An enhanced polyphenylene sulfide composite material and a preparation method thereof

Abstract

The application discloses an enhanced polyphenylene sulfide composite material and a preparation method thereof, relates to the technical field of polymer composite materials, and is characterized by the following steps: taking polyphenylene sulfide, polyether ether ketone, modified alpha-zirconium phosphate, an aromatic interface bridging agent, a high-temperature antioxidant and a silicone processing aid as raw materials, and making the polyphenylene sulfide form a continuous matrix, the polyether ether ketone is dispersed in the matrix in the form of microfibers, and the modified alpha-zirconium phosphate is attached to the surface of the polyether ether ketone microfibers and located in the interface region; during the preparation, the following steps are sequentially performed: alpha-zirconium phosphate silane modification, bridging modification, thermal mixing and coating with polyether ether ketone powder, side-feeding melt extrusion, thermal stretching into fibers and low-temperature fiber preservation molding. The application has the beneficial effects of improving the interface load transmission efficiency, reducing the disordered aggregation of inorganic fillers, maintaining the polyether ether ketone microfiber reinforcing structure, and improving the tensile, bending and impact resistance and the rigid retention ability under the condition of temperature rise.

Description

Technical Field

[0001] This invention relates to the field of polymer composite materials technology, and in particular to a reinforced polyphenylene sulfide composite material and its preparation method. Background Technology

[0002] Heat-resistant thermoplastic composites, due to their excellent heat resistance, chemical resistance, dimensional stability, and melt processability, are widely used in electronics, electrical engineering, mechanical transmission, fluid transportation, and wear- and corrosion-resistant structural components. To further improve the load-bearing capacity and high-temperature stability of these materials, existing technologies typically employ fiber reinforcement, inorganic filler reinforcement, blending modification, and in-situ microfibrillation to enhance their performance. In-situ microfibrillation refers to the deformation and orientation of the dispersed phase along the flow or stretching direction in the matrix during melt processing and stretching, forming a fibrous structure and thus creating a reinforcing phase within the material. Compared to externally added macro-fibers, this technology offers better processing continuity and higher equipment adaptability. However, its actual reinforcing effect depends not only on whether the dispersed phase can form fibers, but also on the interfacial bonding after fiber formation, the morphological stability during thermoforming, and whether the filler or interfacial components can be effectively distributed in the stress transfer region.

[0003] While existing technologies have proposed various methods for reinforcing thermoplastic composites, they still fall short in addressing the continuous synergistic problem of "microfiber formation—interfacial force transfer—high-temperature shape preservation." For example, the published document CN1944512A, "In-situ Microfibrillated Composite Materials with Controllable Microfiber Flexibility and Their Preparation Methods," discloses a method for preparing in-situ microfibrillated composite materials through melt extrusion, hot stretching, and quenching. Its focus is on controlling the flexibility of microfibers and improving processing adaptability. However, this type of approach mainly focuses on adjusting the morphology of the dispersed phase and does not adequately address the issues of interfacial reinforcement between microfibers and the continuous matrix, the directional distribution of interfacial components, and the maintenance of microfiber structure during subsequent thermoforming processes. For example, the published document CN116120600A, "An In-situ Impregnation Molding Method for Fiber-Reinforced Thermoplastic Composites," improves the fiber impregnation effect by adjusting the viscosity of the resin system, making it suitable for molding fiber-reinforced thermoplastic composites. However, its technical focus is on macroscopic fiber wetting and molding process control, and it cannot directly solve problems such as weak interfacial bonding after in-situ fiber formation of the dispersed phase in the melt blend system, easy disordered agglomeration of inorganic reinforcing components, and shrinkage or coarsening of the fiber structure due to thermal history. Therefore, existing reinforcement methods often improve fiber formation, filler dispersion, or resin wetting separately, but lack overall consideration for dispersed phase fiber formation, effective positioning of interfacial control components, and matching of molding temperature windows. This results in difficulties in simultaneously achieving good performance in terms of room temperature strength, impact resistance, and rigidity retention under heating conditions.

