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Low percolation threshold of graphene/polymer composites prepared by solvothermal reduction of graphene oxide in the polymer solution
Nanoscale Research Lettersvolume 8, Article number: 132 (2013)
Graphene/polyvinylidene fluoride (PVDF) composites were prepared using in-situ solvothermal reduction of graphene oxide in the PVDF solution. The electrical conductivity of the composites was greatly improved by doping with graphene sheets. The percolation threshold of such composite was determined to be 0.31 vol.%, being much smaller than that of the composites prepared via blending reduced graphene sheets with polymer matrix. This is attributed to the large aspect ratio of the SRG sheets and their uniform dispersion in the polymer matrix. The dielectric constant of PVDF showed a marked increase from 7 to about 105 with only 0.5 vol.% loading of SRG content. Like the other conductor-insulator systems, the AC conductivity of the system also obeyed the universal dynamic response. In addition, the SRG/PVDF composite shows a much stronger nonlinear conduction behavior than carbon nanotube/nanofiber based polymer composite, owing to intense Zener tunneling between the SRG sheets. The strong electrical nonlinearity provides further support for a homogeneous dispersion of SRG sheets in the polymer matrix.
Recently, there is a great demand for polymeric materials with excellent electrical performance and high mechanical strength in the electronic industries. Conventional polymeric materials are insulators and can be made conductive by adding large volume fractions of conducting fillers in micrometer size such as metal and graphite particles [1–3]. However, high filler loadings generally result in low mechanical strength, heavy weight, and poor processability [4–6]. In this respect, fillers of nanometer dimensions are added to polymers to enhance their mechanical and physical performances [7–10]. Carbonaceous nanofillers such as carbon nanotubes (CNTs) with large mechanical strength and high electrical conductivity have been widely added to polymers to form conductive nanocomposites [11–17]. Their large aspect ratios enable the formation of conductive network in the polymer matrix at low filler contents. However, single-walled carbon nanotubes are very expensive, and the cost of multiwalled CNTs still remain relatively high despite a large reduction in their price in recent years . The high cost of CNTs and their strong tendency to form aggregates have greatly limited their potential applications.
Graphite nanoplatelets (GNPs) prepared from the exfoliation of graphite intercalation compound (GIC) are low-cost fillers for preparing conductive polymer nanocomposites. The GIC can be synthesized by reacting natural graphite with electron-donor agents such as alkali metals or with electron acceptors . However, GNPs consist of tens to hundreds of stacked graphene layers, corresponding to partially exfoliated graphite . In 2004, Geim and co-workers successfully exfoliated graphite into graphene monolayer using the scotch tape method . The monolayer graphene they obtained is believed to be a promising nanofiller for polymers due to its exceptionally high mechanical strength and excellent electrical and thermal properties. It has been reported that graphene/polymer composites exhibit much improved electrical and mechanical properties when compared to CNT/polymer composites [22, 23]. In practice, however, the low yield of mechanically exfoliated graphene has greatly limited its applications. Thus, high-yield graphene oxide (GO) prepared from the chemical oxidation of graphite in strong oxidizing acids is commonly used to prepare graphene [24, 25]. GO is electrically insulating; therefore, chemical reduction or thermal treatment is needed to restore its electrical conductivity [26, 27]. In addition, graphene sheets have a great tendency to aggregate when they are loaded to the polymers. The aggregation is mainly due to the van der Waals attractions between the graphene sheets. This would deteriorate the electrical performance of the resultant composites, and usually, more fillers need to be loaded to form a percolating network in this case. In this study, we fabricated graphene/polymer composites using solvothermal reduction of GO in the polymer solution. This method enables the reduction of GO to graphene and its blending with the polymer matrix in one step. The polymer material used was polyvinylidene fluoride (PVDF). It is a semicrystalline polymer having remarkable thermal stability, excellent chemical resistance, and extraordinary pyro- and piezoelectric characteristics. It has found wide applications in the fields of electronic and biomedical engineering . This study presents the first report on the synthesis and electrical characterization of the solvothermal reduced graphene/PVDF nanocomposites.
Graphite flakes and PVDF (Kynar 500) were purchased from Sigma-Aldrich Inc. (St. Louis, MO, USA) and Arkema Inc. (King of Prussia, PA, USA), respectively.
