High-performance polyurethane elastomer for high-resilience motor vehicle seats and method for the production thereof

Abstract

The application relates to the field of polyurethane foaming materials, and particularly discloses a high-performance polyurethane elastomer for a high-rebound motor vehicle seat and a preparation method thereof, and the high-performance polyurethane elastomer for the high-rebound motor vehicle seat comprises the following components in parts by weight: polyether polyol 60-80 parts, a curing agent 40-60 parts, a foaming agent 1-2 parts, a catalyst 0.5-1 part, a chain extender 3-6 parts, a plasticizer 1-2 parts, a stabilizer 0.5-1 part, nano filler 2-6 parts, nano connecting material 1-4 parts and a flame retardant 1-2 parts; the preparation method comprises the following steps: uniformly mixing the polyether polyol, the nano connecting material, the nano filler and the flame retardant, then uniformly mixing and stirring the plasticizer, the chain extender and the stabilizer, finally uniformly mixing the foaming agent and the catalyst, defoaming, and obtaining a mixture; uniformly mixing the mixture and the curing agent, pouring into a mold, then performing a curing treatment, and obtaining a finished product; the finished product has the advantages of good rebound elasticity, good compression deformation resistance, good moisture and heat resistance and good tear resistance.

Description

Technical Field

[0001] This application relates to the field of polyurethane foam materials, and more specifically, it relates to a high-performance polyurethane elastomer for high-resilience electric vehicle seats and a method for preparing the same. Background Technology

[0002] The seats on high-speed trains generally need to have high elasticity and high resilience, so that they can quickly rebound and recover their deformation after being subjected to pressure, preventing them from collapsing after sitting for a long time. They also have good shock absorption and cushioning performance, which can reduce the transmission of vibration during train operation and improve the riding experience.

[0003] Currently, polyurethane elastomers are required in the manufacturing process of high-speed train seats. To ensure shock absorption and durability, polyurethane elastomers need to have good elasticity and tear resistance, as well as good resistance to compression deformation to reduce the problem of collapse caused by long-term high-pressure use. At the same time, polyurethane elastomers are easily affected by humid heat, and contact with high-temperature moisture can easily lead to performance degradation and affect their service life.

[0004] Therefore, how to prepare a new elastomer material for high-speed train seats with good resilience, good resistance to compression deformation, good resistance to damp heat and tearing is an urgent problem to be solved. Summary of the Invention

[0005] In order to prepare a new elastomer material for high-speed train seats with advantages such as good resilience, good resistance to compression deformation, good resistance to damp heat and tear resistance, this application provides a high-resilience high-performance polyurethane elastomer for high-speed train seats and its preparation method.

[0006] In a first aspect, this application provides a high-performance polyurethane elastomer for high-resilience high-speed train seats, employing the following technical solution: A high-performance polyurethane elastomer for high-resilience electric vehicle seats comprises the following raw materials in parts by weight: 60-80 parts of polyether polyol, 40-60 parts of curing agent, 1-2 parts of foaming agent, 0.5-1 part of catalyst, 3-6 parts of chain extender, 1-2 parts of plasticizer, 0.5-1 part of stabilizer, 2-6 parts of nanofiller, 1-4 parts of nanolinker, and 1-2 parts of flame retardant.

[0007] By adopting the above technical solution, polyether polyol, as a soft segment component, provides the flexibility and reversible deformation capability of the molecular chain. Combined with chain extender and curing agent, it forms crosslinking points, increases the crosslinking structure density, and improves the resilience of polyurethane elastomer. Combined with the nanofilling effect of nanofillers and nanolinkers, it further improves the network structure density of polyurethane elastomer and further improves the resilience of polyurethane elastomer.

[0008] Polyether polyols, in combination with foaming agents, generate gas during the reaction process, forming a porous structure. Combined with nanofillers, these nanofillers act as heterogeneous nucleation sites during foaming, increasing the number of cells, reducing cell diameter, and forming a uniform microporous structure. Furthermore, the synergistic effect of nanolinkers and nanofillers enables progressive compression. Under impact loads, the dense cell walls buckling, gas compression, and cell wall friction work together to dissipate kinetic energy, thereby improving the cushioning effect of the finished polyurethane elastomer.

