CN117757263A - High-strength low-friction wear-resistant resin matrix composite material and preparation method and application thereof - Google Patents
High-strength low-friction wear-resistant resin matrix composite material and preparation method and application thereof Download PDFInfo
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Abstract
The invention provides a high-strength low-friction wear-resistant resin matrix composite material, and a preparation method and application thereof, and belongs to the field of composite materials. According to the invention, the irradiation modified polytetrafluoroethylene nano powder is used as a solid lubricant, and the multi-scale chopped carbon fiber is used for compounding and filling in the PPS composite material to construct a compact filler reinforced network structure, so that the obtained composite material has excellent mechanical property and heat conduction property, and simultaneously has excellent low-friction wear-resisting function. The high-strength low-friction wear-resistant resin matrix composite material has very wide application prospect in the fields of aerospace, transportation, electronic devices, high-end mechanical equipment and the like, and can be used for preparing parts such as wear-resistant bearings, self-lubricating parts, mechanical gaskets and the like used under dry friction and other application working conditions.
Description
Technical Field
The invention belongs to the field of composite materials, and particularly relates to a high-strength low-friction wear-resistant resin matrix composite material, and a preparation method and application thereof.
Background
It is well known that frictional wear phenomena are everywhere visible in daily life and industrial production. In some cases, friction plays a critical role in the proper operation of the mechanical system, but periodic friction often results in significant energy loss and material wear, thereby greatly shortening the service life of the mechanical equipment and related components. Therefore, reducing the adverse frictional wear in various forms, improving the self-lubricating wear resistance of materials has become an important measure for saving energy and improving the reliability of mechanical equipment. At present, the resin-based composite material has the advantages of light weight, low cost, high specific strength, easy processing and forming and the like, so that the resin-based composite material gradually replaces materials such as metal, ceramic and the like in a plurality of fields, and is widely applied to the fields of tribology, such as gears, bearings, pulleys, medical equipment and the like.
Polyphenylene Sulfide (PPS) is a linear thermoplastic resin with high rigidity and high crystallinity, and is considered as the sixth largest special engineering plastic. PPS and its composites are widely used in the fields of aerospace, transportation, mechanical parts, electronics, household appliances, etc., by virtue of its excellent thermodynamic properties, electrical properties, dimensional stability and chemical resistance. However, since PPS itself has a high friction coefficient (0.45-0.57) and a high wear rate (3.55X10) -3 mm 3 Nm), the prepared parts are easily subjected to severe friction and wear due to the influence of extreme load, frequent start-stop operation and the like in the use process, so that the parts cannot meet the requirements of friction structural members in mechanical equipmentThe use requirement. Therefore, the friction and wear resistance of PPS is improved to prepare the high-strength low-friction wear-resistant functional composite material and the parts, so that the PPS has important scientific value and application prospect.
In order to promote the application of PPS and composite materials thereof in the field of mechanical engineering, a great deal of attempts are made by students at home and abroad to modify the friction and wear of the PPS and the composite materials, however, the thermodynamic property of the materials and the tribological property of the materials under the condition of extreme load are mostly ignored by the current technical method, so that the materials cannot meet the performance requirements of mechanical equipment parts in practical application. The invention adopts aerogel, reinforcing fiber and liquid phase auxiliary agent to carry out mixed filling modification on PPS, but the improvement degree of self-lubricating performance is limited (friction coefficient is 0.178 at the minimum), and meanwhile, the mechanical strength and the heat conduction performance are not ideal. The invention discloses an isolated network composite material containing hybridized nano filler, a preparation method and application thereof, wherein the isolated network composite material is prepared by co-depositing grafted carbon nano tubes on the surface of PPS by utilizing self-polymerization of dopamine or copolymerization of dopamine polyether imide, and then coating silicon carbide nano particles to prepare the high-heat-conductivity PPS-based composite material, and friction and abrasion of PPS are reduced by greatly reducing friction temperature, but the improvement degree of the method on the friction and the chemical properties of PPS is limited (the friction coefficient is 0.193 at the minimum and the specific abrasion rate is 2.50x10) -5 mm 3 /Nm). The invention mainly adopts graphene powder, basalt fiber, curing agent and vulcanizing agent to modify PPS, and the friction coefficient and the wear rate of PPS are greatly reduced by the method, but the mechanical strength is poor, so that the PPS is difficult to play a role in practical application. Therefore, development of the self-lubricating wear-resistant resin matrix composite material with excellent mechanical strength and high heat conduction performance and a preparation method thereof have important scientific value and application prospect.