[0004] Therefore, the field of heat-resistant thermoplastic composites still needs a composite material and its preparation method that can simultaneously solve the problems of the dispersed phase being difficult to stabilize into fibers, insufficient interfacial load transfer after fiber formation, and the easy destruction of microfiber structure during thermoforming. This method should be able to improve the effective reinforcing effect of the dispersed reinforcing phase in a continuous matrix, reduce the disordered agglomeration of interfacial reinforcing components, enable better stress transfer in the interfacial region, and maintain the microfiberized morphology of the dispersed phase while satisfying the matrix's molding fluidity, thereby improving the material's tensile, flexural, and impact resistance properties, as well as its modulus retention under heating conditions. Summary of the Invention

[0005] To achieve the above-mentioned objectives and address the aforementioned technical problems, this invention provides a reinforced polyphenylene sulfide composite material, prepared from raw materials comprising the following components in parts by mass: 70-85 parts of polyphenylene sulfide, 10-25 parts of polyetheretherketone, 0.5-3 parts of modified α-zirconium phosphate, 0.2-1.5 parts of aromatic interfacial bridge agent, 0.2-0.5 parts of high-temperature antioxidant, and 0.1-0.3 parts of silicone processing aid; The polyphenylene sulfide forms a continuous matrix, and the polyether ether ketone is dispersed in the continuous polyphenylene sulfide matrix in the form of microfibers; The modified zirconium phosphate is at least partially attached to the surface of the polyether ether ketone microfiber and at least partially distributed in the interface region between the polyether ether ketone microfiber and the polyphenylene sulfide continuous matrix; Furthermore, the modified α-zirconium phosphate is an α-type layered zirconium phosphate surface-treated with a silane coupling agent.

[0006] Furthermore, the amount of the silane coupling agent is 2% to 8% of the mass of the α-type layered zirconium phosphate; Preferably, the silane coupling agent is γ-glycidoxypropyltrimethoxysilane.

[0007] Furthermore, the aromatic interface bridging agent is an aromatic compound containing amino or sulfone groups.

[0008] Preferably, the aromatic interfacial bridger is 4,4'-diaminodiphenyl sulfone.

[0009] Furthermore, the modified α-zirconium phosphate has a particle size of 0.2 μm to 2 μm and a sheet thickness of no more than 100 nm; The polyetheretherketone microfibers have an average diameter of 0.5 μm to 5 μm after molding, and an aspect ratio of not less than 15.

[0010] The present invention also provides a method for preparing the above-described reinforced polyphenylene sulfide composite material, comprising the following steps: S1, silane surface modification of α-zirconium phosphate is performed to obtain silane-modified α-zirconium phosphate; S2, the silane-modified α-zirconium phosphate is mixed with an aromatic interfacial bridging agent to obtain bridged modified α-zirconium phosphate; S3, At a temperature below the melting point of polyether ether ketone, the bridging modified α-zirconium phosphate is thermally mixed and coated with polyether ether ketone powder, so that the bridging modified α-zirconium phosphate is at least partially attached to the surface of the polyether ether ketone powder, thereby obtaining bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder. S4, first melt plasticize polyphenylene sulfide, then add the bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder, high temperature antioxidant and silicone processing aid for melt extrusion to obtain extrudate; S5, the extrudate is thermally stretched to form microfibers in polyether ether ketone in polyphenylene sulfide; S6, the hot-stretched material is molded at 305℃~320℃ to obtain the reinforced polyphenylene sulfide composite material.

[0011] Further, step S1 includes: adding the silane coupling agent to a mixed solvent of ethanol and water, adjusting the pH to 4.5-5.5, and pre-hydrolyzing for 30-60 minutes; adding α-zirconium phosphate, stirring at 60-80°C for 1-3 hours, filtering, and drying to obtain the silane-modified α-zirconium phosphate.

[0012] Further, in step S3, the particle size of the polyetheretherketone powder is 20 μm to 100 μm; The temperature of the hot-mix coating is 120℃~180℃, the mixing speed is 500rpm~1500rpm, and the mixing time is 5min~20min.

[0013] Further, in step S4, the polyphenylene sulfide is added through the main feed port of the twin-screw extruder, and the bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder is added through the middle and rear side feed port of the twin-screw extruder; The temperature of the melt plasticizing section of the melt extrusion is 340℃~365℃, the die temperature is 350℃~360℃, and the material residence time after the addition of the bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder is no more than 3 minutes. In step S5, the temperature of the hot stretching is 330℃~342℃, and the stretching ratio is 3~8 times.

[0014] The beneficial effects of the technical solution provided by this invention are as follows: This invention improves the load transfer efficiency of polyetheretherketone (PEEK) / PEEK composite systems by forming a microfiber-like reinforcing phase within a continuous polyphenylene sulfide (PPS) matrix. The PEEK microfibers form an in-situ reinforcing structure within the matrix, which helps to disperse external stress and hinder crack propagation, thereby improving the tensile, flexural, and impact resistance of the composite material.