[0009] The combination of polyether polyols, nanofillers, nanolinkers, and stabilizers can improve the heat and moisture stability of polyurethane elastomers, reduce the water vapor penetration path, prevent moisture diffusion, and make them less susceptible to moisture-induced reductions in elasticity and strength. The combination of nanofillers and nanolinkers with chain extenders and plasticizers improves the stability of the cell structure and acts as stress-dispersing connection points, thereby improving the tear resistance and compression resistance of the finished polyurethane elastomers.

[0010] Preferably, the nanofiller is composed of modified zirconium phosphate and modified mesoporous silica in a mass ratio of 1:1-2.

[0011] By adopting the above technical solution, zirconium phosphate, with its layered crystal structure and hydroxyl groups on the surface, possesses a high specific surface area and can serve as a heterogeneous nucleation center for foamed polyurethane elastomers. In the early stages of foaming, nuclei are aggregated on the zirconium phosphate surface, increasing the cell nucleation density, inhibiting cell merging and collapse, and improving the closed-cell rate and structural stability. Meanwhile, mesoporous silica has a hexagonal mesoporous structure, and the silanol groups on its surface can form a connecting network with the polyurethane soft segments. The guiding effect of the mesoporous structure further improves the uniformity of cell arrangement. Its mesoporous structure can also regulate the cell growth rate, improve the fineness, closed-cell rate, and structural stability of the cells, reduce water vapor permeation, and improve the dimensional stability of the polyurethane elastomer under humid and hot conditions. Furthermore, the rigid zirconium phosphate and mesoporous silica form a binding resistance around the cell walls, which can effectively prevent the cells from collapsing and breaking under high temperature or stress, improving the stability of the cell structure. Thus, the polyurethane foam material has high resilience and high buffering capacity.

[0012] Polyurethane elastomers formed by zirconium phosphate and mesoporous silica surface hydroxyl groups and polyether polyols have good cross-linking effect, improving the density of the cross-linking structure, thereby improving the compressive strength and tear resistance of polyurethane elastomers; and the layered stress dispersion structure of zirconium phosphate, combined with the stress absorption effect of mesoporous silica, improves toughness, thereby further improving the tear resistance and compressive strength of polyurethane elastomers.

[0013] Preferably, the modified zirconium phosphate is prepared by treating zirconium phosphate with polyetheramine at a mass ratio of 1:0.3-0.6.

[0014] By employing the above technical solution, polyetheramine treatment of zirconium phosphate improves the dispersion stability of zirconium phosphate in polyether polyols. The intercalated nanosheet structure can increase the density of heterogeneous nucleation sites, increase the number of gas nuclei, increase the closed-cell rate of cells, and improve cell stability. Furthermore, the long-chain polyether backbone of polyetheramine has good compatibility with polyether polyols, improving the density and stability of the crosslinking network. The resulting soft-chain-soft-chain structural transition zone can resist impact while protecting the cell walls from damage, thereby improving the resilience and cushioning of polyurethane foam materials. Simultaneously, combined with the rigidity of zirconium phosphate, when the polyurethane elastomer is subjected to impact, the polyetheramine on the zirconium phosphate surface and the polyurethane matrix, through flexible buffering combined with the rigid resistance of zirconium phosphate, can improve the tear resistance and compression deformation resistance of polyurethane elastomers.

[0015] Preferably, the modified mesoporous silica is prepared by loading perfluoropolyether diol onto mesoporous silica in a mass ratio of 1:0.1-0.25:0.1-0.25 and then coating it with polycaprolactone diol.

[0016] By adopting the above technical solution, mesoporous silica not only contains an open mesoporous structure, but also has hydroxyl groups on its surface, which facilitates the loading of all polyether glycols and their connection with the hydroxyl groups on the surface of perfluoropolyether glycols. Then, polycaprolactone diol is used to block the pores of the mesoporous silica, preventing the mesoporous silica from adsorbing moisture and affecting the uniformity of the distribution of the water-dispersing foaming agent during the raw material mixing stage, thereby ensuring foaming density and foaming uniformity.

[0017] At a foaming temperature of 60-80℃, polycaprolactone diol melts and flows, exposing perfluoropolyether diol. Polycaprolactone diol has a long-chain flexible structure and contains hydroxyl groups, which can connect with substances such as polyether polyols, improving the connection stability between modified mesoporous silica and polyurethane matrix. Combined with the hydrophobic properties of polycaprolactone diol and perfluoropolyether diol, as well as the dense cross-linked network structure, it improves the moisture and heat resistance of polyurethane elastomer.

