Fatigue-resistant high-elasticity coupling rubber and preparation method thereof

Abstract

The application belongs to the technical field of rubber elastic element material, and particularly relates to a kind of fatigue-resistant high-elasticity coupling rubber and a preparation method thereof.The method takes natural rubber, cis-butadiene rubber and hydrogenated nitrile rubber as the main body, adds composite processing aids, reinforcing carbon black, white carbon black, silane-modified carbon black graphene composite, polydopamine-coated halloysite zinc oxide composite, sulfur-containing silane coupling agent, antioxidant, rubber processing aid, naphthenic oil, tackifying resin, sulfur, accelerator, scorch retarder and anti-reversion agent, and then performs plastication, mixing, storage, thin passage and sheeting to obtain a coupling rubber compound;the compound is co-molded and vulcanized with a coupling framework that has been deoiled, sandblasted or shot blasted and coated with a primer and a surface rubber to obtain the fatigue-resistant high-elasticity coupling rubber.The application can improve the resilience, fatigue resistance, tear resistance of the rubber and the stability of the rubber and the framework.

Description

Technical Field

[0001] This invention belongs to the technical field of rubber elastic element materials, specifically relating to a fatigue-resistant, highly elastic coupling rubber and its preparation method. Background Technology

[0002] Couplings, as crucial connecting components in mechanical transmission systems, are typically used to connect the driving and driven shafts, compensating for installation misalignment, absorbing vibration and shock, and reducing transmission noise while transmitting torque. The rubber elements in flexible couplings directly bear cyclic torsional, compressive, shear, and impact loads, and their performance stability directly affects the smoothness, safety, and service life of the equipment. Existing coupling rubbers are typically based on natural rubber, butadiene rubber, nitrile rubber, or hydrogenated nitrile rubber, with certain strength, elasticity, and aging resistance achieved by adding carbon black, silica, vulcanizing agents, accelerators, antioxidants, softeners, and adhesive systems. However, under heavy loads, high-frequency start-stop, impact vibration, or long-term continuous operation conditions, ordinary coupling rubber is still prone to problems such as rebound decay, increased dynamic heat generation, crack initiation, tear propagation, increased permanent compression set, and failure of the rubber-metal skeleton interface, leading to decreased coupling buffering performance and even transmission instability.

[0003] Existing high-elasticity coupling rubber formulations largely rely on carbon black and silica for reinforcement. Carbon black can improve tensile strength, abrasion resistance, and tear strength, while silica can improve wet slip resistance, heat resistance, and interfacial reinforcement. However, both can easily form localized stress concentration areas in the rubber matrix due to differences in surface polarity, filler aggregation, and uneven dispersion. Especially when couplings are subjected to alternating torsional loads for extended periods, filler agglomeration areas and weak areas at the rubber phase interface can become the initiation sites of fatigue cracks. Although sulfur-containing silane coupling agents can improve the bonding between silica and rubber, their ability to regulate the interface between carbon black and graphite-based carbon materials remains limited. Graphene oxide has a layered structure and high interfacial crack resistance, halloysite nanotubes provide tubular support and crack deflection, and nano-zinc oxide can participate in rubber vulcanization activation and improve crosslinking uniformity. However, when these functional fillers are directly added to rubber, they are prone to agglomeration, insufficient dispersion, or unstable interfacial bonding, making it difficult to fully exert their synergistic reinforcement and fatigue resistance effects.

[0004] Furthermore, coupling rubber not only requires high resilience and fatigue life of the rubber compound itself, but also a stable and reliable bonding interface with the metal skeleton. In traditional rubber-skeleton bonding processes, if the skeleton surface treatment is insufficient, the base and top rubber are improperly matched, or the molding and vulcanization conditions are unstable, interfacial delamination can easily occur under dynamic shear and temperature rise conditions. Simultaneously, natural rubber and butadiene rubber systems may experience changes in their cross-linking network under prolonged hot vulcanization or service temperature increases, leading to decreased elasticity and shortened fatigue life. Therefore, there is an urgent need to provide a method for preparing fatigue-resistant, highly elastic coupling rubber that balances the elasticity of the rubber compound, multi-scale dispersion of fillers, interfacial modification, vulcanization stability, and skeleton bonding reliability. This would address the problems of insufficient fatigue resistance, low filler reinforcement efficiency, rapid crack propagation, and insufficient skeleton bonding stability in existing coupling rubbers during long-term dynamic service. Summary of the Invention

[0005] To address the shortcomings of existing technologies, the present invention aims to provide a fatigue-resistant, highly elastic coupling rubber and its preparation method.

[0006] In a first aspect, the present invention provides a method for preparing fatigue-resistant, highly elastic coupling rubber, comprising the steps of:

[0007] S1. By weight, mix 55.0-70.0 parts of natural rubber, 15.0-30.0 parts of butadiene rubber, and 5.0-15.0 parts of hydrogenated nitrile butadiene rubber, and masticate to obtain a plasticized rubber compound; add 8.0-10.0 parts of composite processing aid, 30.0-60.0 parts of reinforcing carbon black, 10.0-25.0 parts of silica, 3.0-8.0 parts of silane-modified carbon black graphene composite, 2.0-6.0 parts of polydopamine-coated halloysite zinc oxide composite, and 0.6... 1.2 parts of bis-[3-(triethoxysilyl)propyl]disulfide, 2.0-4.0 parts of antioxidant, 0.5-2.0 parts of rubber processing aid, 0-8.0 parts of naphthenic oil and 1.0-3.0 parts of C5 petroleum resin are mixed and discharged to obtain a first-stage compound; the first-stage compound is left to stand, and 1.5-2.5 parts of sulfur, 1.2-2.2 parts of accelerator, 0.1-0.5 parts of scorch inhibitor and 1.0-2.0 parts of anti-reversion agent are added, mixed, thin-passed and sheeted to obtain the coupling rubber compound;

[0008] S2. Degrease, sandblast, or shot blast the surface of the coupling frame to obtain a pretreated coupling frame; spray the primer and top coat onto the surface of the pretreated coupling frame in sequence, and dry to obtain a coupling frame with an adhesive layer; load the coupling rubber material into a mold, and mold and vulcanize it with the coupling frame with the adhesive layer, demold, and place at room temperature.

