* Supporting Information S

The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/acsmacrolett.8b00475.

■

Materials and experimental details and supporting Figures S1−S10 (PDF).

AUTHOR INFORMATION

Corresponding Authors

*E-mail: [email protected]. Phone: +82 52 217 2558. *E-mail: [email protected]. ORCID

Hyun-Wook Lee: 0000-0001-9074-1619 Jongnam Park: 0000-0002-0954-0172 So Youn Kim: 0000-0003-0066-8839 Author Contributions

The manuscript was written through contributions of all authors. All authors have given approval to the final version of the manuscript. Notes

The authors declare no competing financial interest.

■

ACKNOWLEDGMENTS This work was supported by the Research program through the National Research Foundation of Korea (NRF; NRF2018R1A2B6008319 and 2015K2A9A2A18065964). J.P. acknowledges the institutional research program of Korea Institute of Science and Technology (KIST) (2E28070) and N.K.K. acknowledges the Global Ph.D. Fellowship Program (NRF-2016H1A2A1907114). SAXS experiments at PLS-II 6D UNIST-PAL beamline were supported in part by MSIT, POSTECH, and UNIST Central Research Facilities.

■

REFERENCES

(1) Hashemi, A.; Jouault, N.; Williams, G. A.; Zhao, D.; Cheng, K. J.; Kysar, J. W.; Guan, Z. B.; Kumart, S. K. Enhanced Glassy State Mechanical Properties of Polymer Nanocomposites via Supramolecular Interactions. Nano Lett. 2015, 15 (8), 5465−5471. (2) Musino, D.; Genix, A. C.; Fayolle, C.; Papon, A.; Guy, L.; Meissner, N.; Kozak, R.; Weda, P.; Bizien, T.; Chaussee, T.; Oberdisse, J. Synergistic Effect of Small Molecules on Large-Scale Structure of Simplified Industrial Nanocomposites. Macromolecules 2017, 50 (13), 5138−5145. 966