[0018] Preferably, the nanolinking material is composed of nanocellulose and hydroxyapatite microspheres in a mass ratio of 1:0.2-0.5.

[0019] By adopting the above technical solution, the nanocellulose and hydroxyapatite microspheres contain hydroxyl groups on their surface, which can not only improve the cross-linking network between the nano-linking material and polyether polyol and isocyanate, but also act as heterogeneous nucleating agents to promote uniform gas nucleation, improve the elasticity and cushioning of the finished polyurethane elastomer. Furthermore, the nanocellulose and hydroxyapatite microspheres can improve the toughness of the polyurethane elastomer. Combined with the crack orientation change induced by the hydroxyapatite microspheres and the connecting and supporting effect of the nanocellulose, the tear resistance of the polyurethane elastomer is further improved.

[0020] Preferably, the nanocellulose is prepared by treating nanocellulose filaments with an ethylenediamine solution.

[0021] By adopting the above technical solution, amino groups are introduced on the surface of nanocellulose filaments after ethylenediamine treatment. These groups can react and connect rapidly with isocyanate during the foaming process, thereby improving the cross-linking effect between nanocellulose and the polyurethane matrix, increasing the foaming closed-cell rate, and ensuring high density and high structural stability of the bubbles while uniformly dispersing the foaming agent.

[0022] Preferably, the hydroxyapatite microspheres are prepared by loading sucrose polyether onto porous hydroxyapatite microspheres in a mass ratio of 1:0.1-0.2.

[0023] By adopting the above technical solution, porous hydroxyapatite microspheres are tough and contain hydroxyl groups on their surface. Their high specific surface area promotes denser and more uniform nucleation of bubbles, improving the fineness and uniformity of the pores. The multi-hydroxyl structure of sucrose polyether can connect with the porous hydroxyapatite microspheres on the one hand, and can be compatible with polyether polyols on the other hand, improving the crosslinking effect of hydroxyapatite microspheres with polyether polyols and isocyanates. Through the formed connecting phase interface, the pore wall merging or rupture is inhibited, improving the uniformity of the pores, thereby improving the elasticity and cushioning of polyurethane elastomers.

[0024] Sucrose polyether can reduce the density of water molecule adsorption sites, and the hydroxyl groups on the surface of hydroxyapatite microspheres can react with isocyanates to form urea bonds, which in turn form a high-density cross-linked network with polyether polyol segments, extending the diffusion path of water molecules, reducing water absorption, and improving resistance to damp heat. Furthermore, the high degree of cross-linking of sucrose polyether with high toughness, combined with the high degree of cross-linking of hydroxyapatite microspheres, can improve tear resistance.

[0025] Preferably, the plasticizer is composed of dioctyl phthalate and tri(butoxyethyl) phosphate in a mass ratio of 1:0.1-0.3.

[0026] By adopting the above technical solutions, dioctyl phthalate and tri(butoxyethyl) phosphate can improve the toughness of polyurethane elastomers; and dioctyl phthalate and tri(butoxyethyl) phosphate have certain flame retardant effects, which can also improve the flame retardant effect of polyurethane elastomers.

[0027] Preferably, the stabilizer is composed of carbodiimide and hydroxyl silicone oil in a mass ratio of 1:0.5-1.

[0028] By adopting the above technical solution, carbodiimide has good waterproof stability, and combined with the hydrophobicity of hydroxyl silicone oil, it further improves the hygrothermal stability of polyurethane foam materials.

[0029] Secondly, this application provides a method for preparing a high-performance polyurethane elastomer for high-resilience electric vehicle seats, employing the following technical solution: A method for preparing a high-performance polyurethane elastomer for high-resilience electric vehicle seats includes the following steps: S1. Mix polyether polyol, nano-linking material, nano-filler and flame retardant evenly, then add plasticizer, chain extender and stabilizer and mix evenly, finally add foaming agent and catalyst and mix evenly, and after degassing, obtain the mixture. S2. Mix the mixture and curing agent evenly, pour it into the mold, and then cure it to obtain the finished product.

[0030] By adopting the above technical solution, the prepared polyurethane elastomer has the advantages of high resilience, good cushioning, good resistance to damp heat, and good tear resistance.