[0015] This invention employs bridging-modified zirconium phosphate to regulate the interface between polyetheretherketone (PEEK) and polyphenylene sulfide (PPS). Modified zirconium phosphate can be distributed as an interface reinforcing component between PEEK microfibers and the PPS matrix. The aromatic interface bridging agent can improve the interaction between the inorganic layers, PEEK microfibers, and the PPS matrix, addressing the problem of insufficient interfacial bonding and allowing the microfiber reinforcement effect to be more fully realized.

[0016] This invention first thermally mixes and coats bridging-modified α-zirconium phosphate with polyetheretherketone (PEEK) powder, then adds it to the polyphenylene sulfide (PPS) melt via a side-feeding method. This facilitates the preferential entry of the interface-modifying components into the composite system along with the PESK phase, reducing the disordered agglomeration of inorganic fillers in the PESK matrix and improving the effective utilization rate of the interface-reinforcing components. Simultaneously, the mid-to-late-stage side-feeding and shorter residence time help reduce the excessive thermal history impact of the PESK powder and interface-modifying components during the high-temperature melting process.

[0017] This invention uses thermal stretching to microfibrilize the polyether ether ketone (PEEK) dispersed phase and then molds it at a temperature below the melting point of PEEK but not below the melting point of polyphenylene sulfide (PPS). This ensures that the PPS matrix can be melted and molded while preventing the formed PEEK microfibrils from remelting and shrinking, thus helping to maintain a stable microfibril-reinforced structure.

[0018] The modified zirconium phosphate and polyether ether ketone microfibers in this invention can also induce heterogeneous nucleation and interfacial induction in the polyphenylene sulfide matrix, which is beneficial to improving the crystallization behavior of polyphenylene sulfide and enhancing the structural stability of the matrix. Through the synergistic effect of microfiber reinforcement, interfacial bridging, and low-temperature fiber-retaining molding, this invention can simultaneously improve the room-temperature mechanical properties and rigidity retention capacity of the composite material under heated conditions. Attached Figure Description

[0019] Figure 1 This is a cross-sectional SEM image of Embodiment 1 of the present invention.

[0020] Figure 2 This is a cross-sectional SEM image of Comparative Example 4 of the present invention.

[0021] Figure 3 This is a cross-sectional SEM image of Comparative Example 6 of the present invention.

[0022] Figure 4 The graphs show the relationship between energy storage modulus and temperature for embodiments and comparative examples of the present invention. Detailed Implementation

[0023] The purpose of this invention is to provide an enhanced polyphenylene sulfide composite material and its preparation method, in order to solve the technical problems in existing melt blending reinforced systems where the dispersed phase is difficult to stably form and maintain a microfibrillated structure, the interfacial load transfer is insufficient after fiber formation, and the microfibrillated structure is prone to shrinkage or coarsening during thermoforming, resulting in the inability to simultaneously achieve the material's room temperature mechanical properties, impact resistance, and rigidity retention under heating conditions.

[0024] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be further described in detail below with reference to embodiments. Of course, the specific embodiments described herein are merely illustrative and not intended to limit the invention.

[0025] Example 1 This embodiment provides an enhanced polyphenylene sulfide composite material.

[0026] By weight, the raw materials include: 78 parts polyphenylene sulfide, 18 parts polyether ether ketone, 2 parts modified α-zirconium phosphate, 0.8 parts aromatic interfacial bridge agent, 0.3 parts high-temperature antioxidant, and 0.2 parts silicone processing aid.

[0027] The aromatic interfacial bridging agent is 4,4'-diaminodiphenyl sulfone; the silane coupling agent is γ-glycidoxypropyltrimethoxysilane, and the amount of the silane coupling agent is 5% of the mass of α-layered zirconium phosphate; the particle size of the polyether ether ketone powder is 50 μm.

[0028] The high-temperature antioxidant is obtained by compounding antioxidant 1010 and antioxidant 168 in a mass ratio of 1:1.

[0029] The silicone processing aid is ultra-high molecular weight polysiloxane silicone powder.

[0030] Specifically, the steps include the following: S1, Silane-modified α-zirconium phosphate was prepared.