Disclosure of Invention
The invention aims to provide a high-strength low-friction wear-resistant resin matrix composite material, and a preparation method and application thereof.
The invention provides a high-strength low-friction wear-resistant resin matrix composite material which is prepared from the following raw materials in parts by weight: 10-200 parts of resin matrix, 5-80 parts of solid lubricant and 1-60 parts of carbon fiber; the carbon fiber comprises a carbon fiber A and a carbon fiber B, wherein the average length of the carbon fiber A is 0.1-3mm, the average diameter of the carbon fiber A is 1-20 mu m, the average length of the carbon fiber B is 1-20mm, and the average diameter of the carbon fiber B is 1-20 mu m.
Further, the high-strength low-friction wear-resistant resin matrix composite is prepared from the following raw materials in parts by weight: 20-100 parts of resin matrix, 10-50 parts of solid lubricant and 10-40 parts of carbon fiber; the carbon fiber consists of carbon fiber A and carbon fiber B, wherein the weight ratio of the carbon fiber A to the carbon fiber B is (1-3): 1-3.
Further, the high-strength low-friction wear-resistant resin matrix composite is prepared from the following raw materials in parts by weight: 56 parts of a resin matrix, 24 parts of a solid lubricant and 20 parts of carbon fibers; the carbon fiber consists of carbon fiber A and carbon fiber B, wherein the weight ratio of the carbon fiber A to the carbon fiber B is 1:3.
Further, the average length of the carbon fiber A is 0.2-1mm, the average diameter is 2-10 mu m, the average length of the carbon fiber B is 2-10mm, and the average diameter is 2-10 mu m.
Further, the average length of the carbon fiber A was 0.3mm, the average diameter was 6 μm, the average length of the carbon fiber B was 3mm, and the average diameter was 7. Mu.m.
Further, the resin matrix is a thermoplastic resin; the solid lubricant is polytetrafluoroethylene or a derivative thereof; the carbon fiber is polyacrylonitrile-based or pitch-based chopped carbon fiber.
Further, the resin matrix is polyphenylene sulfide; the derivative of polytetrafluoroethylene is irradiation modified polytetrafluoroethylene, and the carbon fiber is polyacrylonitrile-based chopped carbon fiber.
The invention also provides a method for preparing the high-strength low-friction wear-resistant resin matrix composite material, which comprises the following steps: drying raw materials, premixing, and melt blending. The high-strength low-friction wear-resistant resin matrix composite prepared by the method can be prepared by adopting conventional thermoplastic processing means such as hot press molding, calendaring molding, (micro) injection molding and the like.
Further, the molding is injection molding.
The invention also provides application of the high-strength low-friction polymer wear-resistant resin matrix composite material in the fields of aerospace, transportation, electronic devices and high-end mechanical equipment.
The high-strength low-friction wear-resistant resin matrix composite can be used for preparing parts such as wear-resistant bearings, self-lubricating parts, mechanical gaskets and the like used under dry friction and other working conditions.
Compared with the prior art, the invention has the following beneficial effects: according to the invention, the irradiation modified polytetrafluoroethylene nano powder is used as a solid lubricant, and a compact filler reinforcing network is constructed in the PPS composite material by utilizing multi-scale chopped carbon fiber compound filling, so that the obtained composite material has excellent mechanical property and heat conduction property, and meanwhile, the formation of a high-lubrication transfer film on the surface of an accessory is promoted, and further, excellent tribological properties can be shown under different PV working conditions. The high-strength low-friction wear-resistant resin matrix composite material has wide application prospects in the fields of aerospace, transportation, electronic devices, high-end mechanical equipment and the like, and can be used for preparing parts such as wear-resistant bearings, self-lubricating parts, mechanical gaskets and the like used under dry friction and other working conditions.
It should be apparent that, in light of the foregoing, various modifications, substitutions and alterations can be made herein without departing from the spirit and scope of the invention as defined by the appended claims.
The above-described aspects of the present invention will be described in further detail below with reference to specific embodiments in the form of examples. It should not be understood that the scope of the above subject matter of the present invention is limited to the following examples only. All techniques implemented based on the above description of the invention are within the scope of the invention.
Drawings
FIG. 1 is a topography of (A) i-PTFE, (B) PSCF and (C) SCF.