[0031] In summary, this application has the following beneficial effects: 1. Polyether polyols, as soft segment components, provide flexibility and reversible deformation capability of molecular chains. Combined with chain extenders and curing agents, they form crosslinking points, increase the crosslinking structure density, and improve the resilience of polyurethane elastomers. Combined with the nanofilling effect of nanofillers and nanolinkers, they further improve the network structure density of polyurethane elastomers and further improve the resilience of polyurethane elastomers.

[0032] 2. Polyether polyols, in combination with foaming agents, generate gas during the reaction process, forming a porous structure. Combined with nanofillers, these nanofillers act as heterogeneous nucleation sites during foaming, increasing the number of cells, reducing cell diameter, and forming a uniform microporous structure. Furthermore, the synergistic effect of nanolinkers and nanofillers enables progressive compression. Under impact loads, the dense cell walls buckling, gas compression, and cell wall friction work together to dissipate kinetic energy, improving the cushioning effect of the finished polyurethane elastomer.

[0033] 3. The combination of polyether polyol, nanofiller, nano-linker and stabilizer can improve the heat and moisture stability of polyurethane elastomer, reduce the water vapor penetration path, prevent moisture diffusion, and make it less susceptible to moisture-induced reduction in its elasticity and strength. The combination of nanofiller and nano-linker with chain extender and plasticizer can improve the stability of the cell structure and act as stress dispersion connection points, thereby improving the tear resistance and compression deformation resistance of the finished polyurethane elastomer. Detailed Implementation

[0034] The present application will be further described in detail below with reference to the embodiments.

[0035] Preparation examples of nanofillers All of the following ingredients are commercially available.

[0036] Preparation Example 1: The nanofiller was prepared using the following method: 1 kg of zirconium phosphate was dispersed in 10 kg of ethanol. The average particle size of zirconium phosphate was 80 nm. Then, 0.5 kg of polyetheramine was added. After ultrasonic dispersion for 20 min, the temperature was raised to 50 °C and stirred at 200 r / min for 2 h. During the process, ethanol was continuously added to maintain the ethanol content. Then, zirconium phosphate was separated by filtration and dried at room temperature to obtain modified zirconium phosphate. 1 kg of mesoporous silica with an average particle size of 100 nm was placed in 10 kg of ethanol and ultrasonically dispersed for 10 min. Then, 0.2 kg of perfluoropolyether glycol was added and ultrasonically dispersed for another 10 min. The temperature was raised to 50 °C and stirred at 200 r / min for 2 h, with ethanol continuously added to maintain the ethanol level. Then, 90% of the ethanol was distilled off under reduced pressure at 55 °C to obtain the composite material. 0.2 kg of polycaprolactone glycol was placed in 3 kg of ethyl acetate and stirred until completely dissolved to obtain the solution. The solution was added dropwise to the composite material over 50 min. Then, the mixture was stirred at 45 °C for 1 h and finally air-dried at 50 °C to obtain the modified mesoporous silica. 1 kg of modified zirconium phosphate and 1.5 kg of modified mesoporous silica were mixed and stirred evenly to obtain nanofillers.

[0037] Preparation Example 2: The difference between this preparation example and Preparation Example 1 is that: 1 kg of zirconium phosphate was dispersed in 10 kg of ethanol. The average particle size of zirconium phosphate was 80 nm. Then, 0.3 kg of polyetheramine was added. After ultrasonic dispersion for 20 min, the temperature was raised to 50 °C and stirred at 200 r / min for 2 h. During the process, ethanol was continuously added to maintain the ethanol content. Then, zirconium phosphate was separated by filtration and dried at room temperature to obtain modified zirconium phosphate. 1 kg of mesoporous silica with an average particle size of 100 nm was placed in 10 kg of ethanol and ultrasonically dispersed for 10 min. Then, 0.1 kg of perfluoropolyether glycol was added and ultrasonically dispersed for another 10 min. The temperature was raised to 50 °C and stirred at 200 r / min for 2 h, with ethanol continuously added to maintain the ethanol level. Then, 90% of the ethanol was distilled off under reduced pressure at 55 °C to obtain the composite material. 0.1 kg of polycaprolactone glycol was placed in 3 kg of ethyl acetate and stirred until completely dissolved to obtain the solution. The solution was added dropwise to the composite material over 50 min. Then, the mixture was stirred at 45 °C for 1 h and finally air-dried at 50 °C to obtain the modified mesoporous silica. 1 kg of modified zirconium phosphate and 1 kg of modified mesoporous silica were mixed and stirred evenly to obtain nanofillers.