[0009] In this invention, during the preparation of fatigue-resistant, high-elasticity coupling rubber, natural rubber, butadiene rubber, and hydrogenated nitrile rubber are plasticized to form a continuous rubber phase. Natural rubber provides the elastic recovery and strength foundation, butadiene rubber helps reduce dynamic heat generation and improve flexural properties, and hydrogenated nitrile rubber improves heat resistance, oil resistance, and aging stability. Zinc oxide, magnesium oxide, stearic acid, and zinc stearate in the composite processing aids participate in vulcanization activation and improve compounding processing; reinforcing carbon black and silica constitute the basic reinforcing system, and the silanol groups on the surface of silica can undergo interfacial condensation bonding with the silanol structure formed by the hydrolysis of bis-[3-(triethoxysilyl)propyl]disulfide. The sulfur-containing structure in bis-[3-(triethoxysilyl)propyl]disulfide participates in the formation of the rubber crosslinking network during vulcanization. After the silane-modified carbon black-graphene composite is dispersed in the rubber phase, the carbon black particles enhance the reinforcing effect, the graphene oxide sheets hinder the linear propagation of cracks, and the sulfur-containing silane interface layer strengthens the bond between the filler and the rubber. The polydopamine-coated halloysite-zinc oxide composite buffers stress concentration through the interface coating of halloysite nanotubes, nano-zinc oxide, and polyphenols. Antioxidants improve the rubber compound's resistance to thermo-oxidative aging, rubber processing aids improve filler dispersion and mixing fluidity, naphthenic oil adjusts the rubber compound's flexibility, and C5 petroleum resin improves the rubber compound's adhesion properties. Sulfur, accelerators, scorch inhibitors, and anti-reversion agents synergistically regulate vulcanization speed, scorch safety, crosslinking density, and thermal stability. After the coupling skeleton is degreased, sandblasted, or shot-blasted, the base rubber and top rubber form an adhesive transition layer between the metal surface and the coupling rubber compound. During compression molding and vulcanization, the rubber crosslinking network and the skeleton bonding interface are established simultaneously, thus giving the fatigue-resistant, high-elasticity coupling rubber good resilience, tear resistance, fatigue resistance, and skeleton bonding stability.

[0010] According to a preferred embodiment of the present invention, in step S1, the plasticizing temperature is 80-100℃, and the plasticizing time is 4-6 minutes; the composite processing aid is composed of zinc oxide, magnesium oxide, stearic acid, and zinc stearate; the reinforcing carbon black is composed of carbon black N330 and carbon black N550; the antioxidant is composed of antioxidant 4020 and antioxidant RD; the rubber processing aid is zinc soap SL-5050; the accelerator is composed of accelerator CZ, accelerator DM, and accelerator TMTD; the scorching inhibitor is scorching inhibitor CTP; and the anti-reversion agent is anti-reversion agent WK-901.

[0011] According to a preferred embodiment of the present invention, in step S2, the base adhesive is Chemlok 205; the top adhesive is Chemlok 6125; the molding vulcanization step includes: heating the mold to 140-155°C, holding the mold under pressure at 10-22 MPa for vulcanization; and placing the mold at room temperature for 10-20 hours.

[0012] According to a preferred embodiment of the present invention, the preparation method of the silane-modified carbon black graphene composite includes:

[0013] A1. By weight, mix 45.0-65.0 parts of carbon black N330, 10.0-25.0 parts of carbon black N550, 2.0-6.0 parts of graphene oxide, 0.5-2.0 parts of polyvinylpyrrolidone, 180.0-260.0 parts of anhydrous ethanol and 40.0-80.0 parts of deionized water, disperse by ultrasonication, filter, wash with deionized water, and vacuum dry at 60-75℃ to obtain a pre-dispersed carbon black-graphene mixture.

[0014] A2. Mix 3.0-8.0 parts of bis-[3-(triethoxysilyl)propyl]disulfide, 50.0-80.0 parts of anhydrous ethanol and 15.0-30.0 parts of deionized water, add glacial acetic acid to adjust the pH to 4.5-5.5, and stir and hydrolyze at 30-40℃ to obtain silane hydrolysate; disperse the pre-dispersed carbon black graphene mixture in 120.0-180.0 parts of anhydrous ethanol, sonicate, add silane hydrolysate, stir and react at 55-70℃, filter, wash with anhydrous ethanol, vacuum dry at 65-80℃, grind and sieve.

[0015] In this invention, during the preparation of the silane-modified carbon black graphene composite, carbon black N330, carbon black N550, graphene oxide, polyvinylpyrrolidone, anhydrous ethanol, and deionized water are co-dispersed. Carbon black N330 and carbon black N550 act as particulate reinforcing fillers, forming a reinforcing framework in the mixed system. Graphene oxide, with its sheet-like structure and oxygen-containing polar groups, can be distributed between carbon black N330 and carbon black N550, increasing the contact interface between the fillers and providing reaction sites for subsequent interfacial bonding. Polyvinylpyrrolidone can be adsorbed on the surfaces of carbon black N330, carbon black N550, and graphene oxide, reducing the tendency for particles and sheets to re-agglomerate through steric hindrance, thus maintaining a relatively uniform dispersion state in the pre-dispersed carbon black graphene mixture. Bis-[3-(triethoxysilyl)propyl]disulfide is hydrolyzed in a weakly acidic system consisting of anhydrous ethanol, deionized water, and glacial acetic acid to form a silane hydrolysate containing a silanol structure. After the silane hydrolysate is added to a pre-dispersed carbon black-graphene mixture, it mainly forms an interface bond with the hydroxyl, carboxyl, and epoxy groups on the surface of graphene oxide through the hydrolyzed silanol structure. At the same time, a sulfur-containing silane adsorption layer is formed on the surface of carbon black N330 and carbon black N550. During the subsequent vulcanization process, the sulfur-containing structure of bis-[3-(triethoxysilyl)propyl]disulfide participates in the rubber crosslinking, making the interfacial bonding between carbon black N330, carbon black N550, graphene oxide, and the rubber phase more stable. After washing, vacuum drying, grinding and sieving, carbon black particles, graphene oxide sheets and sulfur-containing silane interface layer together form silane-modified carbon black graphene composite. This composite can improve filler dispersion and reduce local stress concentration in the adhesive, and delay fatigue crack propagation through graphene oxide sheets.

[0016] According to a preferred embodiment of the present invention, in step A1, the ultrasonic dispersion time is 30-50 min; the vacuum drying time at 60-75°C is 6-10 h.

[0017] According to a preferred embodiment of the present invention, in step A2, the ultrasonic dispersion time is 20-40 min; the stirring hydrolysis time at 30-40°C is 30-60 min; the stirring reaction time at 55-70°C is 3-5 h; and the vacuum drying time at 65-80°C is 8-12 h.

