Research Article | Open Access
Hyeon Myeong Seo, Jin Ho Park, Trung Dung Dao, Han Mo Jeong, "Compatibility of Functionalized Graphene with Polyethylene and Its Copolymers", Journal of Nanomaterials, vol. 2013, Article ID 805201, 8 pages, 2013. https://doi.org/10.1155/2013/805201
Compatibility of Functionalized Graphene with Polyethylene and Its Copolymers
The compatibility of polyethylene (PE) with a functionalized graphene sheet (FGS), which was prepared by the thermal reduction of graphite oxide, was examined in this study. The dispersion of the FGS in the PE was improved as the molecular weight of the PE was decreased. The PE copolymers containing polar comonomers such as maleic anhydride or acrylic acid exhibited better compatibility with FGS than the PE homopolymers. The compatibility of the FGS with PE copolymers containing small amounts of comonomers, which have a solubility parameter slightly larger [up to approximately 0.5 (J/cm3)1/2] than that of PE itself, was better than the compatibility of both the PE and PE copolymers containing larger amounts of comonomers. The morphology, electric conductivity, and tensile properties of FGS/PE copolymer/PE nanocomposites showed that the copolymers with a solubility parameter slightly larger than that of PE effectively served as a compatibilizer in FGS/PE nanocomposites.
Nanocomposites composed of polymer matrices and nanosize fillers have attracted considerable technological and scientific attention because many physical properties of these matrix polymers, such as the electrical, mechanical, barrier, and flame-retarding properties, can be improved significantly with small amounts of fillers, in comparison to conventional composites. The unique properties of the nanocomposites stem not only from inherent properties of the nanofillers, but also from the maximized interfacial contact and interactions between the nanofiller and the polymer matrix. Therefore, the chemical structure of both the filler surface and the matrix polymer should be tailored to optimize the compatibility between the nanofiller and the matrix polymer in order to obtain a high performance nanocomposite [1–4].
Graphene, a single-atom-thick, two-dimensional sheet composed of sp2 bonded carbon atoms arranged in a honeycomb structure, holds great promise for the preparation of high performance nanocomposites because it has an extremely high surface area (as high as 2,600 m2/g), a high aspect ratio, and superior physical properties. It has a Young’s modulus of 1 TP, electrical conductivity of 6,000 S/cm, and thermal conductivity of 5,000 W/m·K [2–5].
Flake type graphenes can be prepared effectively in bulk by the rapid heating of graphite oxide (GO) powders because CO2 gas is generated through the thermal decomposition of the oxygen-containing groups of GO. Therefore, the thermally-reduced GO sheets are simultaneously exfoliated into individual graphene sheets by the instantaneous CO2 gas pressure build up in the gallery between the sheets . This method is economical and ecofriendly because it does not use any solvent for the reduction. These exfoliated graphene sheets are normally few-layer graphenes with specific surface areas ranging from 400 to 1500 m2/g, according to Brunauer, Emmett, and Teller (BET) measurements using nitrogen adsorption in the dry state [3, 7]. These exfoliated sheets are called functionalized graphene sheets (FGSs) because they contain some of the oxygen-containing functional groups including epoxy and hydroxyl groups even after the thermal reduction . Therefore, they disperse finely in polar solvents and polymers [7, 9–11].
Electrically conductive composites made of polymers and conducting fillers have been extensively investigated in the past few decades [1, 2, 4]. These materials can be utilized as antistatic or electromagnetic shielding materials to prevent damage to electronics by electrostatic discharge or electromagnetic interference. Polyethylene (PE) is a typical general-purpose polymer which displays good mechanical properties and high chemical resistance. Therefore it can be used effectively at various applications such as a packaging material for electronics if modified to have improved electrical conductivity [12, 13]. Graphene can be used as an efficient conductive filler for the modification, because it has high electric conductivity, surface area, and aspect ratio. However, graphenes are difficult to disperse in apolar polyolefins such as PE  and thus a high graphene loading fraction is necessary to provide a composite having the properly enhanced electrical conductivity. Normally a high filler loading deteriorates mechanical properties and processability and increases composite density. Therefore, proper modification of graphene, polyethylene, or another appropriate compatibilizer is necessary for fine dispersion of graphene. For example, Kuila et al. functionalized graphene with long alkyl groups by using the reaction of GO and long alkyl amine, followed by subsequent chemical reduction, in order to enhance the compatibility of graphene with linear low density polyethylene (LLDPE) . Some previous studies have focused on graphite nanoplatelet (GNP)/PE nanocomposites [15–19]. The GNPs prepared by exfoliation of intercalated graphite are normally thicker than FGS and have almost no oxygen-containing functional groups. However, to the best of our knowledge, there is no current study that focuses on FGS/PE nanocomposite. The compatibility of FGS with PE can be modulated by adjusting the structure of the PE or by using an appropriate compatibilizer. Therefore, in this study, we examined how the compatibility of PE can be adjusted by the molecular weight or by copolymerizing polar moiety such as acrylic acid or maleic anhydride. In addition, the compatibilizing effect of these copolymers in a FGS/PE nanocomposite was also examined, because a proper compatibilizer is in some cases more economical and facile for enhancing compatibility than complicated modification of FGS or PE.