[0038] Preparation Example 3: The difference between this preparation example and Preparation Example 1 is that: 1 kg of zirconium phosphate was dispersed in 10 kg of ethanol. The average particle size of zirconium phosphate was 80 nm. Then, 0.6 kg of polyetheramine was added. After ultrasonic dispersion for 20 min, the temperature was raised to 50 °C and stirred at 200 r / min for 2 h. During the process, ethanol was continuously added to maintain the ethanol content. Then, zirconium phosphate was separated by filtration and dried at room temperature to obtain modified zirconium phosphate. 1 kg of mesoporous silica with an average particle size of 100 nm was placed in 10 kg of ethanol and ultrasonically dispersed for 10 min. Then, 0.25 kg of perfluoropolyether glycol was added and ultrasonically dispersed for another 10 min. The temperature was raised to 50 °C and stirred at 200 r / min for 2 h, with ethanol continuously added to maintain the ethanol level. Then, 90% of the ethanol was distilled off under reduced pressure at 55 °C to obtain the composite material. 0.25 kg of polycaprolactone glycol was placed in 3 kg of ethyl acetate and stirred until completely dissolved to obtain the solution. The solution was added dropwise to the composite material over 50 min. Then, the mixture was stirred at 45 °C for 1 h and finally air-dried at 50 °C to obtain the modified mesoporous silica. 1 kg of modified zirconium phosphate and 2 kg of modified mesoporous silica were mixed and stirred evenly to obtain nanofillers.

[0039] Preparation example of nano-linking material All of the following ingredients are commercially available.

[0040] Preparation Example 4: The nano-linking material was prepared using the following method: 1 kg of nanocellulose filaments were placed in 10 kg of ethylenediamine solution. The average length of the nanocellulose filaments was 100 nm. The nanocellulose filaments were ultrasonically dispersed for 20 min, filtered out, and dried to obtain nanocellulose. 100g of porous hydroxyapatite microspheres with an average particle size of 100nm were placed in 2000mL of anhydrous ethanol and ultrasonically dispersed for 20min to obtain a dispersion. 10g of sucrose polyether was placed in 100mL of anhydrous ethanol and stirred to dissolve, obtaining a sucrose polyether solution. The sucrose polyether solution was added dropwise to the dispersion, and ultrasonication was continued for 20min. The temperature was raised to 45℃, and the mixture was stirred at 200r / min for 20min. Then, 90% of the ethanol was distilled off, and the mixture was air-dried at room temperature to obtain hydroxyapatite microspheres. 1 kg of nanocellulose and 0.4 kg of hydroxyapatite microspheres were mixed and stirred evenly to obtain nano-connecting material.

[0041] Preparation Example 5: The difference between this preparation example and Preparation Example 4 is that: 1 kg of nanocellulose filaments were placed in 10 kg of ethylenediamine solution. The average length of the nanocellulose filaments was 100 nm. The nanocellulose filaments were ultrasonically dispersed for 20 min and then filtered out to obtain nanocellulose. 100g of porous hydroxyapatite microspheres with an average particle size of 100nm were placed in 2000mL of anhydrous ethanol and ultrasonically dispersed for 20min to obtain a dispersion. 15g of sucrose polyether was placed in 100mL of anhydrous ethanol and stirred to dissolve, obtaining a sucrose polyether solution. The sucrose polyether solution was added dropwise to the dispersion, and ultrasonication was continued for 20min. The temperature was raised to 45℃, and the mixture was stirred at 200r / min for 20min. Then, 90% of the ethanol was distilled off, and the mixture was air-dried at room temperature to obtain hydroxyapatite microspheres. 1 kg of nanocellulose and 0.2 kg of hydroxyapatite microspheres were mixed and stirred evenly to obtain nano-connecting material.