Graphite oxide was prepared using a typical Hummers method . In a typical composite fabrication procedure, graphite oxide was firstly ultrasonicated in N, N-dimethylformamide (DMF) for 40 min to be exfoliated into GO. PVDF pellets were then dissolved in this suspension at 60°C. Subsequently, the solution mixture was transferred into a 50-ml steel autoclave and placed in an oven at 100°C for 12 h. In this solvothermal reaction, DMF acted as the solvent for dissolving PVDF and also served as a medium to transmit heat and pressure to reduce GO. After the reaction ended, the autoclave was taken out and allowed to cool naturally, and a solution mixture of solvothermal reduced graphene (SRG) sheets and PVDF was obtained. This solution was used to fabricate the SRG/PVDF composites via the coagulation method . In this process, the suspension was dropped into a blender containing a large amount of distilled water. The SRG/PVDF composite mixture precipitated out immediately due to its insolubility in the DMF/water mixture. The obtained fibrous SRG/PVDF mixture was vacuum filtrated and dried and finally hot-pressed into thin sheets of approximately 1 mm thick.
To convert wt.% loading of graphene sheets in the composite samples to vol.% (as used in the text), a density for the GO sheets of 2.2 g/cm3 was assumed . The prepared GO was examined using an atomic force microscope (AFM, Veeco Nanoscope V, Plainview, NY, USA). The morphology of the SRG/PVDF composites was examined using a scanning electron microscope (SEM, Jeol JSM 820, JEOL Ltd., Akishima-shi, Japan). The dielectric constant and electrical conductivity of the composites were measured with a Hewlett Packard 4284A Precision LCR Meter (Hewlett-Packard Company, Palo Alto, CA, USA). The current density-electric field (J-E) characteristic of the composites was measured by a Hewlett Packard 4140B pA meter/DC voltage source (Hewlett-Packard Company, Palo Alto, CA, USA). Silver paste was coated on the specimen surfaces to form electrodes.
Results and discussion
Figure 1 shows the AFM image of GO sheets prepared from chemical oxidation of graphite in strong acids. From the thickness measurements, it is obvious that the graphite oxide was completely exfoliated into monolayer GO. Because of the presence of carbonyl and carboxyl functional groups on its surface, the thickness of the sheets was approximately 1 nm, slightly thicker than graphene . The average size of GO sheets was in the order of several micrometers, rendering them with very large aspect ratios. Figure 2 shows the morphology of SRG/PVDF composites containing different SRG loading levels. At low filler loadings, it is rather difficult to distinguish SRG sheets from the polymer matrix, due to its low contrast to the background and monolayer nature. As the filler content increases, the SRG sheets become more distinguishable, particularly at a filler content of 1.4 vol.%.
The percolation theory is often employed to characterize the insulator-conductor transition of the polymer composites containing conductive fillers. Figure 3 shows the electrical conductivity versus filler content for the SRG/PVDF composites. According to the percolation theory, the static conductivity of the composites is given by [32, 33]:
where pc is the percolation threshold, p is the filler content, and t is the critical exponent. As shown in Table 1, the fit of electrical conductivity to Equation 1 yields a percolation threshold as low as 0.31 vol.% (Figure 3). Such a percolation threshold is lower than that of the graphene/PVDF composite prepared by direct blending chemically/thermally reduced GO sheets with polymers [34, 35]. The low pc is attributed to the homogeneous dispersion of SRG sheets within the PVDF matrix. In this study, we found that the SRG sheets could remain stable in the PVDF solution up to several weeks. Without PVDF in DMF, however, black SRG precipitates appeared after 1 day. So it is considered that the PVDF molecular chains could stabilize the SRG sheets. Since the GO sheets were enclosed by the PVDF molecular chains and reduced to SRG sheets during the solvothermal process, they would not fold easily or form aggregates as often happened. This would facilitate the formation of conducting network and result in a low percolation threshold. The large aspect ratios of the SRG sheets make the percolation threshold even smaller.