[0018] According to a preferred embodiment of the present invention, the method for preparing the polydopamine-coated halloysite zinc oxide composite includes:

[0019] B1. By weight, mix 20.0-40.0 parts halloysite nanotubes, 180.0-260.0 parts deionized water and 40.0-70.0 parts anhydrous ethanol, disperse by ultrasonication, add 5.0-12.0 parts nano zinc oxide and 0.5-2.0 parts polyethylene glycol 400, disperse by ultrasonication, filter, and vacuum dry at 60-75℃ to obtain a halloysite-supported zinc oxide mixture;

[0020] B2. Dissolve 0.8-2.0 parts of tris(hydroxymethyl)aminomethane in 80.0-120.0 parts of deionized water, and adjust the pH to 8.3-8.7 with hydrochloric acid to obtain a buffer solution; add the halloysite-supported zinc oxide mixture to 180.0-260.0 parts of deionized water, disperse by sonication, add the buffer solution, 3.0-7.0 parts of dopamine hydrochloride and 0.3-1.5 parts of tannic acid, stir and react in the dark at 25-35℃, centrifuge, wash with deionized water and anhydrous ethanol in sequence, vacuum dry at 55-70℃, grind and sieve.

[0021] In this invention, during the preparation of the polydopamine-coated halloysite-zinc oxide composite, halloysite nanotubes are first dispersed in a mixed medium composed of deionized water and anhydrous ethanol. Halloysite nanotubes have a tubular structure, with an outer surface dominated by silicon-oxygen structures and an inner surface containing aluminum hydroxyl groups, which can provide adsorption contact sites for nano-zinc oxide. After adding nano-zinc oxide and polyethylene glycol 400, the ether oxygen chains and terminal hydroxyl groups of polyethylene glycol 400 can wet, disperse, and bridge the halloysite nanotubes and nano-zinc oxide, allowing the nano-zinc oxide to distribute on and around the surface of the halloysite nanotubes under ultrasonic dispersion conditions, reducing the self-aggregation tendency of the nano-zinc oxide. This stage mainly involves physical co-dispersion, hydrogen bond adsorption, and drying fixation, resulting in a relatively stable halloysite-supported zinc oxide mixture of halloysite nanotubes and nano-zinc oxide. When halloysite-loaded zinc oxide mixtures are introduced into a weakly alkaline buffer solution formed by tris(hydroxymethyl)aminomethane and hydrochloric acid, dopamine hydrochloride undergoes oxidative self-polymerization, gradually forming a polydopamine deposition layer containing catechol and amino groups on the surface of halloysite nanotubes and nano-zinc oxide. Tannic acid, containing polyphenolic hydroxyl groups, can co-deposit with the oxidative polymerization product of dopamine hydrochloride and is fixed on the surface of halloysite nanotubes and nano-zinc oxide through hydrogen bonding, coordination, and adsorption. After light-protected stirring reaction, centrifugation, washing, vacuum drying, grinding, and sieving, halloysite nanotubes, nano-zinc oxide, the dopamine hydrochloride polymer deposition layer, and tannic acid together form a polydopamine-coated halloysite-zinc oxide composite, which in turn provides tubular framework support, zinc oxide vulcanization activation, interfacial buffering, and crack deflection in the rubber system.

[0022] According to a preferred embodiment of the present invention, in step B1, the vacuum drying time at 60-75°C is 6-10 hours.

[0023] According to a preferred embodiment of the present invention, in step B2, the ultrasonic dispersion time is 20-40 min; the stirring reaction time at 25-35°C in the dark is 6-10 h; and the vacuum drying time at 55-70°C is 10-16 h.

[0024] A second aspect of the present invention provides a fatigue-resistant, high-elasticity coupling rubber prepared according to the aforementioned method for preparing fatigue-resistant, high-elasticity coupling rubber.

[0025] Compared with the prior art, the present invention has the following beneficial effects:

[0026] (1) This invention uses natural rubber, butadiene rubber, and hydrogenated nitrile rubber as the main rubber compounds, which can take into account elastic recovery, flexural cushioning, heat resistance, and aging resistance. The composite processing aids, in combination with sulfur, accelerators, scorching inhibitors, and anti-reversion agents, can improve the vulcanization activation efficiency, enabling the rubber compound to form a more stable cross-linked structure and reducing performance degradation under long-term heating and repeated deformation conditions. Naphthenic oil improves the flexibility and flowability of the rubber compound, and C5 petroleum resin improves the adhesion and molding stability of the rubber compound, giving the coupling rubber compound a better mold filling effect and bonding foundation during compression molding and vulcanization.

[0027] (2) This invention introduces a silane-modified carbon black graphene composite and a polydopamine-coated halloysite zinc oxide composite into the rubber compound system, and combines them with reinforcing carbon black, silica, and bis-[3-(triethoxysilane)propyl] disulfide. Carbon black N330 and carbon black N550 in the silane-modified carbon black graphene composite provide reinforcing support, graphene oxide can hinder direct crack propagation, and bis-[3-(triethoxysilane)propyl] disulfide improves the interfacial bonding between the filler and the rubber phase. Halloysite nanotubes in the polydopamine-coated halloysite zinc oxide composite have a tubular supporting effect, nano-zinc oxide participates in vulcanization activation, and the coating layer formed by dopamine hydrochloride and tannic acid can buffer stress concentration, thereby improving the tear resistance and fatigue resistance of the rubber compound.

[0028] (3) In this invention, the coupling skeleton is degreased, sandblasted, or shot-blasted, and a primer and a top coat are sequentially sprayed onto the surface of the pretreated coupling skeleton to form a stable bonding interface between the coupling skeleton and the coupling rubber compound. During the compression molding and vulcanization process, the coupling rubber compound completes cross-linking, and the coupling skeleton with the adhesive layer is simultaneously bonded and molded with the rubber compound, which can reduce interfacial peeling under alternating torsion, compression, and shear conditions. The fatigue-resistant, high-elasticity coupling rubber obtained in this way has good resilience, tear resistance, fatigue resistance, low heat generation, and skeleton bonding stability, and is suitable for coupling elastic elements that are subjected to long-term impact, vibration, and torsional loads. Detailed Implementation

[0029] To facilitate understanding of the present invention, the following embodiments are provided. Those skilled in the art should understand that these embodiments are merely illustrative and should not be construed as limiting the scope of the invention.

