Mechanical and Tribological Behavior of Graphene Oxide Supported Aramid Fiber Reinforced Epoxy Resin

1  Introduction

Epoxy resin (EP) is widely used in aerospace, automotive, and mechanical equipment [1–3] in mining due to its excellent mechanical properties, thermal stability, superior electrical insulation, and chemical resistance [4], as well as ease of processing and low cost, with applications in coatings, composites [5], casting materials [6], adhesives [7], fire retardant material [8], and injection molding materials. However, its high brittleness [9] and high friction coefficient [10] have limited its widespread application. To address this issue, adding other materials (such as sponges, fibers, etc.) to EP materials to improve the performance of the obtained composite materials is widely used. Fibers such as aramid fiber (AF) [11–14], carbon fiber (CF) [15–17], and basalt fiber (BF) [18–20] have been introduced into the epoxy resin to improve its performance. AF, in particular, is commonly used in polymer composites due to its low density, high specific strength, high specific modulus, and high-temperature resistance [21,22] developed aramid pulp/carbon fiber reinforced polybenzoxazine composites as high-performance friction materials with high thermal degradation temperature, glass transition temperature, and good wear resistance. Through the method of knitted aramid fiber, the fiber can form a support, so that it can play a greater role in the composite material [23,24].

To achieve the desired effect of fiber reinforcement, it is vital to improve the interactions between the matrix and the filler surface [25–28]. Therefore, methods for modifying the fiber surface have been developed, including surface etching [29], plasma processing [30], and coating [31,32], to improve the performance of the fiber/resin composite. Surface etching involves chemically etching the fiber surface, which affects the fiber’s properties. Reference [33] used LiF/HCl solution etching Ti3AlC2 to synthesize Ti3C2Tx MXene and it was utilized for surface modification of polyethylene (PE) fiber to form a stable absorptive buffer layer on the fiber interface. Inspired by the strong adhesion ability of polydopamine (PDA) originating from the mussel secretory gland, dopamine. Sun et al. [34] used a PDA coating quickly and uniformly formed on CF through the rapid synthesis under anoxic conditions by ultrasound, to change the interface of the composite. To improve the frictional properties of the composites, nanomaterials such as graphene oxide (GO) [35], carbon nanotubes (CNF) [19], and reduced graphene oxide (rGO) [36] are often added. Compared to CNF and rGO, GO contains carboxyl (-COOH), hydroxyl (-OH), and epoxy (-O-) functional groups [37], which can enhance the chemical interactions between the polymer matrix and the nanomaterials. Thus, GO can effectively improve the tribological properties of composites. Wang et al. designed a porous 3D graphene lubricant using polyurethane (PU) foam carrier, and then poured monomer-casting polyamide 6 (MCPA6) into the 3D graphene lubricant to prepare a self-lubricating composite material [38]. However, direct coating of GO on the fiber surface is challenging [39]. Feng et al. [40] adhered PDA-modified reduced graphene oxide (PDA-rGO) to the nickel foam skeleton; the self-polymerized PDA layer binds GO to the fiber through chemical interactions and improves the tribological properties of the composites [41]. According to published reports, there is no report on the use of polydopamine modification to load GO onto knitted aramid fibers to improve the properties of epoxy resin.

Based on the above survey, in this study, the tribological properties of EP were improved by incorporating a knitted aramid fiber/polydopamine/graphene oxide woven support framework into the EP matrix. AF can improve the mechanical properties of the matrix and reduce the volume wear rate. Coating the surface of AF by PDA can make the surface of AF load other substances. We selected GO as the modified material on account of GO was two-dimensional functional material with certain lubrication properties. The purpose of this study was to investigate the effect of PDA and GO on the properties of knitted aramid fiber composites, and to provide a basis for future research.