Figure 4a shows the frequency dependency of the dielectric constant (εr) of the SRG/PVDF composites. Apparently, εr increases markedly with increasing SRG content. The increased εr can be attributed to the formation of various nanocapacitors consisting of SRG sheets separated by dielectric PVDF film [36–38]. At 1 kHz, the dielectric constant of pure PVDF is 7. This value reaches 60 and 105 when the PVDF was filled with 0.4 and 0.5 vol.% SRG, respectively. Although carbon-based polymeric composites with high dielectric permittivity have been reported [35, 39–41], the dielectric loss of those composites are generally too large for practical applications. In contrast, the electrical conductivity of the SRG/PVDF composite (for p = 0.4 or 0.5 vol.%) is relatively low (see Figure 4b); therefore, the dielectric loss can be minimized. The good dielectric performance in combination with high flexibility makes such SRG/PVDF composite an excellent candidate of high-k material.
Figure 4b shows the variation of conductivity with frequency for SRG/PVDF composites. For the composites with low SRG loadings (p ≤ 0.3 vol.%), σ(f) increases almost linearly with frequency, which is a typical characteristic of insulating materials. When the filler content reaches 0.4 vol.% and above, σ(f) at low-frequency region shows a marked increase, due to the onset of the formation of percolating structure spanning the polymer matrix. For the composites with higher SRG loadings (p ≥ 0.8 vol.%), the conductivity is independent of the frequency at low-frequency regime. Above a characteristic frequency, the conductivity increases with increasing frequency. This indicates that a percolating SRG network throughout the whole system has been fully developed. The frequency-independent plateau is termed as the DC conductivity (σDC) and particularly obvious for the composites with high SRG loadings. The two-stage conductivity behavior can be described by the following relationship [42, 43]:
where A is a constant depending on temperature and x is a critical exponent depending on both frequency and temperature. This behavior is typical for a wide number of conducting composite materials  and usually termed as ‘universal dynamic response’ [43, 44]. Ezquerra et al. have had a detailed study of such a behavior [45–47]. We have also investigated this dynamic response in carbon nanotube/nanofiber based composites [48, 49]. By fitting the data in Figure 4b to Equation 2, the values of σDC, A, and x for percolative SRG/PVDF composites could be extracted. They are listed in Table 2.
Figure 5 presents the J-E characteristic of the PVDF composite with 1.4 vol.% SRG sheets. The composite exhibits a much stronger nonlinear conduction behavior compared with the polymer composites with carbon nanotubes/nanofibers . Similarly, other SRG/PVDF composites with SRG content above pc also exhibit such a behavior. As with other carbon/polymer composites, the current density J can be divided into linear J L and nonlinear J NL . The nonlinear part is caused by the Zener tunneling of electrons between the SRG sheets. As shown in the inset of Figure 5, the Zener tunneling predicts the nonlinear current density (JNL) very well on the basis of the tunneling equation, i.e., J = AEnexp(−B/E) where A, B, and n are constants . To the best of our knowledge, this is the first report about Zener effect in graphene/polymer composite. From our previous study, a homogeneous dispersion of conductive filler within the insulating matrix tends to cause strong Zener current . Hence, the strong electrical nonlinearity provides further support for the uniform dispersion of the SRG sheets in the PVDF matrix.
SRG/PVDF composite was prepared by in-situ solvothermal reduction of graphene oxide in the PVDF solution. The large aspect ratio of SRG sheets in combination with uniform dispersion in the polymer matrix led to a relatively low percolation threshold of 0.31 vol.%, which is smaller than graphene/polymer composites prepared by direct blending chemically/thermally reduced GO sheets with PVDF. It is found that only 0.5 vol.% SRG doping will increase the dielectric constant of the material from 7 to about 105, while keeping the conductivity at a low level. Such a dielectric performance is superior to those of carbon nanotube/nanofiber based polymeric composites. The AC conductivity of the composite above pc follows the universal dynamic response, as with many other conductor-insulator systems. Moreover, the electrical nonlinearity of these composites is stronger than the carbon nanotube/nanofiber filled polymer system, resulting from the Zener tunneling effect between the uniformly dispersed SRG sheets.