[0030] Example 1

[0031] This embodiment provides a method for preparing fatigue-resistant, highly elastic coupling rubber, the steps of which include:

[0032] Step S1: Add 62.5g of natural rubber, 22.5g of butadiene rubber, and 10.0g of hydrogenated nitrile rubber to a mixer. Set the rotor speed of the mixer to 55r / min and plasticize at 90℃ for 5min to obtain a plasticized rubber compound. Add 9.0g of composite processing aid, 45.0g of reinforcing carbon black, 17.5g of silica, 5.5g of silane-modified carbon black graphene composite, and 4.0g of polydopamine to the plasticized rubber compound. A compound containing halloysite-coated zinc oxide, 0.9 g of bis-[3-(triethoxysilane)propyl]disulfide, 3.0 g of antioxidant, 1.25 g of rubber processing aid, 4.0 g of naphthenic oil, and 2.0 g of C5 petroleum resin was mixed at 60 r / min for 9 min, with the discharge temperature controlled at 115℃. After discharge, a first-stage compound was obtained. The 9.0 g of composite processing aid consisted of 3.5 g zinc oxide, 1.5 g magnesium oxide, and 2.5 g hardener. The compound consists of fatty acid and 1.5g zinc stearate; 45.0g reinforcing carbon black is composed of 30.0g carbon black N330 and 15.0g carbon black N550; 3.0g antioxidant is composed of 1.8g antioxidant 4020 and 1.2g antioxidant RD; and the rubber processing aid is zinc soap SL-5050. A section of the compound was left to stand at 25℃ for 12 hours, then added to a two-roll mill. The two-roll mill temperature was controlled at 55℃. 2.0g sulfur and 1... 0.7g accelerator, 0.3g anti-scorching agent, and 1.5g anti-reversion agent were mixed for 6 minutes, passed through a thin pass 4 times, with the roller gap controlled at 1.0mm and the sheet thickness controlled at 3.0mm to obtain the coupling rubber compound; wherein, the 1.7g accelerator consists of 1.0g accelerator CZ, 0.5g accelerator DM, and 0.2g accelerator TMTD, the anti-scorching agent is anti-scorching agent CTP, and the anti-reversion agent is anti-reversion agent WK-901;

[0033] Step S2: After degreasing the surface of the coupling frame, perform sandblasting. After sandblasting, blow away the surface dust to obtain a pre-treated coupling frame. Apply Chemlok 205 as a primer evenly to the surface of the pre-treated coupling frame at a coating amount of 80 g / m². 2 After surface drying at 25℃ for 30 minutes, Chemlok 6125 is evenly sprayed as a topcoat at a rate of 120 g / m². 2After surface drying at 25℃ for 30 minutes, the material is dried at 80℃ for 20 minutes to obtain a coupling skeleton with an adhesive layer. The coupling rubber material is cut into blanks that match the mold cavity and placed into the mold. The blanks are then molded and vulcanized with the coupling skeleton with the adhesive layer. The mold is heated to 147.5℃ and vulcanized under pressure at 16MPa for 85 minutes. After vulcanization, the material is demolded and placed at 25℃ for 15 hours to obtain fatigue-resistant and highly elastic coupling rubber.

[0034] Preparation steps of silane-modified carbon black graphene composite:

[0035] Step A1: Add 55.0g carbon black N330, 17.5g carbon black N550, 4.0g graphene oxide, 1.25g polyvinylpyrrolidone, 220.0g anhydrous ethanol and 60.0g deionized water to a glass dispersion container. Stir at 300r / min for 15min using a mechanical stirrer to fully wet carbon black N330, carbon black N550, graphene oxide and polyvinylpyrrolidone. Then, use an ultrasonic dispersion device to ultrasonically disperse at 400W and 40kHz for 40min. During the ultrasonic process, control the system temperature not to exceed 35℃. After ultrasonication, filter through a 0.45μm filter membrane. Wash the filter cake three times with deionized water, each time using 100.0g of deionized water, until there is no obvious black suspended matter in the washing liquid. Place the filter cake in a vacuum drying oven and vacuum dry at 67.5℃ and -0.08MPa for 8h to obtain a pre-dispersed carbon black and graphene mixture.

[0036] Step A2: Add 5.5g of bis-[3-(triethoxysilyl)propyl]disulfide, 65.0g of anhydrous ethanol, and 22.5g of deionized water to a glass reaction vessel. Stir and mix at 300 rpm for 10 min. Adjust the pH to 5.0 by adding glacial acetic acid dropwise. Hydrolyze the mixture at 300 rpm for 45 min under a 35°C water bath to obtain a silane hydrolysate. Add the pre-dispersed carbon black and graphene mixture obtained in Step A1 to 150.0g of anhydrous ethanol. The mixture was ultrasonically dispersed at 400W and 40kHz for 30 min, and then silane hydrolysate was added. The mixture was stirred at 300r / min at 62.5℃ for 4 h. After the reaction, the mixture was filtered through a 0.45μm filter membrane. The filter cake was washed three times with anhydrous ethanol, each time using 80.0g of anhydrous ethanol, until the washing liquid was clear. The filter cake was then vacuum dried at 72.5℃ and -0.08MPa for 10 h. After drying, the mixture was ground and passed through a 200-mesh sieve to obtain the silane-modified carbon black graphene composite.

[0037] Preparation steps of polydopamine-coated halloysite zinc oxide composite:

[0038] Step B1: Add 30.0g halloysite nanotubes, 220.0g deionized water and 55.0g anhydrous ethanol to a glass dispersion container, stir at 300r / min for 15min to fully wet the halloysite nanotubes, then sonicate at 400W and 40kHz for 40min. Add 8.5g nano zinc oxide and 1.25g polyethylene glycol 400, stir at 300r / min for 10min, and continue to sonicate at 400W and 40kHz for 40min. During sonication, control the system temperature not to exceed 35℃. After sonication, filter with a 0.45μm filter membrane, and vacuum dry the filter cake at 67.5℃ and -0.08MPa for 8h to obtain a halloysite-supported zinc oxide mixture.

[0039] Step B2: Dissolve 1.4 g of tris(hydroxymethyl)aminomethane in 100.0 g of deionized water, stir at 300 rpm until completely dissolved, add hydrochloric acid to adjust the pH to 8.5 to obtain a buffer solution; add the halloysite-supported zinc oxide mixture obtained in Step B1 to 220.0 g of deionized water, sonicate at 400 W and 40 kHz for 30 min, add the buffer solution, 5.0 g of dopamine hydrochloride and 0.9 g of tannic acid, and incubate at 30°C in the dark. The reaction was stirred at 5000 r / min for 8 h. After the reaction was completed, the mixture was centrifuged at 5000 r / min for 10 min. The precipitate was washed three times with 100.0 g of deionized water each time, and then washed twice with 80.0 g of anhydrous ethanol each time, until the washing solution was nearly colorless. The precipitate was vacuum dried at 62.5℃ and -0.08 MPa for 13 h. After drying, the precipitate was ground and passed through a 200-mesh sieve to obtain polydopamine-coated halloysite zinc oxide composite.

