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Coatings 2018, 8(11), 387; doi:10.3390/coatings8110387
Preparation, Structure, and Properties of Surface Modified Graphene/Epoxy Resin Composites for Potential Application in Conductive Ink
Faculty of Printing, Packaging Engineering and Digital Media Technology, Xi’an University of Technology, Xi’an 710048, China
School of Mechanical and Precision Instrument Engineering, Xi’an University of Technology, Xi’an 710048, China
Fuli Institute of Food Science, Zhejiang University, Hangzhou 310058, China
Authors to whom correspondence should be addressed.
Received: 22 August 2018 / Accepted: 27 October 2018 / Published: 30 October 2018
The dispersity of graphene (GE) in the matrix has an important influence on the thermal, mechanical, and electrical properties of its derived composites. In this paper, surface modification with a silane coupling agent and a double injection method were used to improve the dispersity of GE in epoxy resin (EP). The thermal, mechanical, and electrical properties of modified graphene/epoxy resin composites (modified GE/EP) were investigated by the thermogravimetric analysis, a four-probe method, and the tensile and bending strength. The results reveal that these properties of the composites can be improved significantly by using the modified GE as the filler. The surface of the modified GE/EP composite was smooth when the curing temperature was 75 °C. The weight loss of the modified GE/EP composite was lower than that of pure EP. The tensile and bending strength of modified GE/EP-0.07 (0.07 wt % modified GE) reached 74.65 and 106.21 MPa, respectively. In addition, the resistivity of modified GE/EP-0.1 (0.1 wt % modified GE) decreased to 52 Ω·cm, which was lower than that of CB/EP-1 (1 wt % carbon black, 95 Ω·cm) and Ag/EP-50 (50 wt % Ag particles, 102 Ω·cm). It is worth noting that the percolation threshold of the modified GE/EP composites was 0.025 vol % modified GE. These results show that the modified GE/EP composites have a potential application in conductive ink when the modified GE is used as the conductive filler.
Keywords:surface modified graphene; thermal properties; mechanical properties; conductivity
In recent years, carbon black (CB), carbon nanotubes (CNTs), and graphene (GE) used as conductive fillers have attracted the attention of many researchers [1,2,3]. Due to the high Young’s modulus, excellent thermal property, superior conductivity, high surface area, high strength, and fast mobility of charge carries [4,5,6,7,8], the GE is regarded as the ideal reinforcing material for the composites. Moreover, GE/polymer composites exhibit superior performances in many aspects [9,10,11,12], and have been applied in sensors, super-capacitors, magnetic shielding, and memory devices . The GE has an important influence on the properties of the composites according to previous reports. Guo and co-workers found that the Young’s modulus and shear modulus of composites increased linearly with the increase of GE content . Chen and co-workers reported that the functionalized GE significantly improved the mechanical, thermal, and tribological properties of as-prepared composites . In addition, Alam and co-workers greatly enhanced the mechanical properties of composites by adding 1 vol % of GE . Moreover, Govorov and co-workers have reported that the conductivity of the GE/EP composites was correlated to their tensile stress after the loading of GE .
It is important to develop the preparation method of the GE and GE/polymer composites for exploring their applications. There are several methods that can be employed to synthesize GE, including the reduction of graphene oxide (GO) , mechanical exfoliation of graphite , chemical vapor deposition , and epitaxial growth . The reduction method is the most convenient compared to the others. To prepare GE/polymer composites, melt-blending , solution blending , and in-situ polymerization  are mostly employed. The dispersity of GE in the polymer matrix has an important influence on the properties of the composites, which could be improved by modifying the GE with compatible chemical groups for the polymer matrix. Moreover, the surface modification of GE can also improve the dispersity of GE in solvents [25,26]. Therefore, the covalent and non-covalent methods have been developed to modify GE. The non-covalent method can greatly preserve the original structure of GE, but the interactions between the GE surface and the modifiers are weak. Therefore, the covalent method is much more desirable in some application fields . In addition, it is interesting that the GE can be used as the conductive filler and epoxy resin as the binder for the conductive ink. Lee and co-workers reported that conductive ink containing the dispersed GE nanosheets showed a high stability . Wei and co-workers reported that the modified GE of various functional groups could improve the surface tension and adhesion of GE ink . Shulga and co-workers prepared an aqueous suspension of the composite using GO and humic acid, which was used as the ink to print the films with various thicknesses . Nemala and co-workers prepared a lower-cost conductive ink with few-layers GE, as a substitute for a Pt-based counter electrode, decreasing the cost significantly . These studies inspire the GE/EP composites to be further explored in conductive inks.