FIG. 2. (A) P/i-PTFE, (B) P/i-PTFE/PS20, (C) P/i-PTFE/PS15-S5, (D) P/i-PTFE/PS10-S10, (E) P/i-PTFE/PS5-S15, and (F) brittle profile of the P/i-PTFE/S20 composite.
FIG. 3, (A) flexural properties, (B) tensile strength and surface hardness of each resin-based composite material.
FIG. 4. The (A) instantaneous coefficient of friction, (B) average coefficient of friction and specific wear rate of each resin-based composite.
FIG. 5 shows wear surface topography of (A) P/i-PTFE, (B) P/i-PTFE/P20, (C) P/i-PTFE/PS15-S5, (D) P/i-PTFE/PS10-S10, (E) P/i-PTFE/PS5-S15, and (F) P/i-PTFE/S20 composites.
FIG. 6 shows wear scar 3D topographies of (A) P/i-PTFE, (B) P/i-PTFE/PS20, (C) P/i-PTFE/PS15-S5, (D) P/i-PTFE/PS10-S10, (E) P/i-PTFE/PS5-S15, and (F) P/i-PTFE/S20 composites.
FIG. 7. Instantaneous friction temperature (A) and thermal conductivity (B) for each resin-based composite.
FIG. 8. Coefficient of friction (A) and specific wear (B) for each resin-based composite at high PV conditions. FIG. 9 shows the morphology of the corresponding steel disk surface transfer layer of the (A) P/i-PTFE, (B) P/i-PTFE/P20, (C) P/i-PTFE/PS5-S15, and (D) P/i-PTFE/S20 composites in the pin-disk frictional wear test.
Detailed Description
The raw materials and equipment used in the invention are all known products and are obtained by purchasing commercial products.
Polyphenylene Sulfide (PPS) powder (density 1.35g/cm 3 Melting temperature 285 deg.c) from german Ji Gao new materials, inc. Irradiation modified polytetrafluoroethylene nano powder (i-PTFE) (with the brand of JH-305F and the particle size of 200-300 nm) is purchased from Sichuan gold core polymer material Co. WD-30 type polyacrylonitrile-based short carbon fiber (PSCF, average length 0.3mm, average diameter 6 μm), LSC 070-PEEK-based short carbon fiber (SCF, average length 3mm, average diameter 7 μm), were purchased from Shanghai composite materials science and technology Co., ltd. The microscopic morphologies of i-PTFE, PSCF, and SCF are shown in FIG. 1.
Example 1 preparation of the high-Strength Low-Friction wear-resistant resin-based composite Material of the invention
The resin matrix composite material is prepared by adopting a melt blending method, and the specific operation is as follows: all raw materials were dried at 80.+ -. 5 ℃ for 12.+ -. 0.5h before use. The dried raw materials were premixed in the proportions shown in table 1. Then, melt mixing was performed using a co-rotating parallel twin screw extruder (TSSJ/25/33, chengdu chemical Co., ltd., china). And (3) uniformly plasticizing through an extruder, cooling, granulating, and then placing in a blast drying oven for drying for 12+/-1 h to obtain the modified starch. And carrying out injection molding processing and forming on the obtained composite material by adopting an injection molding machine. The following high-strength low-friction wear-resistant resin matrix composite materials are prepared respectively: P/i-PTFE/PS20, P/i-PTFE/PS15-S5, P/i-PTFE/PS10-S10, P/i-PTFE/PS5-S15 and P/i-PTFE/S20.
TABLE 1 raw material ratios
Note that: in Table 1, 30 parts by weight are used in an amount of 300g.
The following is a method for preparing a control sample.
Comparative example 1 preparation of self-lubricating resin matrix composite Material
A self-lubricating resin matrix composite (P/i-PTFE) was prepared according to the method of example 1 and the raw material ratios shown in Table 1.
The following experiments prove the beneficial effects of the invention.
Experimental example 1, characterization of the microscopic morphology of the broken section of each resin-based composite Material
(1) Experimental method
The brittle fracture surface of each resin matrix composite was observed by SEM scanning electron microscopy (JSM-9600, japan).