2  Experiments

2.1 Materials

The aramid fiber is from Dongguan Shenglan Rope Belt Weaving Co., Ltd. (Dongguan, China). Dopamine hydrochloride (PDA; C8H11NO2·HCl) from Hefei BASF Biotechnology Co., Ltd. (Hefei, China). Tris (Tris; NH2C(CH2OH)) was purchased from Tianjin Deen Chemical Reagent Co., Ltd. (Tianjin, China). Graphite flakes (800 mesh), sulfuric acid (95%–98%), potassium permanganate were purchased from Qingdao Tianshengda Graphite Co., Ltd. (Qingdao, China), Luoyang Haohua Chemical Co., Ltd. (Luoyang, China), Tianjin Chemical Co., Ltd. (Tianjin, China). Hydrogen peroxide (30%), sodium hydroxide (analytically pure), sodium nitrate (analytically pure) and hydrochloric acid (37%) were all from Tianjin Damao Chemical Reagent Factory (Tianjin, China). E-44 epoxy resin and 650 curing agent (polyamide resin) are provided by Dingyuan Danbao Resin Co., Ltd. (Zhenjiang, China). Unless otherwise stated, all chemical reagents and solvents are used as received without further purification.

2.2 Knitted AF Modified and Load GO

2.2.1 Preparation of PDA Modified Knitted AF

Aramid fabric with 30 mm × 30 mm aramid rope was knitted by hand knitting method. With 0.5 g dopamine hydrochloride, 0.3 g TRIS configuration solution 250 mL, with 10% HCl solution to adjust the solution pH = 8.5, get 2 g/L PDA solution. The treated aramid fabric was then placed in the solution for 24 h and continuously stirred. The soaked fabric was rinsed with distilled water for three times and dried at 60°C for 6 h to obtain AF/PDA.

2.2.2 Preparation of GO and AF/PDA Load GO

Graphene oxide was prepared by the improved Hummers method [42] and graphene oxide was prepared by ultrasonic method.

The GO solution was prepared according to the required graphene oxide concentration, and the AF/PDA fabric obtained in the previous step was placed in it, soaked for 24 h, and dried at 80°C for 10 h to obtain AF/PDA/GO.

2.3 Preparation of EP/AF/PDA/GO

Put the cleaned beaker on the balance, put it into the rotor, weigh a certain amount of epoxy resin, then add ethanol in proportion, stir it with a magnetic stirrer, and then weigh the polyamide resin in proportion, and stir it evenly. After ultrasonic defoaming for 30 min in an ultrasonic cleaner, it was poured into a mold with an AF/PDA/GO support skeleton, dried at 45°C for 4 h, and then placed for 2 d to solidify and demould. The preparation process of EP/AF/PDA/GO composites is shown in Fig. 1a.

Figure 1: (a) Schematic diagram of EP/AF/PDA/GO composites preparation process, (b) Interaction mechanism between different components

2.4 Characterizations and Instruments

The worn surfaces of EP, EP/AF, EP/AF/PDA, EP/AF/PDA/GO composites were characterized by scanning electron microscopy (SEM, JSM-IT100, JEOL Inc., Tokyo, Japan). FTIR analysis was performed using an IRTracer-100 spectrometer (FTIR, Nicolet iS50, Thermo Scientific, Huntham, MA, USA) to characterize the composite and modified fiber groups in the range of 400–4000 cm−1. The three-dimensional surface morphology of the wear track of EP composites was measured by scanning electron microscopy (SEM, JSM-IT100, JEOL Inc., Tokyo, Japan).

2.5 Mechanical and Tribological Tests

The hardness of the samples was tested by Shore hardness tester (LXD-D, Dongguan Three Measuring Tools Co., Ltd., Dongguan, China) according to GB 2411-80. Each sample was tested 5 times, and the average value was taken as the hardness. According to GB/T 1040, 224–228, the samples were made into dumbbell type, 3 in each group, a total of 4 groups. The tensile strength and modulus of EP and its composites were tested by electronic universal testing machine controlled by CMT4503 microcomputer (CMT4503, Master Industrial Systems Inc., Shenzhen, China), and the tensile speed was set to 2 mm/min. The tensile strength and modulus values are calculated according to the following equations:

σ=pb−h(1)

E=ΔσΔε(2)

where σ(MPa) is the tensile strength, p(N) is the breakage load, b(mm) is the sample width, and h(mm) is the sample thickness; E is the tensile modulus, Δσ indicates the increase in stress on the specimen, Δε is the strain of the tensile specimen.