In this paper, we demonstrate an effective strategy to prepare surface modified GE, which can be used as an excellent filler for conductive ink. The GO was first modified by grafting with a silane coupling agent (KH-560) via the covalent method and then reduced into the GE form. The modified GE can be dispersed homogeneously in organic solvents. Subsequently, the modified GE/EP composites were prepared using a double injection method similar to the previous report . Thus, the dispersity of GE in epoxy resin can be improved significantly by associating the above two methods, and the GE content for preparing GE/EP composites with excellent properties can be reduced. The morphologies, structure, conductivity, thermal, and mechanical properties of as-prepared composites were investigated by different characterization methods. Interestingly, when 0.07 wt % modified GE was added, the tensile and bending strength of the modified GE/EP composite reached 74.65 and 106.21 MPa, respectively. When 0.1 wt % modified GE was added, the resistivity of the modified GE/EP composite decreased to 52 Ω·cm.
Natural graphite flakes (100 meshes) used in this paper were purchased from Qingdao Sunshine Co. Ltd. (Qingdao, Shandong, China). Hydrazine hydrate was purchased from Jinan Aoxiang Chemical Reagent Co. Ltd. (Jinan, China). Acetic acid (36 wt %) and ethanol were purchased from Sinopharm Chemical Reagent Co. Ltd. (Shanghai, China). KH-560 was purchased from Jinan Huanzheng Co. Ltd. (Jinan, China). Epoxy resin (E-44) was purchased from Xi’an Resin Factory (Xi’an, China). Ag particles were purchased from Guangdong Lingguang New Materials Co. Ltd. (Zhaoqing, China), and their average size was about 1.2 µm. Carbon black (1500 meshes) was purchased from Dongguan Tangxia Xiangyang Graphite Products Processing Plant (Dongguan, China).
2.2. Preparation of Modified GO
Graphene oxide (GO) derived from natural graphite was prepared by using the modified Hummers’ method according to previous reports [31,32]. The preparation of modified GO can be briefly described as follows. The GO (100 mg) powder was dispersed in 100 mL of ethanol by an ultrasonic dispersion with stirring for 3 h to form the dispersion. A mixture of KH-560 (20 mg) in 10 mL deionized water and 36 wt % acetic acid in 7 mL water was added to the GO dispersion for 30 min ultrasonic treatment. Then, the mixture was heat-treated with reflux condensing at 80 °C for 4 h. The products were collected by centrifuging at 10,000 rpm and further washed wish deionized water three times. Finally, the modified GO was dried in a vacuum oven at 80 °C for 24 h.
2.3. Reduction of Modified GO
The modified GO (50 mg) was dispersed in 100 mL of deionized water by an ultrasonic dispersion with stirring for 2 h. Then, 50 mL of pre-prepared 85% hydrazine hydrate was added to the modified GO dispersion. The mixture was heat-treated with reflux condensing at 95 °C for 24 h. Then, the products were separated by centrifuging at 10,000 rpm and washed with ethanol three times. Finally, the modified GE was obtained after drying in a vacuum oven at 80 °C for 24 h.