[0040] Example 2

[0041] The difference between this embodiment and Embodiment 1 is that this embodiment provides a method for preparing fatigue-resistant, highly elastic coupling rubber, the steps of which include:

[0042] Step S1: Add 55.0g of natural rubber, 15.0g of butadiene rubber, and 5.0g of hydrogenated nitrile rubber to a mixer and plasticize at 80℃ for 4 minutes to obtain a plasticized rubber compound. Add 8.0g of composite processing aid, 30.0g of reinforcing carbon black, 10.0g of silica, 3.0g of silane-modified carbon black graphene composite, 2.0g of polydopamine-coated halloysite zinc oxide composite, 0.6g of bis-[3-(triethoxysilyl)propyl] disulfide, 2.0g of antioxidant, 0.5g of rubber processing aid, 0g of naphthenic oil, and 1.0g of C5 petroleum resin to the plasticized rubber compound. Mix until the filler is evenly dispersed and then discharge the compound to obtain a first-stage compound. The 8.0g of composite processing aid consists of 3.0g of zinc oxide, 1.0g of magnesium oxide, and... The compound consists of 2.0g stearic acid and 2.0g zinc stearate; 30.0g reinforcing carbon black is composed of 20.0g carbon black N330 and 10.0g carbon black N550; 2.0g antioxidant is composed of 1.2g antioxidant 4020 and 0.8g antioxidant RD; and the rubber processing aid is zinc soap SL-5050. A section of the compound was left to stand for 8 hours, then 1.5g sulfur, 1.2g accelerator, 0.1g anti-scorching agent, and 1.0g anti-reversion agent were added. The mixture was then mixed for 4 minutes, thin-passed, and sheeted to obtain the coupling rubber compound. The 1.2g accelerator is composed of 0.7g accelerator CZ, 0.4g accelerator DM, and 0.1g accelerator TMTD; the anti-scorching agent is anti-scorching agent CTP; and the anti-reversion agent is anti-reversion agent WK-901.

[0043] Step S2: Degrease and sandblast the surface of the coupling frame to obtain a pretreated coupling frame; first spray Chemlok 205 as a base coat on the surface of the pretreated coupling frame, and after the base coat is dry, spray Chemlok 6125 as a top coat, and dry to obtain a coupling frame with an adhesive layer; put the coupling rubber material into a mold, and mold it with the coupling frame with the adhesive layer for vulcanization; heat the mold to 140℃, hold it under pressure at 10MPa for vulcanization, demold, and place it at room temperature for 10h to obtain fatigue-resistant and highly elastic coupling rubber.

[0044] Preparation steps of silane-modified carbon black graphene composite:

[0045] Step A1: Add 45.0g carbon black N330, 10.0g carbon black N550, 2.0g graphene oxide, 0.5g polyvinylpyrrolidone, 180.0g anhydrous ethanol and 40.0g deionized water to a dispersion container, stir to initially wet the materials, and then ultrasonically disperse for 30min. After ultrasonic dispersion, filter the mixture, wash the filter cake with deionized water until the washing liquid is clear, place the filter cake in a vacuum drying oven, and vacuum dry at 60℃ for 6h to obtain a pre-dispersed carbon black graphene mixture.

[0046] Step A2: Add 3.0g of bis-[3-(triethoxysilyl)propyl]disulfide, 50.0g of anhydrous ethanol and 15.0g of deionized water to a reaction vessel, stir and mix, add glacial acetic acid to adjust the pH to 4.5, stir and hydrolyze at 30℃ for 30min to obtain silane hydrolysate; add the pre-dispersed carbon black graphene mixture to 120.0g of anhydrous ethanol, ultrasonically disperse for 20min, add silane hydrolysate, stir and react at 55℃ for 3h, filter after the reaction, wash the filter cake with anhydrous ethanol until the washing liquid is clear, vacuum dry the filter cake at 65℃ for 8h, grind and sieve to obtain silane modified carbon black graphene composite.

[0047] Preparation steps of polydopamine-coated halloysite zinc oxide composite:

[0048] Step B1: Add 20.0g halloysite nanotubes, 180.0g deionized water and 40.0g anhydrous ethanol to a dispersion container, stir to wet the halloysite nanotubes and then sonicate for 30min. Add 5.0g nano zinc oxide and 0.5g polyethylene glycol 400, continue to sonicate for 30min, filter, and vacuum dry the filter cake at 60℃ for 6h to obtain halloysite-supported zinc oxide mixture.

[0049] Step B2: Dissolve 0.8g of tris(hydroxymethyl)aminomethane in 80.0g of deionized water, add hydrochloric acid to adjust the pH to 8.3 to obtain a buffer solution; add halloysite-loaded zinc oxide mixture to 180.0g of deionized water, sonicate for 20min, add buffer solution, 3.0g of dopamine hydrochloride and 0.3g of tannic acid, stir and react at 25℃ in the dark for 6h, after the reaction is completed, centrifuge and separate, wash the precipitate with deionized water and anhydrous ethanol successively until the washing solution is nearly colorless, vacuum dry at 55℃ for 10h, grind and sieve to obtain polydopamine-coated halloysite-zinc oxide composite.