Psarras GC: Hopping conductivity in polymer matrix–metal particles composites. Composites Part A 2006, 37: 1545–1553. 10.1016/j.compositesa.2005.11.004
Mrozek RA, Cole PJ, Mondy LA, Rao RR, Bieg LF, Lenhar JL: Highly conductive, melt processable polymer composites based on nickel and low melting eutectic metal. Polymer 2010, 51: 2954–2958. 10.1016/j.polymer.2010.04.067
Mironov VS, Kim JK, Park M, Lim S, Cho WK: Comparison of electrical conductivity data obtained by four-electrode and four-point probe methods for graphite-based polymer composites. Polym Test 2007, 26: 547–555. 10.1016/j.polymertesting.2007.02.003
Tjong SC, Xu SA: Non-isothermal crystallization kinetics of calcium carbonate filled beta-crystalline phase polypropylene composites. Polym Int 1997, 44: 95–103. 10.1002/(SICI)1097-0126(199709)44:1<95::AID-PI821>3.0.CO;2-L
Meng YZ, Tjong SC: Rheology and morphology of compatibilized polyamide 6 blends containing liquid crystalline copolyesters. Polymer 1998, 39: 99–107. 10.1016/S0032-3861(97)00218-8
Tjong SC, Liu SL, Li RKY: Mechanical properties of injection molded blends of polypropylene with thermotropic liquid crystalline polymer. J Mater Sci 1996, 31: 479–484. 10.1007/BF01139167
Tjong SC, Meng YZ, Hay AS: Novel preparation and properties of polypropylene-vermiculite nanocomposites. Chem Mater 2002, 14: 44–51. 10.1021/cm010061b
Bao SP, Tjong SC: Impact essential work of fracture of polypropylene/montmorillonite nanocomposites toughened with SEBS-g-MA elastomer. Composites Part A 2007, 38: 378–387. 10.1016/j.compositesa.2006.03.005
Cheng X, Tjong SC, Zhao Q, Li RKY: Facile method to prepare monodispersed Ag/polystyrene composite microspheres and their properties. J Polym Sci Part A Polym Chem 2009, 47: 4547–4555. 10.1002/pola.23507
Tjong SC, Bao SP, Liang GD: Polypropylene/montmorillonite nanocomposites toughened with SEBS-g-MA: structure–property relationship. J Polym Sci, Part B: Polym Phys 2005, 43: 3112–3126. 10.1002/polb.20596
Bao SP, Liang GD, Tjong SC: Effect of mechanical stretching on electrical conductivity and positive temperature coefficient characteristics of poly(vinylidene fluoride)/carbon nanofiber composites prepared by non-solvent precipitation. Carbon 2011, 49: 1758–1768. 10.1016/j.carbon.2010.12.062
Tjong SC: Polymer nanocomposite bipolar plates reinforced with carbon nanotubes and graphite nanosheets. Energy and Environ Sci 2011, 44: 605–626.
Gong XY, Liu J, Baskaran S, Voise RD, Young JS: Surfactant-assisted processing of carbon nanotube/polymer composites. Chem Mater 2000, 12: 1049–1052. 10.1021/cm9906396
Gao JB, Zhao B, Itkis ME, Bekyarova E, Hu H, Kranak V, Yu AP, Haddon RC: Chemical engineering of the single-walled carbon-nanotube-nylon 6 interface. J Am Chem Soc 2006, 128: 7492–7496. 10.1021/ja057484p
Logakis E, Pandis CH, Peoglos V, Pissis P, Pionteck J, Potschke P, Micusil M, Omastova M: Electrical/dielectric properties and conduction mechanism in melt processed polyamide 6/multi-walled carbon nanotubes composites. Polymer 2009, 50: 5103–5111. 10.1016/j.polymer.2009.08.038
Dang ZM, Wang L, Yin Y, Zhang Q, Lei QQ: Giant dielectric permittivities in functionalized carbon-nanotube/electroactive-polymer nanocomposites. Adv Mater 2007, 19: 852–857. 10.1002/adma.200600703
Jiang MJ, Dang ZM, Yao SH, Bai JB: Effects of surface modification of carbon nanotubes on the microstructure and electrical properties of carbon nanotubes/rubber nanocomposites. Chem Phys Lett 2008, 457: 352–356. 10.1016/j.cplett.2008.04.022