2.4. Preparation of Modified GE/EP Composites
The EP (5 g) was diluted in the mixed solution of 10 mL ethanol and 10 mL butanone. A certain amount of the modified GE was dispersed in 20 mL ethanol. Then, the above two mixtures were slowly injected into a beaker within 10 min by using the double injection method with magnetic stirring at 500 rpm. The tributyl phosphate (30 mg) and polyethylene glycol (50 mg) were added to the mixture containing the modified GE and EP with ultrasonic agitation for 2 h. Subsequently, ethylenediamine (0.6 g) and dibutyl phthalate (1.5 g) were added to the mixture. Eventually, the above mixture was poured into a polytetrafluoroethylene (PTFE) mold for curing for 4 h at different temperatures (70, 75, and 80 °C) and the modified GE/EP composites were obtained. The content of modified GE was set as 0.01, 0.03, 0.05, 0.07, and 0.1 wt %, respectively. In this paper, CB and Ag particles were also used as the fillers for the contrast, and the as-prepared composites were denoted as CB/EP and Ag/EP. The content of CB was 0.2, 0.4, 0.6, 0.8, and 1.0 wt %, respectively. In addition, the content of Ag particles was set as 10, 20, 30, 40, and 50 wt %, respectively. The as-prepared composite samples were denoted as modified GE/EP-x (x = 0.01, 0.03, 0.05, 0.07, and 0.1, respectively), CB/EP-y (y = 0.2, 0.4, 0.6, 0.8, and 1.0, respectively), and Ag/EP-z (z = 10, 20, 30, 40, and 50, respectively).
Fourier transform infrared spectra (FTIR) of the samples were performed on a NICOLET-10 infrared spectrometer (Thermo Fisher Scientific, Waltham, MA, USA) using KBr as the sample matrix in the range of 1000–3500 cm−1. The morphologies of the samples were investigated by a scanning electron microscope (SEM Hitachi SU8010, Tokyo, Japan). Raman spectra were obtained on a Raman spectrometer (Horiba JOBIN YVON HR800, Kyoto, Japan) and a 633 nm argon-ion laser was used for the excitation under ambient conditions. The conductivity of the composites was measured on a four-probe instrument (ST-2258C, Suzhou Jingge Electronic Co., Ltd., Suzhou, China), and the tested samples were cut into dimensions of 20 mm × 10 mm × 3 mm. The resistivity was calculated according to Equation (1):where L is the distance between the electrodes, A is the cross section area, and R is the measured resistance. The thermal stability of the samples was studied by thermogravimetric analysis (TGA) on a thermogravimetric apparatus (NETZSCH TG209, Selb, Germany) in an N2 atmosphere at the heating rate of 10 °C·min−1. The tensile and bending strength of the modified GE/EP, CB/EP, and Ag/EP composites were tested on a universal testing machine (SHIMADZU AGS-J, Kyoto, Japan) according to the standard test methods (ASTM D 638-08 Type I  and ASTM D 790-03 ). For the tensile strength test, the composite samples were cut into a dumbbell-like shape and the dimension was determined according to type I. In addition, the dimension of the composite samples was 127 mm × 12.7 mm × 3.2 mm for the bending strength test, the crosshead speed was 2 mm·min−1, and the loading was 5 kN. During the mechanical tests and the conductivity measurements, five samples for each composite were tested to get the average value. Error bars often represent one standard deviation of uncertainty. Since the average values were presented in the graph, the standard error is the appropriate measurement to calculate the error bars. The standard deviation and the standard error were calculated according to the Equations (2) and (3), respectively:where σ is the standard deviation, n is the number of samples (five in this paper), xi presents the measured sample values, μ presents the average values, and σs presents the standard error.
3. Results and Discussions
Fourier transform infrared spectra of as-prepared GO, modified GO, and modified GE are shown in Figure 1. The intensity of the adsorption peak at 1087 cm−1, ascribed to the stretching vibration of C–O in modified GO, is enhanced compared with GO. In addition, the adsorption peaks at 992 cm−1 and 1270 cm−1, ascribed to the stretching vibration of Si–O and the bending vibration of Si–C in the spectra of modified GO, respectively, indicate that the surface of GO is modified successfully by KH-560. The adsorption peak at 1735 cm−1 in the spectra of GO and modified GO was attributed to the stretching vibration of C=O. The intensity of the adsorption peak for C=O in the spectra of GE is lower than that of modified GO. Moreover, the intensity of the peaks at around 3426 and 3201 cm−1, attributed to the stretching vibration of –O–H, is weakened significantly. This may be due to the reduction of GO and the coupling between –O–H on the GO and –O–CH3 in KH-560.