(2) Experimental results
FIG. 2 shows the cross-sectional microscopic morphology of each resin-based composite. As shown in FIG. 2 (A), significant voids and i-PTFE particle agglomerates were observed in the P/i-PTFE, indicating that i-PTFE packing would form defects in the composite. In addition, the fracture morphology of P/i-PTFE is very smooth, which indicates that the composite has brittle characteristics. FIG. 2 (B-F) shows the cross-sectional microscopic morphology of the P/i-PTFE/CFs composite. The results show that Carbon Fibers (CFs) are randomly dispersed and intertwined within the PPS matrix to form a "reinforced concrete" type reinforcing structure. In addition, voids or marks due to CFs peeling caused by external force are also observed. However, as the SCF content increases, fewer voids or defects are observed at the fracture surface of the P/i-PTFE/CFs composite. This is because the low aspect ratio PSCF forms a loose network of filler within the composite, which tends to be destroyed by external forces, creating more defects at the fracture surface, especially P/i-PTFE/PS20. In contrast, with increasing SCF content, more interpenetrating network structures are formed, which can resist external forces and contribute to improved mechanical properties. When the addition ratio of PSCF to SCF is 1:3, the composite material has the least defects in the cross section, because a certain content of PSCF can effectively fill gaps among SCFs, thereby reducing fiber-poor areas and enabling the polymer matrix to show a more compact morphology under a carbon fiber interpenetrating network.
Experimental example 2 mechanical characterization of resin-based composite materials
(1) Experimental method
The mechanical properties of each resin-based composite were tested at room temperature using a universal materials tester (Instron 5567, usa). Tensile strength test according to GB/T1040.2-2022 standard, sample size 150X 10X 4mm 3 The test speed was 10mm/min. Bending performance test was performed according to GB/T9341-2008 standard, sample size: 80X 10X 4mm 3 Test speed: 2mm/min.
The surface hardness of each resin matrix composite was tested using a HANDPILX-D Shore durometer (HANDPI Instrument Co., leqing, china).
(2) Experimental results
Fig. 3 shows the mechanical properties of each resin-based composite, including flexural properties, tensile strength, and surface hardness. Fig. 3 (a) shows that with the addition of CFs, both the flexural strength and flexural modulus of the composite material increase significantly. When the PSCF/SCF mass ratio is 1:3, the flexural strength and modulus of the material both reach maximum values. Namely, the flexural strength and modulus of P/i-PTFE/PS5-S15 reached 191.1MPa and 13.7GPa, respectively, 125.6% and 389.3% higher than that of P/i-PTFE. Thus, the different aspect ratio CFs hybridization is beneficial to improve the flexural properties of the composite material. Fig. 3 (B) shows the tensile strength and surface hardness of resin-based composites containing different CFs. Similar to flexural properties, the tensile strength of PPS/i-PTFE/CF composites increases significantly with the addition of CFs, and the tensile strength value continues to increase with increasing SCF content. This is due to the higher aspect ratio CFs having better reinforcement, thereby increasing the tensile strength of the composite. In addition, fig. 3 (B) shows that the surface hardness of the resin-based composite material is improved upon the addition of CFs, which is related to the improvement in surface hardness caused by the formation of entangled CFs network structure. The experimental results show that the mechanical properties and the surface hardness of the P/i-PTFE/CFs composite material are improved simultaneously.
Experimental example 3 characterization of Friction wear Properties of resin-based composite materials
(1) Experimental method
According to GB/T3960-2016, a ring block type friction and wear tester (M-200, beijing crown test laboratory instruments Co., ltd.) is used to test the tribological properties of each resin matrix composite under the working conditions of 0.42M/s sliding speed and 200N load. The sample size was 30X 7X 6mm 3 A 45# steel ring with a surface roughness ra=0.8 μm was used as a friction pair. Before the test, the surface of the steel ring is ground and polished by sand paper, and is placed in acetone for ultrasonic cleaning, and then the steel ring is taken out for natural drying, and each sample is subjected to three parallel experiments. The wear rate of the composite material is measured by a volumetric calculation method, and the test time is 1h.
The calculation formulas of the instantaneous friction coefficient (μ) and the Specific Wear Rate (SWR) are as follows:
wherein P is the friction torque (Nm), F is the applied load (N), r is the radius of the friction pair (mm), v is the wear volume (mm 3 ) D is the sample width (mm), w is the wear scar width (mm) of the sample after the friction test, and L is the sliding distance (m).
The wear surface microscopic morphology and the wear mark morphology of the resin matrix composite after friction test were observed by means of SEM scanning electron microscopy (JSM-9600, japan) and three-dimensional optical profilometer (ContourGT-K, germany), respectively.