[0050] Example 3

[0051] The difference between this embodiment and Embodiment 1 is that this embodiment provides a method for preparing fatigue-resistant, highly elastic coupling rubber, the steps of which include:

[0052] Step S1: Add 70.0g of natural rubber, 30.0g of butadiene rubber, and 15.0g of hydrogenated nitrile rubber to a mixer and plasticize at 100℃ for 6 minutes to obtain a plasticized rubber compound. Add 10.0g of composite processing aid, 60.0g of reinforcing carbon black, 25.0g of silica, 8.0g of silane-modified carbon black graphene composite, 6.0g of polydopamine-coated halloysite zinc oxide composite, 1.2g of bis-[3-(triethoxysilane)propyl] disulfide, 4.0g of antioxidant, 2.0g of rubber processing aid, 8.0g of naphthenic oil, and 3.0g of C5 petroleum resin to the plasticized rubber compound. Mix until the filler is evenly dispersed and then discharge the compound to obtain a first-stage compound. The 10.0g of composite processing aid consists of 4.0g of zinc oxide, 2.0g of... The compound consists of magnesium, 2.0g stearic acid, and 2.0g zinc stearate; 60.0g reinforcing carbon black is composed of 40.0g carbon black N330 and 20.0g carbon black N550; 4.0g antioxidant is composed of 2.4g antioxidant 4020 and 1.6g antioxidant RD; and the rubber processing aid is zinc soap SL-5050. A section of the compound was left to stand for 16 hours, then 2.5g sulfur, 2.2g accelerator, 0.5g scorch inhibitor, and 2.0g anti-reversion agent were added. The compound was mixed for 8 minutes, thin-passed, and sheeted to obtain the coupling rubber compound. The 2.2g accelerator is composed of 1.2g accelerator CZ, 0.7g accelerator DM, and 0.3g accelerator TMTD; the scorch inhibitor is anti-scorch agent CTP; and the anti-reversion agent is anti-reversion agent WK-901.

[0053] Step S2: Degrease and shot blast the surface of the coupling frame to obtain a pretreated coupling frame; spray Chemlok 205 as a base coat on the surface of the pretreated coupling frame, and after the base coat is dry, spray Chemlok 6125 as a top coat and dry to obtain a coupling frame with an adhesive layer; load the coupling rubber material into a mold and mold it with the coupling frame with the adhesive layer for vulcanization; heat the mold to 155℃ and vulcanize it under pressure at 22MPa; demold and place it at room temperature for 20h to obtain fatigue-resistant, high-elasticity coupling rubber.

[0054] Preparation steps of silane-modified carbon black graphene composite:

[0055] Step A1: Add 65.0g carbon black N330, 25.0g carbon black N550, 6.0g graphene oxide, 2.0g polyvinylpyrrolidone, 260.0g anhydrous ethanol and 80.0g deionized water to a dispersion container, stir to initially wet the materials, and then ultrasonically disperse for 50min. After ultrasonic dispersion, filter, wash the filter cake with deionized water until the washing liquid is clear, place the filter cake in a vacuum drying oven, and vacuum dry at 75℃ for 10h to obtain a pre-dispersed carbon black graphene mixture.

[0056] Step A2: Add 8.0g of bis-[3-(triethoxysilyl)propyl]disulfide, 80.0g of anhydrous ethanol and 30.0g of deionized water to a reaction vessel, stir and mix, add glacial acetic acid to adjust the pH to 5.5, and stir and hydrolyze at 40℃ for 60min to obtain silane hydrolysate; add the pre-dispersed carbon black graphene mixture to 180.0g of anhydrous ethanol, sonicate for 40min, add silane hydrolysate, stir and react at 70℃ for 5h, filter after the reaction, wash the filter cake with anhydrous ethanol until the washing liquid is clear, vacuum dry the filter cake at 80℃ for 12h, grind and sieve to obtain silane modified carbon black graphene composite.

[0057] Preparation steps of polydopamine-coated halloysite zinc oxide composite:

[0058] Step B1: Add 40.0g halloysite nanotubes, 260.0g deionized water and 70.0g anhydrous ethanol to a dispersion container, stir to wet the halloysite nanotubes and then ultrasonically disperse for 50min. Add 12.0g nano zinc oxide and 2.0g polyethylene glycol 400, continue ultrasonic dispersion for 50min, filter, and vacuum dry the filter cake at 75℃ for 10h to obtain halloysite-supported zinc oxide mixture.

[0059] Step B2: Dissolve 2.0 g of tris(hydroxymethyl)aminomethane in 120.0 g of deionized water, add hydrochloric acid to adjust the pH to 8.7 to obtain a buffer solution; add halloysite-loaded zinc oxide mixture to 260.0 g of deionized water, sonicate for 40 min, add buffer solution, 7.0 g of dopamine hydrochloride and 1.5 g of tannic acid, stir and react at 35 °C in the dark for 10 h, centrifuge after reaction, wash the precipitate with deionized water and anhydrous ethanol until the washing solution is nearly colorless, vacuum dry at 70 °C for 16 h, grind and sieve to obtain polydopamine-coated halloysite-zinc oxide composite.

[0060] Comparative Example 1

[0061] The difference between this comparative example and Example 1 is that 5.5g of silane-modified carbon black graphene composite is not added. Instead, 5.5g of silane-modified carbon black graphene composite is replaced with a non-silane-modified carbon black graphene mixture obtained by directly mixing 4.1g of carbon black N330, 1.1g of carbon black N550 and 0.3g of graphene oxide. The rest is the same as in Example 1.

[0062] Comparative Example 2

[0063] The difference between this comparative example and Example 1 is that 4.0g of polydopamine-coated halloysite zinc oxide composite is not added. Instead, 4.0g of polydopamine-coated halloysite zinc oxide composite is replaced with an uncoated halloysite zinc oxide mixture obtained by directly mixing 3.1g of halloysite nanotubes and 0.9g of nano zinc oxide. The rest is the same as in Example 1.

[0064] Comparative Example 3

[0065] The difference between this comparative example and Example 1 is that 0.9g of bis-[3-(triethoxysilane)propyl] disulfide is not added during the preparation of the fatigue-resistant high-elasticity coupling rubber; otherwise, it is the same as Example 1.

[0066] The properties of the fatigue-resistant, highly elastic coupling rubbers obtained in Examples 1-3 and Comparative Examples 1-3 were tested.

[0067] The fatigue-resistant, high-elasticity coupling rubbers prepared in Examples 1-3 and Comparative Examples 1-3 were placed in an environment of 23°C and 50% relative humidity for 24 hours before being tested, and samples were cut from the same batch of molded vulcanized rubber sheets or coupling rubber parts.

[0068] During the tensile strength test, the film was cut into dumbbell-shaped specimens with a thickness of 2.0 mm. The specimen surface was free of cracks, bubbles, and obvious impurities. A universal testing machine was used for the test, with an initial clamping distance of 25 mm and a tensile speed of 500 mm / min. Five specimens were tested in each group. The maximum tensile force that the specimen could withstand before fracture was recorded. The tensile strength was calculated by dividing the maximum tensile force by the effective cross-sectional area of ​​the specimen, in MPa, and the average value of the five specimens was taken.