The D, G, and G’ bands in the Raman spectrum of graphite correspond to the defects of the carbon layers, the graphitic layers, and the overtone of the D band, respectively. In addition, the intensity ratio of the D band to G band (ID/IG) (denoted as r) reflects the regularity of the crystalline structures in carbon materials [35,36]. As shown in Figure 2, the D band at around 1360 cm−1 and G band at around 1600 cm−1 can be observed in Raman spectra of GO, modified GO, and modified GE, corresponding to the characteristic bands of GE [37,38]. Moreover, the calculated r of GO, modified GO, and modified GE is 1.08, 1.26, and 1.34, respectively. The r value of modified GE is higher than that of modified GO, suggesting that new graphitic domains have been formed during the reduction of GO [39,40].
The as-prepared GO, modified GO, and modified GE dispersions in ethanol after standing for 2 h are shown in Figure 3. Precipitation was observed for the GO dispersion. However, no precipitation was seen for modified GO and modified GE dispersions, indicating that the surface modification of GO with KH-560 can improve the dispersity of GO in ethanol solution.
For investigating their thermal stability, the thermal degradation of as-prepared samples is evaluated in the range of 50–800 °C. The thermogravimetric and deriveative thermogravimetric curves of GO, modified GO, and modified GE are shown in Figure 4. Although the plots exhibit a similarity in shape, differences are observed in the rate of weight loss. The weight loss of GO has two stages: (1) the removal of water below 180 °C, and (2) the decomposition of the oxygen-containing groups below 800 °C. The total weight loss is 50.89 wt % in the range of 50–800 °C. The weight loss of modified GO below 190 °C is ascribed to the removal of water and solvent absorbed on the surface of modified GO. Then, the water and solvent molecules existing between modified GO sheets begin to be removed in the range of 190–270 °C. When the temperature is beyond 270 °C, epoxy groups and other oxygen-containing groups on the modified GO begin to decompose. The total weight loss of modified GO reaches 63.71 wt % in the range of 50–800 °C. The modified GE exhibits a lower weight loss rate (only 41.29 wt %) compared with GO and modified GO. This result demonstrates that there are more functional groups existing on the modified GO and they are decomposed during the heat-treatment. Therefore, the thermal stability of modified GE is the highest and that of modified GO is the lowest. In addition, a higher weight loss rate for modified GO also confirms that KH-560 has been successfully grafted on the surface of GO.
The morphologies of modified GE/EP composites filled with 0.05 wt % modified GE at different curing temperatures are shown in Figure 5. Lots of bubbles are observed on the surface of modified the GE/EP composite cured at 80 °C. This is due to the quick volatilization of the solvent and the curing agent at a higher temperature compared with other curing temperatures (70 and 75 °C). The bubbles on the surface of the modified GE/EP composite cured at 70 °C are obviously reduced (as shown in Figure 5b). However, the upper surface of the composite appears to be transparent. The reason for this may be that the curing velocity of EP is slow at a low curing temperature and the modified GE will settle in the bottom of the EP matrix with a low viscosity. The modified GE will agglomerate, and the phase separation between the fillers and EP matrix has appeared. Thus, the modified GE is distributed unevenly in the EP matrix and the upper surface of the modified GE/EP composites is transparent. As shown in Figure 5c, the surface of the modified GE/EP composite cured at 75 °C is smooth, indicating that the fillers of modified GE are distributed uniformly in the EP matrix and the appropriate curing temperature of 75 °C. In addition, the illustration diagram for preparing the modified GE/EP composite is shown in Figure 6.
Thermogravimetric analysis is also employed to investigate the thermal stability of the modified GE/EP composite. The weight loss curves of pure EP and modified GE/EP-0.05 in the range of 50–600 °C at a heating rate of 10 °C·min−1 are shown in Figure 7. The total weight loss of pure EP in the range of 50–600 °C is about 82 wt % and that of modified GE/EP-0.05 is only about 26 wt %. Compared with pure EP, the thermal stability of the as-prepared composite with modified GE can be improved when modified GE is added to the EP matrix. This is due to the fact that the modified GE with a high specific surface area hinders the removal of low molecular weight fragments in the as-prepared modified GE/EP composite during the thermal decomposition [9,41].