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967

Letter

ACS Macro Letters (21) Yamamoto, S.; Uchiyama, S.; Miyashita, T.; Mitsuishi, M. Multimodal Underwater Adsorption of Oxide Nanoparticles on Catechol-Based Polymer Nanosheets. Nanoscale 2016, 8 (11), 5912−5919. (22) Kang, T.; Banquy, X.; Heo, J. H.; Lim, C. N.; Lynd, N. A.; Lundberg, P.; Oh, D. X.; Lee, H. K.; Hong, Y. K.; Hwang, D. S.; Waite, J. H.; Israelachvili, J. N.; Hawker, C. J. Mussel-Inspired Anchoring of Polymer Loops That Provide Superior Surface Lubrication and Antifouling Properties. ACS Nano 2016, 10 (1), 930−937. (23) Kaushik, N. K.; Kaushik, N.; Pardeshi, S.; Sharma, J. G.; Lee, S. H.; Choi, E. H. Biomedical and Clinical Importance of MusselInspired Polymers and Materials. Mar. Drugs 2015, 13 (11), 6792− 6817. (24) Mian, S. A.; Yang, L. M.; Saha, L. C.; Ahmed, E.; Ajmal, M.; Ganz, E. A Fundamental Understanding of Catechol and Water Adsorption on a Hydrophilic Silica Surface: Exploring the Underwater Adhesion Mechanism of Mussels on an Atomic Scale. Langmuir 2014, 30 (23), 6906−6914. (25) Wang, W. T.; Ji, X.; Na, H. B.; Safi, M.; Smith, A.; Palui, G.; Perez, J. M.; Mattoussi, H. Design of a Multi-Dopamine-Modified Polymer Ligand Optimally Suited for Interfacing Magnetic Nanoparticles with Biological Systems. Langmuir 2014, 30 (21), 6197− 6208. (26) Anderson, B. J.; Zukoski, C. F. Rheology and Microstructure of Entangled Polymer Nanocomposite Melts. Macromolecules 2009, 42 (21), 8370−8384. (27) Kwon, N. K.; Park, C. S.; Lee, C. H.; Kim, Y. S.; Zukoski, C. F.; Kim, S. Y. Tunable Nanoparticle Stability in Concentrated Polymer Solutions On the Basis of the Temperature Dependent Solvent Quality. Macromolecules 2016, 49 (6), 2307−2317. (28) Kim, S. Y.; Hall, L. M.; Schweizer, K. S.; Zukoski, C. F. Long Wavelength Concentration Fluctuations and Cage Scale Ordering of Nanoparticles in Concentrated Polymer Solutions. Macromolecules 2010, 43 (23), 10123−10131. (29) Tschoegl, N. W. The Phenomenological Theory of Linear Viscoelastic Behavior; Springer: Berlin, Heidelberg, 1989. (30) Hall, L. M.; Jayaraman, A.; Schweizer, K. S. Molecular Theories of Polymer Nanocomposites. Curr. Opin. Solid State Mater. Sci. 2010, 14 (2), 38−48. (31) Russel, W. B.; Scholwalter, W. R. Colloidal Dispersions; Cambridge University Press: Cambridge, U.K., 1992. (32) Kim, S. Y.; Zukoski, C. F. Super- and Sub-Einstein Intrinsic Viscosities of Spherical Nanoparticles in Concentrated Low Molecular Weight Polymer Solutions. Soft Matter 2012, 8 (6), 1801−1810. (33) Anderson, B. J.; Zukoski, C. F. Colloidal Glass Transition in Unentangled Polymer Nanocomposite Melts. J. Phys.: Condens. Matter 2009, 21 (28), 285102. (34) Srivastava, S.; Shin, J. H.; Archer, L. A. Structure and Rheology of Nanoparticle-Polymer Suspensions. Soft Matter 2012, 8 (15), 4097−4108. (35) Agrawal, A.; Yu, H. Y.; Sagar, A.; Choudhury, S.; Archer, L. A. Molecular Origins of Temperature-Induced Jamming in SelfSuspended Hairy Nanoparticles. Macromolecules 2016, 49 (22), 8738−8747. (36) Agrawal, A.; Wenning, B. M.; Choudhury, S.; Archer, L. A. Interactions, Structure, and Dynamics of Polymer-Tethered Nanoparticle Blends. Langmuir 2016, 32 (34), 8698−8708. (37) Pusey, P. N.; Vanmegen, W. Phase Behavior of Concentrated Suspensions of nearly Hard Colloidal Spheres. Nature 1986, 320 (6060), 340−342. (38) Joshi, Y. M. Dynamics of Colloidal Glasses and Gels. Annu. Rev. Chem. Biomol. Eng. 2014, 5, 181−202. (39) Baeza, G. P.; Dessi, C.; Costanzo, S.; Zhao, D.; Gong, S. S.; Alegria, A.; Colby, R. H.; Rubinstein, M.; Vlassopoulos, D.; Kumar, S. K. Network Dynamics in Nanofilled Polymers. Nat. Commun. 2016, 7, 11368.

(40) Jouault, N.; Lee, D.; Zhao, D.; Kumar, S. K. Block-CopolymerMediated Nanoparticle Dispersion and Assembly in Polymer Nanocomposites. Adv. Mater. 2014, 26 (24), 4031−4036. (41) Akcora, P.; Liu, H.; Kumar, S. K.; Moll, J.; Li, Y.; Benicewicz, B. C.; Schadler, L. S.; Acehan, D.; Panagiotopoulos, A. Z.; Pryamitsyn, V.; Ganesan, V.; Ilavsky, J.; Thiyagarajan, P.; Colby, R. H.; Douglas, J. F. Anisotropic Self-Assembly of Spherical Polymer-Grafted Nanoparticles. Nat. Mater. 2009, 8 (4), 354−359.

967

DOI: 10.1021/acsmacrolett.8b00475 ACS Macro Lett. 2018, 7, 962−967