[0031] γ-glycidoxypropyltrimethoxysilane was added to a mixed solvent of ethanol and water in a volume ratio of 90:10, the pH was adjusted to 5.0, and pre-hydrolyzed for 45 min; α-zirconium phosphate was added, and the mixture was stirred at 70 °C for 2 h, filtered, and dried to obtain silane-modified α-zirconium phosphate.

[0032] S2, to prepare bridging modified α-zirconium phosphate.

[0033] The silane-modified zirconium phosphate obtained in step S1 was mixed with 4,4'-diaminodiphenyl sulfone to obtain bridged modified zirconium phosphate.

[0034] S3, bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder was prepared.

[0035] At a temperature below the melting point of polyetheretherketone (PEEK), the bridged modified α-zirconium phosphate obtained in step S2 is thermally mixed and coated with PEEK powder. The thermal mixing and coating temperature is 150°C, the mixing speed is 1000 rpm, and the mixing time is 10 min, so that the bridged modified α-zirconium phosphate is at least partially attached to the surface of the PEEK powder, thus obtaining bridged modified α-zirconium phosphate pre-coated PEEK powder.

[0036] S4, melt extrusion.

[0037] Polyphenylene sulfide is added and melt-plasticized through the main feed port of a twin-screw extruder. Then, the bridged modified α-zirconium phosphate pre-coated polyether ether ketone powder obtained in step S3 is added through the middle and rear side feed port of the twin-screw extruder. At the same time, a high-temperature antioxidant and a silicone processing aid are added for melt extrusion to obtain the extrudate. The temperature of the melt plasticizing section is 355℃, the die temperature is 355℃, and the material residence time after the addition of the bridged modified α-zirconium phosphate pre-coated polyether ether ketone powder is no more than 3 minutes.

[0038] S5, thermally stretched into fibers.

[0039] The extrudate obtained in step S4 is subjected to hot stretching to form microfibers in polyether ether ketone within polyphenylene sulfide; wherein the hot stretching temperature is 340°C and the stretching ratio is 5 times.

[0040] S6, fiber-retaining molding.

[0041] The hot-stretched material was molded at 315℃ to obtain a reinforced polyphenylene sulfide composite material.

[0042] Example 2 The procedure is the same as in Example 1, except that: By weight, the raw materials include: 84 parts polyphenylene sulfide, 12 parts polyether ether ketone, 0.8 parts modified α-zirconium phosphate, 0.3 parts aromatic interfacial bridge agent, 0.2 parts high-temperature antioxidant, and 0.1 parts silicone processing aid.

[0043] The amount of silane coupling agent used is 3% of the mass of α-type layered zirconium phosphate; the particle size of polyetheretherketone powder is 30 μm; the hot mixing and coating temperature is 130℃; the hot stretching temperature is 335℃, the stretching ratio is 4 times; and the molding temperature is 310℃.

[0044] Example 3 The procedure is the same as in Example 1, except that: By weight, the raw materials include: 72 parts polyphenylene sulfide, 24 parts polyether ether ketone, 2.8 parts modified α-zirconium phosphate, 1.2 parts aromatic interfacial bridge agent, 0.5 parts high-temperature antioxidant, and 0.3 parts silicone processing aid.

[0045] The amount of silane coupling agent used is 7% of the mass of α-type layered zirconium phosphate; the particle size of polyetheretherketone powder is 80 μm; the hot mixing and coating temperature is 170℃; the hot stretching temperature is 345℃, the stretching ratio is 7 times; and the molding temperature is 320℃.

[0046] Example 4 The procedure is the same as in Example 1, except that: The amount of silane coupling agent used is 2% of the mass of α-type layered zirconium phosphate; the particle size of polyether ether ketone powder is 20 μm; the hot mixing coating temperature is 120℃; the mixing speed is 500 rpm; and the mixing time is 20 min.

[0047] Example 5 The procedure is the same as in Example 1, except that: The amount of silane coupling agent used is 8% of the mass of α-type layered zirconium phosphate; the particle size of polyetheretherketone powder is 100 μm; the hot mixing and coating temperature is 180℃; the mixing speed is 1500 rpm; and the mixing time is 5 min.

[0048] Example 6 The procedure is the same as in Example 1, except that: The hot stretching temperature is 330℃, and the stretching ratio is 3 times; the molding temperature is 305℃.

[0049] Comparative Example 1 The procedure is the same as in Example 1, except that: Without adding modified α-zirconium phosphate and aromatic interfacial bridgers, polyphenylene sulfide and polyether ether ketone are directly melt-blended and molded.