The influences of the fillers content on the mechanical properties of as-prepared modified GE/EP, CB/EP, and Ag/EP composites are shown in Figure 8. When the modified GE content increases from 0.01 to 0.07 wt %, the tensile strength of the as-prepared modified GE/EP composite increases from 58.31 to 74.65 MPa (as shown in Figure 8a). However, the tensile strength begins to decrease when the modified GE content exceeds 0.07 wt %. It can be inferred that the modified GE can improve the tensile strength of the EP matrix. Nevertheless, oxygen-containing groups remaining on the modified GE will react with the curing agent, which decreases the interfacial bonding between modified GE and EP . Tang and co-workers reported that the tensile strength of GE/EP composites was 58 MPa when the GE content was 0.025 wt % . Chhetri and co-workers found that the tensile strength of the functionalized RGO/EP composites with 0.2 wt % RGO could reach 59 MPa . The tensile strength (58.31 MPa) of the as-prepared modified GE/EP composites in this paper is comparable to that in previous reports, but a lower content of filler (0.01 wt %) is required. The tensile strength of the CB/EP composite increases when increasing the CB content and it reaches 60.83 MPa when the CB content is 1.0 wt % (as shown in Figure 8b). In addition, the tensile strength of the Ag/EP composite increases from 14.18 to 22.48 MPa when the Ag particles content increases from 10 wt % to 40 wt %, and then decreases to 18.72 MPa when the Ag particles content is 50 wt % (as shown in Figure 8c).
As shown in Figure 8d, the bending strength of the composites exhibits a similarity with their tensile strength. The bending strength of the modified GE/EP composite increases from 93.05 to 106.21 MPa when the modified GE content increases from 0.01 wt % to 0.07 wt %. Because the surface of the modified GE with containing-oxygen groups and KH-560 is wetted fully by EP molecules, the filler of modified GE and the matrix of EP can achieve close contact due to the wettability between them. However, the bending strength of the modified GE/EP composite decreases significantly when the modified GE content exceeds 0.07 wt %. As shown in Figure 8e, the bending strength of the CB/EP composite increases from 51.27 to 65.49 MPa when increasing the CB content. The bending strength of the Ag/EP composite increases from 21.43 to 34.7 MPa when the Ag particles content increases from 10 wt % to 40 wt % and then decreases to 28.03 MPa when it is 50 wt % (as shown in Figure 8f). When comparing the modified GE/EP composite with the CB/EP and Ag/EP composites, it can be concluded that a small amount of modified GE enables a significant improvement of the mechanical properties for the as-prepared composites. This is ascribed to the interfacial force between the filler of modified GE and the matrix of EP besides the homogeneous dispersion of the filler in the matrix . Thus, the fracture surface of the modified GE/EP composites is investigated to further interpret this phenomenon.
The fracture surfaces of the modified GE/EP composites with different contents of modified GE are shown in Figure 9. When the modified GE content is 0.03 wt %, there are no obvious sheets on the fracture surface of modified GE/EP-0.03, except for the circle regions (as shown in Figure 9a). When the modified GE content is 0.05 wt % and 0.07 wt %, many small sheets appear on the fracture surface of modified GE/EP-0.05 and modified GE/EP-0.07, where some cured EP is stripped from the fracture surface (as shown in Figure 9b,c). Compared with modified GE/EP-0.03, modified GE/EP-0.05, and modified GE/EP-0.07, the sheet surfaces of modified GE/EP-0.1 are smoother (as shown in Figure 9d). The fracture surface of the modified GE/EP composites also indicates that modified GE has been dispersed homogeneously in the EP matrix, agreeing with the results of the mechanical properties. Compared with CB/EP-0.4 and Ag/EP-20, the fracture surfaces of modified GE/EP composites are smoother, demonstrating that the compatibility between the modified GE and EP is better than that for the CB/EP and Ag/EP composites. Based on the mechanical properties and the fracture surface, it can be concluded that the modified GE is dispersed evenly in the EP matrix when the content is in the range of 0.03 wt %–0.07 wt %. Moreover, the appropriate content of the modified GE can improve the mechanical properties of as-prepared composites due to the favorable dispersity of the modified GE in the EP matrix and the strong interfacial force between the modified GE and EP. When the modified GE content is excessive, it is not conducive to improving the mechanical properties due to the inhomogeneous dispersion of the fillers in the matrix, and the fracture surface without stripped EP becomes smoother.