[0042] Preparation Example 6: The difference between this preparation example and Preparation Example 4 is that: 1 kg of nanocellulose filaments were placed in 10 kg of ethylenediamine solution. The average length of the nanocellulose filaments was 100 nm. The nanocellulose filaments were ultrasonically dispersed for 20 min and then filtered out to obtain nanocellulose. 100g of porous hydroxyapatite microspheres with an average particle size of 100nm were placed in 2000mL of anhydrous ethanol and ultrasonically dispersed for 20min to obtain a dispersion. 20g of sucrose polyether was placed in 180mL of anhydrous ethanol and stirred to dissolve, obtaining a sucrose polyether solution. The sucrose polyether solution was added dropwise to the dispersion, and ultrasonication was continued for 20min. The temperature was raised to 45℃, and the mixture was stirred at 200r / min for 20min. Then, 90% of the ethanol was distilled off, and the mixture was air-dried at room temperature to obtain hydroxyapatite microspheres. 1 kg of nanocellulose and 0.5 kg of hydroxyapatite microspheres were mixed and stirred evenly to obtain nano-connecting material. Example

[0043] All of the following ingredients are commercially available.

[0044] Example 1: A high-performance polyurethane elastomer for high-resilience high-speed train seats: The following ingredients were prepared: 70 kg of polyether polyol, 50 kg of curing agent, 1.5 kg of foaming agent, 0.8 kg of catalyst, 5 kg of chain extender, 1.5 kg of plasticizer, 0.8 kg of stabilizer, 4 kg of nanofiller, 2 kg of nanolinker, and 1.5 kg of flame retardant. The curing agent was diisocyanate; the foaming agent was water; the catalyst was stannous octoate; the chain extender was 1,4-butanediol; the plasticizer consisted of dioctyl phthalate and tris(butoxyethyl) phosphate in a mass ratio of 1:0.2; the stabilizer consisted of carbodiimide and hydroxyl silicone oil in a mass ratio of 1:1; the nanofiller was the nanofiller prepared in Preparation Example 1, and the nanolinker was the nanolinker prepared in Preparation Example 4; the flame retardant was ammonium polyphosphate. The preparation method is as follows: S1. Mix polyether polyol, nano-linking material, nano-filler and flame retardant evenly, then add plasticizer, chain extender and stabilizer and mix evenly, finally add foaming agent and catalyst and mix evenly, and after degassing, obtain the mixture. S2. Mix the mixture and curing agent evenly, remove bubbles, pour into a preheated 40℃ mold and keep warm for 30 minutes, then cure at 60℃ for 6 hours, cool, and obtain the finished product.

[0045] Example 2: The difference between this example and Example 1 is that: The following ingredients were prepared: 60 kg of polyether polyol, 40 kg of curing agent, 1 kg of foaming agent, 0.5 kg of catalyst, 3 kg of chain extender, 1 kg of plasticizer, 0.5 kg of stabilizer, 2 kg of nanofiller, 1 kg of nanolinker, and 1 kg of flame retardant. The curing agent was diisocyanate; the foaming agent was water; the catalyst was stannous octoate; the chain extender was 1,4-butanediol; the plasticizer was composed of dioctyl phthalate and tris(butoxyethyl) phosphate in a mass ratio of 1:0.1; the stabilizer was composed of carbodiimide and hydroxyl silicone oil in a mass ratio of 1:0.5; the nanofiller was the nanofiller prepared in Preparation Example 2, and the nanolinker was the nanolinker prepared in Preparation Example 5.

[0046] Example 3: The difference between this example and Example 1 is that: The following ingredients were prepared: 80 kg of polyether polyol, 60 kg of curing agent, 2 kg of foaming agent, 1 kg of catalyst, 6 kg of chain extender, 2 kg of plasticizer, 1 kg of stabilizer, 6 kg of nanofiller, 4 kg of nanolinker, and 2 kg of flame retardant. The curing agent was diisocyanate; the foaming agent was water; the catalyst was stannous octoate; the chain extender was 1,4-butanediol; the plasticizer was composed of dioctyl phthalate and tri(butoxyethyl) phosphate in a mass ratio of 1:0.3; the stabilizer was composed of carbodiimide and hydroxyl silicone oil in a mass ratio of 1:0.8; the nanofiller was prepared using the nanofiller prepared in Preparation Example 3, and the nanolinker was prepared using the nanolinker prepared in Preparation Example 6.

[0047] Example 4: The difference between this example and Example 1 is that: In the nanofiller, the modified zirconium phosphate was replaced with an equal mass of zirconium phosphate.

[0048] Example 5: The difference between this example and Example 1 is that: In the nanofiller, the modified mesoporous silica was replaced with an equal mass of mesoporous silica.

[0049] Example 6: The difference between this example and Example 1 is that: No perfluoropolyether diol was added to the modified mesoporous silica with nanofiller.