[0050] Comparative Example 2 The procedure is the same as in Example 1, except that: Without adding aromatic interfacial bridging agents, only silane-modified α-zirconium phosphate and polyether ether ketone powder are thermally mixed and coated.

[0051] Comparative Example 3 The procedure is the same as in Example 1, except that: The bridging modified zirconium phosphate, polyether ether ketone powder, polyphenylene sulfide, high-temperature antioxidant and silicone processing aid are directly mixed and then fed into a twin-screw extruder without the hot mixing and coating treatment in step S3.

[0052] Comparative Example 4 The procedure is the same as in Example 1, except that: Step S5 is omitted, and the extrudate obtained in step S4 is not subjected to thermal stretching, and proceeds directly to step S6 for molding.

[0053] Comparative Example 5 The procedure is the same as in Example 1, except that: Instead of using a mid-to-rear side feeding method, polyphenylene sulfide, bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder, high-temperature antioxidant and silicone processing aid are all added through the main feed port of the twin-screw extruder.

[0054] Comparative Example 6 The procedure is the same as in Example 1, except that: In step S6, the thermally stretched material is molded at 350°C.

[0055] Experimental test: 1. Mechanical property testing Tensile property testing was conducted in accordance with the national standard GB1040-79, with a test temperature of 23±0.5℃ and a tensile speed of 30 mm / min. The notched impact performance test was conducted in accordance with the national standard GB1043-80. The test temperature was 23±0.5℃, the notch size of the specimen was 2±0.5 mm, the cantilever beam impact method was adopted, and the pendulum energy was 11 J.

[0056] The bending performance test was conducted in accordance with GB / T 9341-2008, with a bending speed of 5 mm / min.

[0057] 2. Microscopic morphology test.

[0058] The sample was cooled in liquid nitrogen and then fractured brittlely. The fracture surface was then sputtered with gold, and the morphology of the fracture surface was observed using a scanning electron microscope. 3. Thermal performance test.

[0059] Differential scanning calorimetry was used to test the melting and crystallization behavior of the composite material. 4. Dynamic mechanical performance testing.

[0060] Dynamic mechanical analysis was used to test the modulus retention of the composite material.

[0061] Table 1 Mechanical Performance Test Data

[0062] The mechanical property test results show that each embodiment is superior to the comparative examples in terms of tensile strength, tensile modulus, flexural strength, flexural modulus, and notched impact strength. This indicates that the combined process of bridging modified α-zirconium phosphate pre-coating PEEK powder, side-feed melt extrusion, hot stretching into fibers, and low-temperature fiber-retaining molding can effectively improve the load-bearing capacity and impact resistance of the PPS / PEEK composite system. This is because, after hot stretching, PEEK transforms from a common dispersed phase into a microfiber-like reinforcing phase, forming a similar in-situ reinforcing skeleton within the continuous PPS matrix. The modified α-zirconium phosphate and aromatic interfacial bridging agents further improve the interfacial bonding between the PEEK microfibers and the PPS matrix, allowing external forces to be more effectively transferred from the matrix to the microfiber-reinforcing phase. Conversely, in the comparative examples, removing the modified α-zirconium phosphate and bridging agent, canceling the hot-mix coating, canceling the hot stretching, changing the feeding method, or using molding with a melting point higher than PEEK all resulted in varying degrees of decrease in mechanical properties. This indicates that the reinforcing effect of the present invention is not due to the addition of a single component, but rather to the combined effect of interface regulation, microfiber formation, and microfiber retention.

[0063] Table 2 DSC Thermal Behavior Data Table

[0064] The combined results from DSC, SEM, and DMA show that PPS and PEEK in the composite system of this invention maintain their relatively stable melt thermal behavior, indicating that the composite modification mainly alters the phase distribution, interfacial bonding, and crystallization behavior, rather than destroying the main thermal characteristics of PPS or PEEK. Specifically, the melting peaks of PPS and PEEK provide the thermal behavior basis for the process selection of "forming at a temperature not lower than the melting point of PPS and lower than the melting point of PEEK" in this invention. The changes in the cooling crystallization peak of PPS indicate that the modified α-zirconium phosphate, PEEK microfibers, and their interfacial regions can produce a certain heterogeneous nucleation or interfacial induction effect on PPS crystallization. Further analysis of the SEM images reveals that in the complete process sample, PEEK forms a relatively obvious microfibrillated structure in the continuous PPS matrix, with locally layered or granular modified α-zirconium phosphate distributed near the microfibers and interfaces. In contrast, in the comparative examples formed without hot stretching or above the melting point of PEEK, the PEEK phase is more often in an insufficiently stretched, shrunken, or coarsened state, indicating that hot stretching is key to microfiber formation, and forming below the melting point of PEEK is an important condition for microfiber retention. The DMA curves further corroborate the above morphology and thermal behavior: the complete process system maintains a better energy storage modulus during the heating process, indicating that a more effective interface constraint and load transfer structure is formed between PEEK microfibers, bridged modified α-zirconium phosphate and PPS matrix; in the comparative example, the high-temperature rigidity retention capacity decreases due to insufficient interface bridging, insufficient microfiberization or damage to the microfiber structure at high temperature.