The conductivity of the as-prepared modified GE/EP, CB/EP, and Ag/EP composites is measured by using a four-probe conductivity meter, and the resistivity is shown in Table 1. The results show that the resistivity of modified GE/EP-0.01 is huge according to the fact that the value is beyond the limitation of the instrument. However, the resistivity of modified GE/EP-0.1 decreases to 52 Ω·cm due to the increase of the modified GE content. This result can be ascribed to the excellent conductivity of the modified GE and its homogeneous dispersion in the EP matrix. The modified GE sheets can make contact with each other and the intervals between them are very small, facilitating the formation of the continuous conductive path in the composites [45,46]. Thus, the as-prepared modified GE/EP composites in this paper exhibit excellent conductivity. The resistivity of the CB/EP composite decreases from 857 to 95 Ω·cm when increasing the CB content from 0.2 wt % to 1.0 wt %. The resistivity of the Ag/EP composite decreases from 763 to 102 Ω·cm when increasing the Ag particles content from 10 wt % to 50 wt %. These results indicate that the modified GE as the filler for the EP matrix is more efficient to improve the conductivity compared with CB and Ag particles. The percolation theory has been used to explain the conductive behaviors of GE-based composites . When the modified GE forms enough conductive paths to transmit electrons in the modified GE/EP composite, its conductivity is improved according to the percolation theory. In addition, the resistivity of the modified GE/EP, CB/EP, and Ag/EP composites with different contents of fillers is shown in Figure 10. The resistivity of the modified GE/EP composites decreases sharply in the range of 0.01 wt %–0.03 wt %. The resistivity of CB/EP and Ag/EP composites decreases sharply in the range of 0.2 wt %–0.4 wt % CB and 10 wt %–20 wt % Ag particles, respectively. Thus, it is inferred that the percolation threshold of modified GE/EP, CB/EP, and Ag/EP composites is in the range of 0.01 wt %–0.03 wt %, 0.2 wt %–0.4 wt %, and 10 wt %–20 wt % fillers, respectively.
For further estimating the percolation threshold of the modified GE/EP composite, the relation between the equated volume fraction of modified GE and the conductivity of as-prepared composites is showed in Table 2. Then, the experimental data is fitted according to the following power law model (Equation (4)):where is the conductivity of the composite, is the conductivity of the conductive filler, is the volume fraction of the filler, is the percolation threshold (the volume fraction), and t is a universal critical exponent. As shown in Figure 11, the percolation threshold of the as-prepared modified GE/EP composites is 0.025 vol % modified GE by fitting the measured data (in Table 2) into Equation (4). When the volume fraction of the modified GE reaches the percolation threshold of 0.025 vol %, the filler of the modified GE can form a conductive network to generate a leap increase in the conductivity of the composite. In addition, a linear relation is obtained for the log-log plot and it gives t = 1.8 with a regression coefficient of 0.94 (as shown in the insert of Figure 11). The universal critical exponent of t represents the dispersion dimension of the filler. The filler exhibits a random 3D dispersion when t ≥ 2 and it exhibits a random 2D dispersion when t < 2 [47,48]. Moreover, the conductivity of the as-prepared modified GE/EP composites in this paper is comparable to that in previous reports, as shown in Table 3. It can be found that the modified GE content in our paper as the conductive filler is less and the as-prepared composites can show desirable conductivity.
The modified GE/EP composites with an excellent mechanical property and conductivity were prepared successfully using the double injection method in this paper. The optimized curing temperature of the modified GE/EP composites with a smooth surface is 75 °C. In addition, the total weight loss of modified GE/EP-0.05 is 26 wt % in the range of 50–600 °C and it exhibits a high thermal stability compared with pure EP. When the modified GE content increases to 0.07 wt %, the tensile strength and bending strength of the composite can reach 74.65 and 106.21 MPa, respectively. When the modified GE content reaches the percolation threshold of 0.025 vol %, it can form a conductive network in the EP matrix to generate a leap increase in the conductivity of the composite. The conductivity of the modified GE/EP composite reaches 1.92 S·m−1 when the modified GE content is 0.12 vol %. In addition, the resistivity of CB/EP-1 and Ag/EP-50 is 95 and 102 Ω·cm, respectively. Compared with CB and Ag particles, the modified GE content in the composite is very low and it has a potential application in conductive ink as the conductive filler.