NanoAmor and Nanostructured & Amorphous Materials, Inc. [http://www.nanoamor.com] 
Viculis LM, Mayer OM, Hahn HT, Kaner RB: Intercalation and exfoliation routes to graphite nanoplatelets. J Mater Chem 2005, 15: 974–978. 10.1039/b413029d
Xiang JL, Drzal LT: Thermal conductivity of exfoliated graphite nanoplatelet. Carbon 2011, 49: 773–778. 10.1016/j.carbon.2010.10.003
Novoselov KS, Geim AK, Morozov SV, Jiang D, Zhang Y, Dubonos SV, Grigorieva IV, Firsov AA: Electric field effect in atomically thin carbon films. Science 2004, 306: 666–669. 10.1126/science.1102896
Kuilla T, Bhadrab S, Yao D, Kim NH, Bose S, Lee JH: Recent advances in graphene based polymer composites. Prog Polym Sci 2010, 35: 1350–1375. 10.1016/j.progpolymsci.2010.07.005
Stankovich S, Dikin DA, Dommett GH, Kohlhaas KM, Zimney EJ, Stach EA, Piner RD, Nguyen ST, Ruoff RS: Graphene-based composite materials. Nature 2006, 442: 282–285. 10.1038/nature04969
Tantis I, Psarras GC, Tasis DL: Functionalized graphene–poly(vinyl alcohol) nanocomposites: physical and dielectric properties. Express Polym Lett 2012, 6: 283–292. 10.3144/expresspolymlett.2012.31
Moazzami GM, Sharif F: Enhancement of dispersion and bonding of graphene-polymer through wet transfer of functionalized graphene oxide. Express Polym Lett 2012, 6: 1017–103. 10.3144/expresspolymlett.2012.107
Park S, Ruoff RS: Chemical methods for the production of graphenes. Nat Nanotechnol 2009, 4: 217–224. 10.1038/nnano.2009.58
McAllister MJ, Li JL, Adamson DH, Schniepp HC, Abdala AA, Liu J, Herrera-Alonso M, Milius DL, Car R, Prud’homme RK, Aksay IA: Single sheet functionalized graphene by oxidation and thermal expansion of graphite. Chem Mater 2007, 19: 4396–4404. 10.1021/cm0630800
Tashiro K: Ferroelectric Polymers: Chemistry, Physics and Applications. Edited by: Nalwa HS. New York: Marcel Dekker; 1995:62.
Hummers WS, Offeman RE: Preparation of graphitic oxide. J Am Chem Soc 1958, 80: 1339–1339. 10.1021/ja01539a017
Du FM, Fischer JE, Winey KI: Coagulation method for preparing single-walled carbon nanotube/poly(methyl methacrylate) composites and their modulus, electrical conductivity, and thermal stability. J Polymer Sci 2003, 41: 3333–3338.
Nakajima T, Matsuo Y: Formation process and structure of graphite oxide. Carbon 1994, 32: 469–475. 10.1016/0008-6223(94)90168-6
Nan CW, Shen Y, Ma J: Physical properties of composites near percolation. Annu Rev Mater Res 2010, 40: 131–151. 10.1146/annurev-matsci-070909-104529
Nan CW: Physics of inhomogeneous inorganic materials. Prog Mater Sci 1993, 37: 1–116. 10.1016/0079-6425(93)90004-5
Ansari A, Giannelis EP: Functionalized graphene sheet-poly(vinylidene fluoride) conductive nanocomposite. J Polym Sci, Part B: Polym Phys 2009, 47: 888–897. 10.1002/polb.21695
Cui LL, Lu XF, Chao DM, Liu HT, Li YX, Wang C: Graphene-based composite materials with high dielectric permittivity via an in situ reduction method. Phys Status Solidi (a) 2011, 208: 459–461. 10.1002/pssa.201026273
Pecharromán C, Esteban-Betegón F, Bartolomé JF, López-Esteban S, Moya JS: New percolative BaTiO3-Ni composites with a high and frequency-independent dielectric constant (훆 r ≈ 80000). Adv Mater 2001, 13: 1541–1544. 10.1002/1521-4095(200110)13:20<1541::AID-ADMA1541>3.0.CO;2-X