[0065] It can be seen that the technical effect of the present invention comes from the continuous synergistic mechanism of "thermal behavior matching - pre-coating interface control - thermal stretching microfiberization - low temperature fiber retention molding".

[0066] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A reinforced polyphenylene sulfide composite material, characterized in that, It is prepared from raw materials comprising the following components, by weight: 70-85 parts of polyphenylene sulfide, 10-25 parts of polyether ether ketone, 0.5-3 parts of modified α-zirconium phosphate, and 0.2-1.5 parts of aromatic interfacial bridger; The polyphenylene sulfide forms a continuous matrix, and the polyether ether ketone is dispersed in the continuous polyphenylene sulfide matrix in the form of microfibers.

2. The reinforced polyphenylene sulfide composite material according to claim 1, characterized in that, The raw materials also include 0.2 to 0.5 parts of high-temperature antioxidant and 0.1 to 0.3 parts of silicone processing aid.

3. The reinforced polyphenylene sulfide composite material according to claim 1, characterized in that, The modified α-zirconium phosphate is an α-type layered zirconium phosphate surface-treated with a silane coupling agent.

4. The reinforced polyphenylene sulfide composite material according to claim 3, characterized in that, The amount of the silane coupling agent used is 2% to 8% of the mass of the α-type layered zirconium phosphate; The silane coupling agent is γ-glycidoxypropyltrimethoxysilane.

5. The reinforced polyphenylene sulfide composite material according to claim 1, characterized in that, The aromatic interface bridger is an aromatic compound containing both amino and sulfone groups, and the aromatic interface bridger is 4,4'-diaminodiphenyl sulfone.

6. The reinforced polyphenylene sulfide composite material according to claim 1, characterized in that, The polyetheretherketone microfibers have an average diameter of 0.5 μm to 5 μm after molding, and an aspect ratio of not less than 15.

7. A method for preparing a reinforced polyphenylene sulfide composite material, used to prepare the reinforced polyphenylene sulfide composite material according to claim 1, characterized in that, Includes the following steps: S1, silane surface modification of α-zirconium phosphate is performed to obtain silane-modified α-zirconium phosphate; S2, the silane-modified α-zirconium phosphate is mixed with an aromatic interfacial bridging agent to obtain bridged modified α-zirconium phosphate; S3, At a temperature below the melting point of polyetheretherketone, the bridging modified α-zirconium phosphate and polyetheretherketone powder are thermally mixed and coated to obtain bridging modified α-zirconium phosphate pre-coated polyetheretherketone powder. S4, first melt plasticize polyphenylene sulfide, then add the bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder and melt extrude to obtain the extrudate; S5, the extrudate is thermally stretched to form microfibers in polyether ether ketone in polyphenylene sulfide; S6, the hot-stretched material is molded at a temperature lower than the melting point of polyether ether ketone and not lower than the melting point of polyphenylene sulfide to obtain the reinforced polyphenylene sulfide composite material.

8. The preparation method according to claim 7, characterized in that, Step S1 includes: pre-hydrolyzing the silane coupling agent and then adding it to α-zirconium phosphate for surface treatment to obtain the silane-modified α-zirconium phosphate.

9. The preparation method according to claim 7, characterized in that, In step S3, the particle size of the polyetheretherketone powder is 20 μm to 100 μm; The temperature of the hot-mix coating is 120℃~180℃.

10. The preparation method according to claim 7, characterized in that, In step S4, the polyphenylene sulfide is added through the main feed port of the twin-screw extruder, and the bridged modified α-zirconium phosphate pre-coated polyether ether ketone powder is added through the middle and rear side feed port of the twin-screw extruder. The material residence time after the addition of the bridging modified α-zirconium phosphate pre-coated polyether ether ketone powder is no more than 3 minutes.

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