2. Materials and Methods
Two kinds of PE were supplied from Hanwha Chemical, and two kinds of PE were purchased from Aldrich. Three kinds of poly(ethylene-co-acrylic acid) (PEA) and a poly(ethylene-graft-maleic anhydride) (PEM) were also purchased from Aldrich. The designation code and characteristics of the PEs and the copolymers are shown in Table 1. The number average molecular weight () and weight average molecular weight () were measured at 150°C by gel permeation chromatography (GPC, Waters, Alliance GPCV2000). Trichlorobenzene was used as the eluent, and polystyrene standard samples were used for the calibration of the molecular weight. The solubility parameters of the polymers in Table 1 were calculated by a group contribution method using Fedors’ data . Expandable graphite (ES350 F5, average particle size: 280 μm) purchased from Qingdao Kropfmuehl Graphite Co., Ltd. (China) was used for the preparation of the FGS.
2.2. Preparation of FGS
Graphite oxide (GO) was prepared using the Brodie method, as described in our previous paper . Elemental analysis demonstrated that the GO composition was C10O3.45H1.58. The GO was thermally reduced at 1100°C in a N2 atmosphere by decomposing the oxygen-containing groups of the GO and generating CO2 gas, thus splitting the GO into individual reduced graphene sheets [5, 6]. Elemental analysis demonstrated that the FGS composition was C10O0.78H0.38, indicating that some oxygen-containing functional groups, such as epoxide or hydroxyl groups, remained even after the thermal reduction . The surface area of the FGS, obtained by a BET measurement using nitrogen adsorption in the dry state, was 428 m2/g. The number average particle size of the FGS was measured using a particle size analyzer (Beckman Coulter LS 13 320) after suspension in ethanol and was determined to be 8.3 μm.
2.3. Preparation of FGS Nanocomposites of PE or PE Copolymer
The nanocomposites were fabricated with a 30 mL Brabender mixer (W30) connected to a Plasti-Corder (Plasti-Corder PL2100). All of the samples were melt compounded at 50 rpm for 10 min. The compounding temperature was 85°C for PEM and PEAs, 90°C for PE3 and PE4, and 100°C for PE1 and PE2. The compounded samples were compression molded at 80°C for PEM and PEAs, at 85°C for PE3 and PE4, and at 95°C for PE1 and PE2 with a pressure of 9.8 MPa, when necessary, for examination.
The nanocomposite films, approximately 30 μm thick, were imaged using an Eclipse LV100 (Nikon) optical microscope equipped with an Artcam-300MI-DS digital camera.
The electric conductivity of the compression molded samples was measured by a four-point probe system (CMT-SR 1000N, AIT Co. Ltd., of Republic Korea).
Differential scanning calorimetry (DSC) was carried out with a DSC Q20 from TA Instruments at a heating and cooling rate of 20°C/min with 10 mg of the sample. After loading at room temperature, the sample was heated to 130°C and then cooled to −40°C to measure the crystallization temperature () and heat of crystallization () of the PE or PE copolymer. It was then heated again to measure the melting temperature () and heat of fusion ().
The cryogenically fractured surface of the nanocomposite was observed using a field emission scanning electron microscope (FE-SEM, JEOL JSM-6500F).
The tensile properties were examined with a tensile tester (OTU-2, Oriental TM Co., Korea). The compression molded samples were cut into a microtensile specimen 27 mm in length, 10 mm in width, and 0.3 mm in thickness. The specimen was elongated at a rate of 50 mm/min.