Pecharromán C, Moya JS: Experimental evidence of a giant capacitance in insulator-conductor composites at the percolation threshold. Adv Mater 2000, 12: 294–297. 10.1002/(SICI)1521-4095(200002)12:4<294::AID-ADMA294>3.0.CO;2-D
Yao SH, Dang ZM, Xu HP, Jiang MJ, Bai JB: Exploration of dielectric constant dependence on evolution of microstructure in nanotube/ferroelectric polymer nanocomposites. Appl Phys Lett 2008, 92: 082902. 10.1063/1.2870104
Dang ZM, Wang L, Yin Y, Zhang Q, Lei QQ: Giant dielectric permittivities in functionalized CNT/PVDF. Adv Mater 2007, 19: 852–857. 10.1002/adma.200600703
He F, Lau S, Chan HL, Fan J: High dielectric permittivity and low percolation threshold in nanocomposites based on poly(vinylidene fluoride) and exfoliated graphite nanoplates. Adv Mater 2009, 21: 710–715. 10.1002/adma.200801758
Dang ZM, Wu JP, Xu HP, Yao SH, Jiang MJ, Bai JB: Dielectric properties of upright carbon fiber filled poly(vinylidene fluoride) composite with low percolation threshold and week temperature dependence. Appl Phys Lett 2007, 91: 072912. 10.1063/1.2770664
Barrau S, Demont P, Peigney A, Laurent C, Lacabanne C: DC and AC conductivity of carbon nanotubes−polyepoxy composites. Macromolecules 2003, 36: 5187–5194. 10.1021/ma021263b
Jonscher AK: The ‘universal’ dielectric response. Nature 1977, 267: 673–679. 10.1038/267673a0
Dyre JC, Schrǿ der TB: Universality of ac conduction in disordered solids. Rev Mod Phys 2000, 72: 873–892. 10.1103/RevModPhys.72.873
Ezquerra TA, Connor MT, Roy S, Kulescza M, Fernandes-Nascimento J, Balta-Calleja FJ: Alternating-current electrical properties of graphite, carbon-black and carbon-fiber polymeric composites. Compos Sci Tech 2001, 61: 903–909. 10.1016/S0266-3538(00)00176-7
Connor MT, Roy S, Ezquerra TA J, Balta-Calleja FJ: Broadband ac conductivity of conductor-polymer composites. Phys Rev B 1998, 57: 2286–2294. 10.1103/PhysRevB.57.2286
Linares A, Canalda JC, Cagiao ME, Garcia-Gutierrez MC, Nogales A, Martin-Gullon I, Vera J, Ezquerra TA: Broad-band electrical conductivity of high density polyethylene nanocomposites with carbon nanoadditives: multiwalled carbon nanotubes and carbon nanofibers. Macromolecules 2008, 41: 7090–7097. 10.1021/ma801410j
He LX, Tjong SC: Alternating current electrical conductivity of high density polyethylene–carbon nanofiber composites. Euro Phys J E 2010, 32: 249–254. 10.1140/epje/i2010-10648-5
He LX, Tjong SC: Electrical conductivity of polyvinylidene fluoride nanocomposites with carbon nanotubes and nanofibers. J Nanosci Nanotech 2011, 11: 10668–10672. 10.1166/jnn.2011.3999
He LX, Tjong SC: Universality of Zener tunneling in carbon/polymer composites. Synth Met 2012, 161: 2647–2650. 10.1016/j.synthmet.2011.09.037
Zener C: A theory of the electrical breakdown of solid dielectrics. Proc Roy Soc A 1934, 145: 523–539. 10.1098/rspa.1934.0116
He LX, Tjong SC: Carbon nanotube/epoxy resin composite: correlation between state of nanotube dispersion and Zener tunneling parameters. Synth Met 2012, 162: 2277–2281. 10.1016/j.synthmet.2012.09.025
This work is supported by the project (R-IND4401), Shenzhen Research Institute, City Unversity of Hong Kong.
The authors declare that they have no competing interests.
LXH carried out the experiments, interpreted the data, and drafted the manuscript. SCT participated in the design of the study, material analysis, and revision of the whole manuscript. Both authors read and approved the final manuscript.