(2) Experimental results
Fig. 4 (a) shows the instantaneous coefficient of friction versus slip time for each resin-based composite. The results show that with the addition of CFs, the coefficient of friction at the early stage of friction is unstable due to the broken CFs acting as a hard abrasive in the sliding interface, but the reinforced filler network structure formed by SCF makes it difficult to be peeled off during sliding, which is beneficial to reducing the fluctuation of the friction process. As shown in FIG. 4 (B), by comparing the average friction coefficient and specific wear rate of P/i-PTFE/PS20 and P/i-PTFE/S20, PSCFs are found to be effective in reducing friction coefficient, while SCFs are found to be significantly less effective in specific wear rate, combined with observations of composite wear surfaces and wear marks in FIGS. 5 and 6, due to the formation of lubricating transfer films promoted by the chips resulting from the susceptibility of the former to peeling, while the high resistance to external forces greatly reduces the wear of the materials. The average friction coefficient and specific wear rate of the P/i-PTFE/PS5-S15 composite material were as low as 0.142 and 1.63X10 when the filling ratio of PSCFs and SCFs was 1:3 -6 mm 3 The wear surface of the P/i-PTFE/PS5-S15 composite is very smooth and exhibits the shallowest and narrowest wear marks, as shown in FIGS. 5, 6 and Table 2, which are mainly due to the synergistic complementation between the different aspect ratios CFs inside to form a complete reinforcing networkThe network structure is helpful for improving the mechanical property and the thermal conductivity of the composite material. In addition, the graphite layer formed by the PSCFs with low length-diameter ratio and the low surface energy i-PTFE play a role in cooperative lubrication, so that the tribological performance of the composite material is greatly improved.
TABLE 2 Width of wear scar for each resin-based composite (R d ) Depth (R) v )
| Sample of | R d (μm) | R v (μm) |
| P/i-PTEF | 6927 | 318 |
| P/i-PTFE/PS20 | 4292 | 99 |
| P/i-PTFE/PS15-S5 | 6630 | 412 |
| P/i-PTFE/PS10-S10 | 3677 | 117 |
| P/i-PTFE/PS5-S15 | 2652 | 29 |
| P/i-PTFE/S20 | 2823 | 33 |
Experimental example 4 characterization of Friction Heat and Heat conductivity of resin-based composite Material
(1) Experimental method
The frictional heat was characterized by monitoring the temperature during the friction test in real time using a multi-path thermometer (AT 4204, an accurate instrument limited, everse, china) equipped with a type K thermocouple.
The thermal conductivity of each resin matrix composite was characterized using a HotDisk thermal constant analyzer (2500-OT, sweden).
(2) Experimental results
Fig. 7 (a) shows the change of the sample temperature of each resin-based composite material with time during the rubbing process, and it can be seen that the rubbing temperature of all the samples was significantly increased before 500s, which is related to the accumulation of the rubbing heat during the running-in period. In this case, once the test piece is in contact with the friction pair, frictional heat starts to be generated and accumulated on the sliding interface, resulting in an increase in the instantaneous friction temperature of the test piece. The P/i-PTFE composite has the highest friction temperature, which means that it may suffer from a large friction resistance during friction testing, thereby generating a large amount of friction heat. As can be seen from FIG. 7 (B), the P/i-PTFE has the lowest coefficient of thermal conductivity (0.27W/mK), so that a lot of frictional heat generated during the material testing process cannot be effectively dispersed, and the frictional heat is accumulated in a long time of friction contact surface, so that the polymer is softened to a certain extent and the mechanical strength is reduced, and serious surface abrasion is caused, which corresponds to the higher coefficient of friction and specific abrasion rate. Wherein the friction temperature of the P/i-PTFE/PS5-S15 composite material during friction is the lowest due to the following factors: (1) The P/i-PTFE/PS5-S15 has higher thermal conductivity (0.62W/mK) compared with other test blocks, which is improved by 129.63 percent compared with the P/i-PTFE, thereby being beneficial to dissipating friction heat in the sliding process and avoiding the aggravation of the abrasion degree; (2) Good transfer film formation reduces direct contact between the composite and the friction pair, thereby reducing friction power consumption of the sliding interface.
Experimental example 5 tribological Performance test of resin-based composite Material at high PV
(1) Experimental method
The friction performance of each resin matrix composite material under the working conditions of the sliding speed of 2m/s and the load of 200N (PV is more than or equal to 10MPa m/s) is tested by adopting a self-made pin-disc type friction and wear test device. The abrasion of the material is measured by a weighing method, the testing time is 210s, after each test is finished, the surface of the steel disc is polished again by sand paper, and the steel disc is cleaned by acetone until the temperature of the steel disc is restored to room temperature, and then the steel disc is tested.