Conceptualization, Y.C. and C.F.; Methodology, K.X.; Software, J.S.; Validation, Y.C., C.F. and Q.Z.; Formal Analysis, Q.Z.; Investigation, L.A.; Resources, J.C.; Data Curation, Q.Z.; Writing—Original Draft Preparation, Q.Z.; Writing—Review and Editing, Y.C.; Visualization, D.L.; Supervision, C.F.; Project Administration, Y.C.; Funding Acquisition, C.F.
This research was funded by the National Natural Science Foundation of China (No. 51772243), Technology Innovation Programme of Xi’an University of Technology (No. 2016CX030), China Postdoctoral Science Foundation Funded Project (No. 2016M592824), the Science and Technology Plan of Yulin City (No. 2016-16-7), and the Science and Technology Plan of Beilin District (No. GX1710).
The authors thank Northwest institute of chemical industry for the measurement. The authors thank Zhen Wang and Mannan Yang for their technical assistance.
Conflicts of Interest
The authors declare no conflict of interest.
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Figure 1. FTIR spectra of GO, modified GO, and modified GE.
Figure 2. Raman spectra of GO, modified GO, and modified GE.
Figure 3. Dispersibility of GO, modified GO, and modified GE in ethanol after standing for 2 h.
Figure 4. (a) TG of GO, modified GO, and modified GE; (b) DTG of GO, modified GO, and modified GE.
Figure 5. Morphologies of the samples obtained at different curing temperatures: (a) 80 °C, (b) 70 °C, and (c) 75 °C.
Figure 6. Illustration diagram of the preparation process of the modified GE/EP composite via a double injection method.
Figure 7. TG of EP and modified GE/EP composite filled with 0.05 wt % modified GE.
Figure 8. Mechanical properties of the composites: (a) the tensile strength of modified GE/EP composites with different contents of modified GE, (b) the tensile strength of CB/EP composites with different contents of CB, (c) the tensile strength of Ag/EP composites with different contents of Ag particles, (d) the bending strength of modified GE/EP composites with different contents of modified GE, (e) the bending strength of CB/EP composites with different contents of CB, (f) the bending strength of Ag/EP composites with different contents of Ag particles.
Figure 9. SEM images of the fracture surfaces of the composites: (a) modified GE/EP-0.03, (b) modified GE/EP-0.05, (c) modified GE/EP-0.07, (d) modified GE/EP-0.1, (e) CB/EP-0.4, (f) Ag/EP-20.
Figure 10. The resistivity of as-prepared modified GE/EP, CB/EP, and Ag/EP composites with different contents of fillers.
Figure 11. The conductivity of as-prepared modified GE/EP composites. Inset: log-log plot of illustrating the percolation model.
Table 1. The resistivity of modified GE/EP, CB/EP, and Ag/EP composites with different contents of fillers.
|Modified GE||Modified GE/EP-0.01||1.84 × 105|
Table 2. The conductivity of modified GE/EP composites with different volume fractions of modified GE according to the conversion of the mass.
|Volume Fraction (vol %)||Conductivity (S·m−1)|
|0.012||5.4 × 10−4|
Table 3. The conductivity of the polymer composites filled with different fillers in previous reports.
|Filler||Polymer Matrix||Content||Conductivity (S·m−1)|
|GE ||Polystyrene||0.81 vol %||15.7|
|Epoxide-functionalized GE ||Epoxy||0.48 vol %||7.8 × 10−8|
|3D GE foam-PANI ||Epoxy||0.39 wt %||0.134|
|GE-coated PU foam ||Epoxy||0.9 wt %||2.46|
|[email protected] ||Epoxy||0.5 wt %||0.8|
|GE foam ||Epoxy||0.2 wt %||3|
|GE ||Polyamide||2.45 vol %||60|
|GE ||Epoxy||13 wt %||8.56|
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