3. Results and Discussions
3.1. Compatibility of FGS with PE or PE Copolymers
Optical microscopy was used to characterize the dispersion of FGS in a nanocomposite on a micrometer scale. Optical microscopy images of nanocomposites containing 0.5 parts FGS per 100 parts PE or PE copolymer (0.5 phr) are shown in Figure 1. The single-layer graphene is transparent because it only absorbs 2.3% of the light intensity, independent of the wavelength in the optical domain. Therefore, the single-layer graphene can barely be observed with an optical microscope. However, the transparency decreases when graphenes are stacked into multilayers or agglomerated. Figures 1(a) and 1(b) show that large black FGS aggregates are dispersed coarsely in PE1 and PE2. The black aggregates become smaller and some of them become translucent, as shown in Figures 1(c) and 1(d). These results show that the dispersion of FGS becomes finer when the molecular weight of the PE is smaller (see Table 1). The PE chain can more easily penetrate into the space between the FGS sheets during melt compounding when the PE chain length is shorter. In addition, the entropy gain accompanied with mixing, in (1), is larger if the PE molecular weight is lower, which reduces the change in Gibbs free energy accompanying the mixing, in (1), and thus contributes affirmatively to make the mixing thermodynamically feasible. These two kinetic and thermodynamic advantages of low molecular weight PE are the causes of the finer FGS dispersion in a low molecular weight PE matrix:
Figures 1(e) and 1(f) show that the dispersion of FGS is finer in PE copolymers than in PEs (Figures 1(a)–1(d)), and the number of translucent FGS aggregates is increased. This result indicates that the incorporation of a small amount of polar moieties, maleic anhydride, or acrylic acid, into the PE chain improved the dispersion of the FGS in the polymer matrix. However, the FGS dispersion became coarser when the acrylic acid content in the PE copolymer was increased further, as illustrated in Figures 1(g) and 1(h). In a two-component regular solution, the heat of mixing, is proportional to the square of the solubility parameter difference of the components. Accordingly, FGS and PE copolymers should have similar solubility parameters, which reduce the in (1) and thus contribute affirmatively in making fine mixing thermodynamically feasible . Therefore, the above result that FGS has optimum compatibility with PE copolymers that have a solubility parameter slightly higher [up to approximately ] than that of PE itself (see Table 1), rather than polymers which have higher or lower solubility parameters, suggests that the solubility parameters of FGS are similar with the optimally compatible PE copolymer.
Table 2 shows that the increase in the electric conductivity of PE1 and PE2 were marginal even with 3.0 phr FGS. However, the percolation threshold where the conductivity increases distinctly lies in the range of 0.5 to 1.5 phr for the nanocomposite of FGS with PE3, PE4, and PE copolymers. In the nanocomposites containing 1.5 phr FGS, the nanocomposites of PEM or PEA5 exhibit better conductivity than those of PE homopolymers or other PEAs. This result also shows that the dispersion of FGS in PE is improved effectively when the chain length is decreased or when PE copolymers have a solubility parameter slightly larger than that of PE homopolymer, as observed by optical microscopy.
In the nanocomposites, the crystallization of matrix polymer can be improved by the nucleating effect of dispersed filler. However, the interaction between the filler and matrix polymer, which hinders rearrangement for crystallization of the matrix polymer, can interfere with the crystallization [22, 23]. In the nanocomposites of PE1, PE2, PE3, and PE4 (Table 2), the , , and values generally exhibited an increase and then a decrease as the content of FGS was increased, although there were some exceptions. This result shows that the nucleating effect is dominant at a low FGS content, whereas the hindrance effect is dominant at a high FGS content in the composites. Similar crystallization behavior of PE had previously been reported for mica/high density polyethylene composites . Table 2 also shows that the increases in , , and are most evident in the FGS nanocomposite of PE4, which has the lowest molecular weight.
As shown in Table 2, all of the and values of the nanocomposites are less than those of the pristine polymers themselves for the nanocomposites of PE copolymers, although the molecular weights of most of them are similar or less than that of PE4. This result demonstrates that the interaction of the copolymers with FGS is stronger than that of PE due to the polar groups in the copolymer.