According to the standard test method of GB 3960–1983, the friction and wear properties of EP composites were evaluated on MM-2HL ring block tester (MM-2HL, Jinan HengXu Testing Machine Technology Co., Ltd., Jinan, China). The sample size is 30 mm × 7 mm × 6 mm, and the dual material is carbon steel (45#) ring. Before the test, the surface of the dual material was polished with 1000# sandpaper and washed with ethanol. The friction test was carried out at room temperature. The normal load was 40 N and the sliding speed was 0.21 m/s. Three friction and wear tests were carried out on each sample. After the test, the wear volume ΔV(mm3) of the specimen is calculated according to the following formula [23]:

ΔV=B⋅[πR2180⋅arcsin⁡(b2R)−b2R2−b24](3)

In the formula, B(mm) is the width of the specimen, R(mm) is the radius of the carbon steel ring, and b(mm) is the width of the wear scar. The specific wear rate W(mm3/Nm) was calculated according to the following formula:

W=ΔVLd(4)

In the formula, L(N) is the load and d(m) is the total sliding distance.

3  Result and Discussion

3.1 Microstructure of the AF with Different Surface Treatments

Fig. 1b shows the physical and chemical changes on the surface of AF. During the preparation process, the polydopamine coating was coated on the surface of AF through the polymerization reaction of dopamine, so that there were a large number of active groups on the surface of AF. After that, graphene oxide was fixed on the surface of AF by physical and chemical action by soaking graphene oxide solution, to obtain AF/PDA/GO. Fig. 2a is the electron microscope image of AF after cleaning without modification. It can be seen from the image that the surface of AF itself is smooth and composed of multiple strands of fibers. The surface roughness is low, resulting in poor bonding with the matrix. During the friction process, the matrix is easy to peel off, resulting in a large amount of friction and wear, reducing the service life of the parts. Fig. 2b is the AF electron microscope image after loading PDA [23,43]. The surface is loaded with a large number of polydopamine molecules, which can effectively increase the roughness of the AF surface and improve the combination of AF and EP. It has an effective effect on reducing the wear of the matrix during the friction process. At the same time, it has a positive effect on the loading of GO. It is difficult for flake GO to be directly loaded onto the AF surface. This situation can be improved by introducing PDA. Fig. 2c shows the surface of AF/PDA after the introduction of GO [44], and it can be observed that GO is loaded on the surface of the fiber.

Figure 2: SEM of (a) AF, (b) AF/PDA, (c) AF/PDA/GO

The infrared spectra of EP and its composites are shown in Fig. 3a. It can be seen from the figure that the broad peak at 3300–3600 cm−1 of pure epoxy resin is related to the-OH stretching vibration of EP. At 830 cm−1, the C-O-C stretching vibration is the characteristic peak of the epoxy group [45], and the peaks at 2933 and 2852 cm−1 are mainly C-H stretching vibration. The peaks at 1500 and 1600 cm−1 are mainly the C=C stretching vibration of aromatic hydrocarbons [46]. The peaks at 1251, 1182, and 1045 cm−1 are mainly C-O stretching vibration. The peak at 553 cm−1 is an OH stretching vibration. Compared with pure EP, the modified matrix did not change significantly, which may be because the epoxy resin itself has a large number of epoxy groups, thus masking the characteristic peaks of the added modified substances. We conducted infrared tests on unpolished fibers and modified fibers, and the results are shown in Fig. 3b. The infrared characteristic peaks of aramid fiber are very similar to those of PDA and GO, which makes it difficult to distinguish the results.

Figure 3: FTIR spectra of (a) EP, EP/AF, EP/AF/PDA and EP/AF/PDA/GO, (b) AF, AF/PDA and AF/PDA/GO

3.2 Mechanical Properties of EP and Its Composites

In order to explore the mechanical properties of the composite material, the surface hardness of the composite material was measured by a hardness tester, and the results were shown in Fig. 4. From the data of Fig. 4, the hardness of pure EP is about 56 SHD [23,47]. It can be seen that the hardness of the composite material increases slightly after adding AF, and the introduction of PDA and GO has no significant effect on the hardness of the composite material.