[0069] During the tear strength test, the film was cut into right-angle tear specimens with a thickness of 2.0 mm. The cut was checked to ensure that the cut was smooth and there was no pre-crack propagation at the notch of the specimen. A universal testing machine was used to stretch and tear the specimen at a speed of 500 mm / min. Five specimens were tested in each group. The maximum tear force during the tearing process was recorded. The tear strength was calculated by dividing the maximum tear force by the specimen thickness, with the unit being kN / m. The average value of the five specimens was taken.

[0070] During the rebound rate test, the rubber compound was made into a cylindrical sample with a thickness of 12.0 mm and flat upper and lower surfaces. After being placed at 23°C for 2 hours, the impact rebound test was carried out. Each sample was impacted 5 times consecutively. The first result was discarded, and the average of the last 4 results was taken as the rebound rate of the sample. 5 samples were tested in each group, and the final result was the average value, in units of .

[0071] During the compression set test, the cylindrical specimen was placed in the compression fixture after measuring its initial height and compressed to 75% of its initial height. It was then kept at 100℃ for 24 hours. After being removed, the compression was released and the specimen was allowed to recover at 23℃ for 30 minutes. The height after recovery was measured, and the compression set was calculated based on the change in height before and after compression. Five specimens were tested in each group, and the average value was taken. The unit is .

[0072] During the flexural fatigue life test, the film was cut into flexural specimens with pre-made notches. The pre-made notches were located in the center of the bending area of ​​the specimen. The specimens were repeatedly flexed at 23°C with a flexural frequency of 5Hz. The crack length was observed every fixed number of cycles. The number of cycles when the crack expanded from the pre-made notch to 10mm was recorded. Three specimens were tested in each group, and the average value was taken. The unit is 10,000 cycles.

[0073] For the rubber-skeleton bond strength test, the coupling skeleton and the coupling rubber compound are molded and vulcanized together to form a peel test specimen. The peel width is controlled at 25 mm. Before the test, check whether the bonding interface is intact. Fix the specimen in the fixture of the universal testing machine and peel it at a speed of 50 mm / min. Record the average peel force in the stable peel stage. Calculate the rubber-skeleton bond strength by dividing the average peel force by the peel width. Test 5 specimens in each group and take the average value. The unit is kN / m.

[0074] The performance test data above are shown in Table 1.

[0075] Table 1: Performance Test Results

[0076]

[0077] The test results in Table 1 clearly show that Examples 1-3 exhibit better results than Comparative Examples 1-3 in terms of tensile strength, tear strength, resilience, compression set, flexural fatigue life, and rubber-skeleton bond strength. This indicates that the present invention can effectively solve the problems of insufficient reinforcement, rapid crack propagation, decreased elastic recovery, increased permanent deformation, and unstable skeleton bonding in existing coupling rubber under long-term alternating torsion, compression shear, and impact loads.

[0078] First, regarding mechanical strength, the tensile strengths of Examples 1-3 were 24.8 MPa, 22.6 MPa, and 23.9 MPa, respectively, significantly higher than those of Comparative Example 1 (19.7 MPa), Comparative Example 2 (20.5 MPa), and Comparative Example 3 (21.1 MPa). The tear strengths of Examples 1-3 were 78.5 kN / m, 72.8 kN / m, and 76.2 kN / m, respectively, also higher than those of Comparative Example 1 (61.4 kN / m), Comparative Example 2 (64.7 kN / m), and Comparative Example 3 (66.3 kN / m). This indicates that the silane-modified carbon black graphene composite, the polydopamine-coated halloysite zinc oxide composite, and bis-[3-(triethoxysilyl)propyl]disulfide synergistically improved filler dispersibility and interfacial bonding stability, reduced stress concentration caused by filler agglomeration and interfacial defects, thereby enhancing the load-bearing capacity and tear resistance of the compound.

[0079] Secondly, in terms of elastic recovery and deformation resistance, the rebound rates of Examples 1-3 were 58.6%, 60.2%, and 56.7%, respectively, which were higher than those of Comparative Example 1 (52.1%), Comparative Example 2 (53.4%), and Comparative Example 3 (54.8%). The compression set of Examples 1-3 were 13.6%, 14.8%, and 14.2%, respectively, which were lower than those of Comparative Example 1 (18.9%), Comparative Example 2 (18.1%), and Comparative Example 3 (17.2%). This indicates that the reinforcing network and vulcanization crosslinking structure formed by the present invention are more stable, and the rubber compound has better dimensional recovery ability after compression deformation, which can alleviate the problem of elastic decay and excessive permanent deformation of existing coupling rubber under long-term compression and shear.

[0080] Furthermore, regarding fatigue resistance, the flexural fatigue lives of Examples 1-3 were 1.68 million, 1.46 million, and 1.57 million, respectively, which were significantly higher than those of Comparative Example 1 (920,000), Comparative Example 2 (1.04 million), and Comparative Example 3 (1.18 million). Among them, Comparative Example 1 showed the most significant decrease in fatigue life after lacking the silane-modified carbon black graphene composite, indicating that the graphene oxide sheets and silane interface layer have a significant inhibitory effect on fatigue crack propagation.

[0081] Comparative Example 2 also showed a decrease in fatigue life after the absence of polydopamine-coated halloysite-zinc oxide composite, indicating that halloysite nanotubes, nano-zinc oxide and the coating interface can buffer stress concentration and improve crack propagation behavior under dynamic load.

[0082] The fatigue life of Comparative Example 3 was also reduced due to the lack of bis-[3-(triethoxysilyl)propyl]disulfide, indicating that sulfur-containing silanes play an important role in the interfacial bonding between the filler and the rubber phase and the stability of the vulcanization network.

[0083] Finally, regarding the rubber-skeleton bonding, the rubber-skeleton bonding strengths of Examples 1-3 were 9.8 kN / m, 9.1 kN / m, and 9.5 kN / m, respectively, which were higher than those of Comparative Example 1 (8.2 kN / m), Comparative Example 2 (8.4 kN / m), and Comparative Example 3 (7.1 kN / m). This indicates that the rubber compound of the present invention forms a more stable bonding interface with the coupling skeleton treated with the base adhesive and top adhesive, which can reduce the risk of interface peeling under dynamic loads.

[0084] In summary, Examples 1-3, compared to Comparative Examples 1-3, simultaneously improved strength, toughness, elastic recovery, fatigue life, and skeleton bonding stability. This demonstrates that the present invention, through the combination of silane-modified carbon black graphene composite, polydopamine-coated halloysite zinc oxide composite, and bis-[3-(triethoxysilyl)propyl]disulfide, solves the technical problems of insufficient rubber reinforcement efficiency, short dynamic fatigue life, poor compression recovery, and insufficient reliability of the rubber-skeleton interface in existing couplings.