3.2. Compatibilizing Effect of the PE Copolymer in FGS/PE Nanocomposites
The compatibilizing effect of PE copolymers on FGS/PE3 nanocomposites containing 0.5 phr FGS was examined with optical microscopy. Figure 2 shows that the dispersion of FGS in the polymer matrix was improved compared to that of Figure 1(c) by the compatibilizing effect of the PE copolymers. The FGS dispersions are finer in Figures 2(a) and 2(b) than those in Figures 2(c) and 2(d), which demonstrates that the compatibilizing effect of PEM or PEA5 is better than that of PEA10 or PEA15. The compatibility of PEM or PEA5 with FGS was determined to be better than that of PEA10 or PEA15 (Figure 1). In addition, the compatibility of PEM or PEA5 with PE3 will be better than that of PEA10 or PEA15 because they have more similar chemical structures and consequently more similar solubility parameters (Table 1). These are the causes of the better compatibilizing effect.
The SEM image (Figure 3(a)) shows a large heterogeneous particle exhibiting coarse structure in the FGS/PE3 nanocomposite containing 1.5 phr FGS. The magnified image of this particle (Figure 3(b)) shows that this particle is an aggregate of crumpled FGSs. However, in Figure 3(c), the regions showing coarse structure are finely dispersed and, even in those regions, it is not easy to find an aggregate of crumpled FGS (Figure 3(d)). These SEM images also demonstrate that the dispersion of FGS in PE3 was improved by the compatibilizing effect of PEA5.
Table 3 shows that the electric conductivity of the FGS/PE3 nanocomposite containing 1.5 phr FGS increased when PE3 was replaced up to 10% by PEM or PEA5 due to the compatibilizing effect of the copolymers. However, it decreased again when 15% of the PE3 was replaced with the copolymers. Furthermore, the electric conductivity of the FGS/PE3 nanocomposite decreased even when less than 10% PE3 was replaced by PEA10 or PEA15 (Table 3). These results suggest the possibility that the copolymer phase, where FGS is preferentially localized, is separated at the high content of 15% for PEM or PEA5 and at an even lower content for PEM10 or PEA15 .
Table 4 shows that the improvements in the modulus and yield strength of PE3 by FGS are evident through the reinforcing effect of FGS even without any compatibilizer. Greater than twofold increases in the modulus and yield strength due to the addition of 3 phr FGS are much higher than the reinforcing effect observed in FGS/PP , paraffin-coated GNP/LLDPE , or alkyl chain-functionalized graphene/LLDPE nanocomposites . However, the elongation at break shows a different story. The elongation drastically decreases when reinforced with FGS, as in the FGS/PP nanocomposite . This result shows that the molecular rearrangement of PE3 toward the tensile axis during tensile deformation is strictly inhibited by FGS.
The tensile properties of the PE copolymers were too poor to carry out the tensile test. However, Table 4 shows that the reinforcing effect of FGS in the FGS/PE3 (1.5/100) nanocomposite was improved when 10% of PE3 was replaced with PE copolymers due to the compatibilizing effect of the replaced copolymers. This reinforcing effect presented in Table 4 was more evident by PEM or PEA5 than by PEA10 or PEA15, which also shows that PEA5 or PEM are better compatibilizers than PEA10 or PEA15 for the FGS/PE nanocomposite.
The compatibility of FGS with high molecular weight PE was so poor that the nanocomposite prepared by melt compounding did not exhibit the percolation threshold of electric conductivity even though the FGS content was as high as 3.0 phr. The compatibility was improved when the molecular weight of PE was decreased. Small amounts of copolymerized polar monomers, such as maleic anhydride or acrylic acid, also improved the compatibility. However, too much of the polar comonomer decreased the compatibility. The PE copolymers with a solubility parameter slightly larger [up to approximately 0.5 ] than that of PE itself showed the optimum compatibility.
The crystallization of the PE in the FGS/PE nanocomposite was enhanced by the FGS due to the nucleating effect. However, in the PE nanocomposites with a high FGS content or in the nanocomposites of the PE copolymers, the crystallinity of the PE or PE copolymers was reduced due to the increased interaction between the FGS and the matrix molecules. This interaction hindered the rearrangement of the matrix molecules for crystallization.
The morphology, electric conductivity, and tensile properties of the FGS/PE copolymer/PE nanocomposites showed that the PE copolymers with a solubility parameter slightly larger than that of PE itself effectively served as a compatibilizer for the FGS/PE nanocomposite.
This work was supported by Priority Research Centers Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Education (2009-0093818).
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