The PV value refers to the product of the unit load P on the contact area of the material and the friction device and the relative sliding linear velocity V, thereby approximately measuring the severity of the material friction test conditions.
(2) Experimental results
Fig. 8 (a) and (B) show the friction coefficient and wear rate, respectively, of each resin-based composite material evaluated using a self-made pin-disc type frictional wear test device. The tribological performance test duration at high PV was 210s, divided into five test cycles, each lasting 42s. As shown in fig. 8 (a), the coefficient of friction at high PV for all samples decreased with increasing test period, which was related to the gradual formation of a transfer film on the surface of the steel disk. Similar to the ring block frictional wear test, the coefficient of friction and wear rate of the P/i-PTFE/PS5-S15 composite at high PV were the lowest throughout the study system. Fig. 9 provides an optical image of a polished steel disk after testing, and the transfer film formed by P/i-PTFE/PS5-S15 at the sliding interface is more uniform, which indicates that adding CFs with different aspect ratios has a synergistic improvement effect on the self-lubricating properties of the composite material, and in addition, the improvement of the thermal conductivity and mechanical properties of the composite material can also improve the tribological properties of the material at high PV.
In conclusion, the high-strength low-friction wear-resistant resin matrix composite material has excellent mechanical strength, heat conduction performance and wear resistance, and has wide application prospects in the fields of aerospace, transportation, electronic devices, high-end mechanical equipment and the like.
Claims (9)
1. The high-strength low-friction wear-resistant resin matrix composite is characterized by being prepared from the following raw materials in parts by weight: 10-200 parts of resin matrix, 5-80 parts of solid lubricant and 1-60 parts of carbon fiber; the carbon fiber comprises a carbon fiber A and a carbon fiber B, wherein the average length of the carbon fiber A is 0.1-3mm, the average diameter of the carbon fiber A is 1-20 mu m, the average length of the carbon fiber B is 1-20mm, and the average diameter of the carbon fiber B is 1-20 mu m.
2. The high-strength low-friction wear-resistant resin-based composite material according to claim 1, which is characterized by being prepared from the following raw materials in parts by weight: 20-100 parts of resin matrix, 10-50 parts of solid lubricant and 10-40 parts of carbon fiber; the carbon fiber consists of carbon fiber A and carbon fiber B, wherein the weight ratio of the carbon fiber A to the carbon fiber B is (1-3): 1-3.
3. The high-strength low-friction wear-resistant resin-based composite material according to claim 2, which is characterized by being prepared from the following raw materials in parts by weight: 56 parts of a resin matrix, 24 parts of a solid lubricant and 20 parts of carbon fibers; the carbon fiber consists of carbon fiber A and carbon fiber B, wherein the weight ratio of the carbon fiber A to the carbon fiber B is 1:3.
4. The high-strength low-friction wear-resistant resin-based composite material according to claim 1, wherein the carbon fibers a have an average length of 0.2 to 1mm, an average diameter of 2 to 10 μm, and the carbon fibers B have an average length of 2 to 10mm and an average diameter of 2 to 10 μm.
5. The high strength, low friction, wear resistant resin based composite material according to claim 4, wherein the carbon fibers a have an average length of 0.3mm, an average diameter of 6 μm, and the carbon fibers B have an average length of 3mm and an average diameter of 7 μm.
6. The high strength, low friction, wear resistant resin matrix composite according to any one of claims 1 to 5, wherein the resin matrix is a thermoplastic resin, the solid lubricant is polytetrafluoroethylene or a derivative thereof, and the carbon fibers are polyacrylonitrile-based or pitch-based chopped carbon fibers.
7. The high strength, low friction, wear resistant resin matrix composite of claim 6 wherein said resin matrix is polyphenylene sulfide, said derivative of polytetrafluoroethylene is radiation modified polytetrafluoroethylene, and said carbon fibers are polyacrylonitrile-based chopped carbon fibers.
8. A method of preparing the high strength low friction, wear resistant resin based composite material according to any one of claims 1 to 7, said method comprising the steps of: and drying, premixing, and melt blending the raw materials to obtain the product.
9. Use of the high strength low friction wear resistant resin based composite material according to any one of claims 1-8 in the field of aerospace, transportation, electronics and high end mechanical equipment.
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