Claims

1. A method for preparing fatigue-resistant, highly elastic coupling rubber, characterized in that the steps include... include: S1. By weight, mix 55.0-70.0 parts of natural rubber, 15.0-30.0 parts of butadiene rubber, and 5.0-15.0 parts of hydrogenated nitrile butadiene rubber, and masticate to obtain a plasticized rubber compound; add 8.0-10.0 parts of composite processing aid, 30.0-60.0 parts of reinforcing carbon black, 10.0-25.0 parts of silica, 3.0-8.0 parts of silane-modified carbon black graphene composite, 2.0-6.0 parts of polydopamine-coated halloysite zinc oxide composite, and 0.6... 1.2 parts of bis-[3-(triethoxysilyl)propyl]disulfide, 2.0-4.0 parts of antioxidant, 0.5-2.0 parts of rubber processing aid, 0-8.0 parts of naphthenic oil and 1.0-3.0 parts of C5 petroleum resin are mixed and discharged to obtain a first-stage compound; the first-stage compound is left to stand, and 1.5-2.5 parts of sulfur, 1.2-2.2 parts of accelerator, 0.1-0.5 parts of scorch inhibitor and 1.0-2.0 parts of anti-reversion agent are added, mixed, thin-passed and sheeted to obtain the coupling rubber compound; S2. Degrease, sandblast, or shot blast the surface of the coupling frame to obtain a pretreated coupling frame; spray the primer and top coat onto the surface of the pretreated coupling frame in sequence, and dry to obtain a coupling frame with an adhesive layer; load the coupling rubber material into a mold, and mold and vulcanize it with the coupling frame with the adhesive layer, demold, and place at room temperature.

2. The method for preparing fatigue-resistant, high-elasticity coupling rubber according to claim 1, characterized in that, In step S1, the plasticizing temperature is 80-100℃, and the plasticizing time is 4-6 minutes; the composite processing aid is composed of zinc oxide, magnesium oxide, stearic acid, and zinc stearate; the reinforcing carbon black is composed of carbon black N330 and carbon black N550; the antioxidant is composed of antioxidant 4020 and antioxidant RD; the rubber processing aid is zinc soap SL-5050; the accelerator is composed of accelerator CZ, accelerator DM, and accelerator TMTD; the anti-scorching agent is anti-scorching agent CTP; and the anti-sulfurization reversion agent is anti-sulfurization reversion agent WK-901.

3. The method for preparing fatigue-resistant, highly elastic coupling rubber according to claim 1, characterized in that, In step S2, the base adhesive is Chemlok 205; the top adhesive is Chemlok 6125; the molding vulcanization step includes: heating the mold to 140-155℃, holding the mold under pressure at 10-22MPa for vulcanization; and placing the mold at room temperature for 10-20 hours.

4. The method for preparing fatigue-resistant, high-elasticity coupling rubber according to claim 1, characterized in that, The preparation method of the silane-modified carbon black graphene composite includes: A1. By weight, mix 45.0-65.0 parts of carbon black N330, 10.0-25.0 parts of carbon black N550, 2.0-6.0 parts of graphene oxide, 0.5-2.0 parts of polyvinylpyrrolidone, 180.0-260.0 parts of anhydrous ethanol and 40.0-80.0 parts of deionized water, disperse by ultrasonication, filter, wash with deionized water, and vacuum dry at 60-75℃ to obtain a pre-dispersed carbon black-graphene mixture. A2. Mix 3.0-8.0 parts of bis-[3-(triethoxysilyl)propyl]disulfide, 50.0-80.0 parts of anhydrous ethanol and 15.0-30.0 parts of deionized water, add glacial acetic acid to adjust the pH to 4.5-5.5, and stir and hydrolyze at 30-40℃ to obtain silane hydrolysate; disperse the pre-dispersed carbon black graphene mixture in 120.0-180.0 parts of anhydrous ethanol, sonicate, add silane hydrolysate, stir and react at 55-70℃, filter, wash with anhydrous ethanol, vacuum dry at 65-80℃, grind and sieve.

5. The method for preparing fatigue-resistant, highly elastic coupling rubber according to claim 4, characterized in that, In step A1, the ultrasonic dispersion time is 30-50 min; the vacuum drying time at 60-75℃ is 6-10 h.

6. The method for preparing fatigue-resistant, highly elastic coupling rubber according to claim 4, characterized in that, In step A2, the ultrasonic dispersion time is 20-40 min; the stirring hydrolysis time at 30-40℃ is 30-60 min; the stirring reaction time at 55-70℃ is 3-5 h; and the vacuum drying time at 65-80℃ is 8-12 h.

7. The method for preparing fatigue-resistant, high-elasticity coupling rubber according to claim 1, characterized in that, The preparation method of the polydopamine-coated halloysite zinc oxide composite includes: B1. By weight, mix 20.0-40.0 parts halloysite nanotubes, 180.0-260.0 parts deionized water and 40.0-70.0 parts anhydrous ethanol, disperse by ultrasonication, add 5.0-12.0 parts nano zinc oxide and 0.5-2.0 parts polyethylene glycol 400, disperse by ultrasonication, filter, and vacuum dry at 60-75℃ to obtain a halloysite-supported zinc oxide mixture; B2. Dissolve 0.8-2.0 parts of tris(hydroxymethyl)aminomethane in 80.0-120.0 parts of deionized water, and adjust the pH to 8.3-8.7 with hydrochloric acid to obtain a buffer solution; add the halloysite-supported zinc oxide mixture to 180.0-260.0 parts of deionized water, disperse by sonication, add the buffer solution, 3.0-7.0 parts of dopamine hydrochloride and 0.3-1.5 parts of tannic acid, stir and react in the dark at 25-35℃, centrifuge, wash with deionized water and anhydrous ethanol in sequence, vacuum dry at 55-70℃, grind and sieve.

8. The method for preparing fatigue-resistant, high-elasticity coupling rubber according to claim 7, characterized in that, In step B1, the vacuum drying time at 60-75℃ is 6-10 hours.

9. The method for preparing fatigue-resistant, highly elastic coupling rubber according to claim 7, characterized in that, In step B2, the ultrasonic dispersion time is 20-40 min; the stirring reaction time in the dark at 25-35℃ is 6-10 h; and the vacuum drying time at 55-70℃ is 10-16 h.

10. A fatigue-resistant, highly elastic coupling rubber, characterized in that, The fatigue-resistant, high-elasticity coupling rubber is prepared by the method according to any one of claims 1-9.

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