Figure 4: Hardness of EP, EP/AF, EP/AF/PDA and EP/AF/PDA/GO composite surfaces

In order to further explore, we conducted a tensile test on the composite material, and the experimental results are shown in Fig. 5a,b. Fig. 5a is the tensile strength and tensile modulus of the composite material. From the figure, it can be seen that after AF is added to the composite material, it’s tensile strength and modulus are greatly improved [47,48]. The main reason is that AF has excellent mechanical properties, which can effectively prevent the direct fracture of the composite material during the tensile process. After the introduction of PDA, GO, the tensile strength of the composites decreased slightly, but it was still higher than that of pure EP, and the tensile modulus decreased to some extent. Fig. 5b is the stress-strain curve of the composite material. The pure EP breaks directly during the tensile process. After adding AF, the mechanical properties of the composite material are greatly improved, which proves that AF plays a significant role in improving the mechanical properties of the composite material. However, the tensile strength and modulus of the composites decreased after the addition of PDA and GO, which needs further study.

Figure 5: (a) Tensile strength and tensile modulus of different EP composites, (b) Stress-strain curve of different EP composites

3.3 Tribological Properties of EP and Its Composites

Fig. 6a is the change curve of friction coefficient with time of pure EP and modified composite under the condition of load 40 N and rotation speed 100 r/min. The friction coefficient of pure EP tends to be stable after the friction time reaches 300 s, and the friction coefficient is about 0.75 when it is stable [23,47]. After the introduction of woven AF as a support, the friction coefficient of EP/AF is lower than that of pure EP, but AF is difficult to play a good lubrication effect, so its friction coefficient is constantly fluctuating and growing, and it is difficult to achieve a stable friction stage. After the introduction of dopamine molecules, the components of the composite are tightly bonded. After 250 s of friction process, the friction coefficient reaches a stable state, about 0.50. Compared with pure EP, the friction coefficient is reduced to a certain extent, and the friction coefficient of EP/AF is basically the same. By introducing GO, the friction coefficient of the composite material has decreased significantly, reaching a stable friction state after 250 s, and the friction coefficient is about 0.42. It can be seen that GO, as a two-dimensional material, can play a certain role in reducing the friction coefficient of the composite material and can effectively reduce the friction coefficient of the composite material. Fig. 6b is specific wear rate and average friction coefficient of EP and its composites. It can be seen from the diagram that the friction coefficient and wear rate of the composite material decreased after the addition of AF. The friction coefficient and wear rate of the composite material after the addition of AF modified by PDA did not change significantly compared with EP/AF. However, after the introduction of GO, the friction coefficient and wear rate of the composite material were further reduced to achieve the best effect of the system. Compared with pure EP, the average friction coefficient is reduced by 48.36%, and the wear rate is reduced by 96.99%.

Figure 6: The tribological properties of EP and its composites: (a) coefficient of friction, (b) specific wear rate and average friction coefficient (40 N, 0.21 m/s)

3.4 Morphology of Wear Surface of EP and Its Composites

In order to study the tribological mechanism of pure EP and EP/AF/PDA/GO composites in detail, SEM images were taken at the wear scars of the corresponding composites. The results are shown in Fig. 7. Fig. 7a is the SEM image of the wear surface of pure EP. It can be seen that there are a large number of wear debris on the surface, as well as a large area of spalling due to friction [47]. After adding AF, it can be seen from Fig. 7b that the wear debris is reduced, and the wear surface becomes more flat. It can be seen that AF fiber has wear-resistant characteristics [49], and the wear debris on the wear surface is reduced. After the introduction of PDA, it can be seen from Fig. 7c that the peeling phenomenon of the matrix on the wear surface of the composite material is reduced, the fiber and the matrix are closely combined, and the amount of wear debris is further reduced compared with EP/AF. Fig. 7d is the wear surface of EP/AF/PDA/GO composites. It can be seen that the wear surface is smooth, and GO has a certain lubricating effect to fill the matrix wear caused by friction and wear. Compared with pure EP, the rough state of the friction surface is effectively improved.

Figure 7: SEM of (a) EP, (b) EP/AF, (c) EP/AF/PDA, (d) EP/AF/PDA/GO worn-out surface

In order to further explore the wear surface morphology of the composite material, the three-dimensional scanning of the wear surface was carried out [23]. The imaging results are as shown in Fig. 8. Fig. 8a shows the three-dimensional morphology of the wear scar surface of pure EP. It can be seen that the depth of the wear scar is deep, and there are a lot of wear debris generated by friction on the surface. Fig. 8b is the three-dimensional morphology of the wear scar surface of EP/AF, which is improved compared with pure EP, and the friction surface is relatively flat. After adding AF as a support, the wear depth is reduced. It can be seen that the addition of AF can improve the wear resistance of the composite material. Fig. 8c shows the wear scar surface of EP/AF/PDA. The wear scar is relatively shallow, and the friction surface is improved compared with EP/AF. The gully caused by surface friction is filled to a certain extent, it is proved that PDA can effectively improve the interfacial bonding between EP and AF in the composites, thus improving the tribological properties of the composites. Fig. 8d is the friction surface of EP/AF/PDA/GO composite material. The surface has a certain roughness, which may be that the GO sheet material plays a certain role on the friction surface.

Figure 8: 3D profile of composite wear surface of (a) pure EP, (b) EP/AF, (c) EP/AF/PDA, (d) EP/AF/PDA/GO

Based on the above data, the tribological mechanism model diagram of EP and its composites is drawn in Fig. 9. It is speculated that the addition of AF fiber can reduce the wear rate of the composite material when the steel ring contacts with the composite material during the friction process. The GO loaded on the AF surface moves to the friction contact surface during the friction process, which plays a role in anti-friction and anti-wear. The GO synergistic with AF, filling the wear position of the friction surface, and reducing the wear of the composite material [44,50], so as to achieve good tribological properties. The results show that GO and AF play a great role in improving the tribological properties of EP composites.

Figure 9: Schematic diagram of the friction reduction of EP composite

4  Conclusion

In this study, we weaved a single AF and then grafted a large number of active groups on the surface of the AF by coating a polydopamine coating on the braided fiber. GO is fixed on the surface of aramid fiber through the interaction with the active groups on the surface of aramid fiber, which plays a certain role in the friction process. It was found that the tribological properties of the EP/AF/PDA/GO composite have great improvement. Compared with pure EP, the friction coefficient is reduced by 48.36%, and the volume wear rate is reduced by 96.99%. The wear surface of the modified material has shallow wear marks, low roughness, and is relatively smooth. Also, we found that the introduction of AF greatly improves the mechanical properties of the composites. The addition of AF improved the hardness, tensile strength, and tensile modulus of the composites. In summary, AF/PDA/GO can be added into the matrix as a support to play a good anti-friction and wear-resistant effect.

Acknowledgement: Prof. Bingli Pan and Prof. Hongyu Liu are very grateful for their guidance and revision of the paper, as well as Yuxuan Zhou’s comments and suggestions on the research process of the paper, Xiaofan Ding and Xinyu Yuan‘s experimental help.

Funding Statement: This work was supported by the Natural Science Foundation of Henan Province (No. 232300421206), National Natural Science Foundation of China (No. 51675162) and Student Research Training Program (2024192, 2023117).

Author Contributions: Study conception and design: Yuanyuan Feng, Bingli Pan; data collection: Xiaofan Ding, Xinyu Yuan; analysis and interpretation of results: Yuanyuan Feng, Yuxuan Zhou; draft manuscript preparation: Bingli Pan, Hongyu Liu. All authors reviewed the results and approved the final version of the manuscript.

Availability of Data and Materials: The datasets generated during and/or analyzed during the current study are available from the corresponding author on reasonable request.

Ethics Approval: Not applicable.

Conflicts of Interest: The authors declare that they have no conflicts of interest to report regarding the present study.

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