[0050] Example 7: The difference between this example and Example 1 is that: In the nano-linking material, nanocellulose is replaced with an equal mass of nanocellulose filaments, meaning that the nanocellulose filaments have not been treated with ethylenediamine solution.

[0051] Example 8: The difference between this example and Example 1 is that: In the nano-linking material, porous hydroxyapatite microspheres of equal mass are used to replace hydroxyapatite microspheres, meaning that the porous hydroxyapatite microspheres have not been treated with sucrose polyether.

[0052] Performance testing 1. Elasticity testing Polyurethane elastomers were prepared using the methods described in Examples 1-5 and 7-8, respectively. The resilience was tested according to GB / T 6670, and the resilience rate was recorded.

[0053] 2. Compression permanent deformation test Polyurethane elastomers were prepared using the methods described in Examples 1-8, and the compression set was tested according to GB / T 6669. The compression set rate was recorded.

[0054] 3. Moist heat resistance test Polyurethane elastomers were prepared using the methods described in Examples 1-6 and 8, respectively. The polyurethane elastomers were sprayed with hot water at 85°C once, dried for 12 hours, sprayed with hot water at 85°C once again, dried for 12 hours, and this process was repeated 10 times. The compression set was then tested according to GB / T 6669, and the compression set rate was recorded.

[0055] 4. Tear resistance test Polyurethane elastomers were prepared using the methods described in Examples 1-5 and 7-8, respectively. The tear strength was tested according to GB / T 10808, and the data were recorded.

[0056] Table 1 Performance Test Table (In the table, " / " indicates that the corresponding embodiment did not test this item and there is no data)

[0057] As can be seen from Examples 1-3 and Table 1, the polyurethane elastomer prepared in this application has high resilience, low compression set, and after hygrothermal treatment, the compression set changes little and the tear strength is high. This indicates that the finished polyurethane elastomer has the advantages of good resilience, good cushioning, good hygrothermal resistance, and good tear resistance.

[0058] Combining Examples 1 and 4-8 with Table 1, it can be seen that in Example 4, the modified zirconium phosphate was replaced with an equal mass of zirconium phosphate in the nanofiller. Compared with Example 1, Example 4 had a lower resilience, higher compression set, and lower tear strength. This indicates that the long-chain polyether skeleton of polyetheramine has good compatibility with polyether polyol, which improves the crosslinking network density and stability, and enhances the resilience, cushioning, and tear resistance of polyurethane foam materials.

[0059] In Example 5, the modified mesoporous silica was replaced with an equal mass of mesoporous silica in the nanofiller. Compared with Example 1, the resilience of Example 5 was lower than that of Example 1, the compression set was higher than that of Example 1, and the tear strength was lower than that of Example 1. This indicates that polycaprolactone diol has a long-chain flexible structure and contains hydroxyl groups, which can be linked with substances such as polyether polyols to improve the connection stability between the modified mesoporous silica and the polyurethane matrix. Combined with the toughness of polycaprolactone diol, it improves the elasticity, cushioning and tear resistance of the polyurethane elastomer.

[0060] In Example 6, no perfluoropolyether glycol was added to the modified mesoporous silica with nanofiller. Compared to Example 1, the polyurethane elastomer of Example 6 showed a higher increase in compression set after hygrothermal treatment than that of Example 1. This indicates that the polycaprolactone glycol melts and flows, exposing the perfluoropolyether glycol. Combined with the hydrophobic properties of polycaprolactone glycol and perfluoropolyether glycol, as well as the dense cross-linked network structure, the hygrothermal resistance of the polyurethane elastomer is improved.

[0061] In Example 7, the nano-cellulose was replaced with an equal mass of nanocellulose filaments, meaning the nanocellulose filaments were not treated with ethylenediamine solution. Compared to Example 1, Example 7 showed a lower resilience, higher compression set, and lower tear strength. This indicates that ethylenediamine treatment introduces amino groups onto the surface of the nanocellulose filaments, enabling them to react and connect rapidly with isocyanate during foaming. This improves the crosslinking effect between nanocellulose and the polyurethane matrix, increases the foaming closed-cell rate, and the high aspect ratio of nanocellulose, combined with the formed three-dimensional network skeleton, ensures high bubble density and high structural stability, thereby improving the resilience, cushioning, and tear resistance of the polyurethane elastomer.

[0062] In Example 8, porous hydroxyapatite microspheres of equal mass were used to replace the hydroxyapatite microspheres in the nano-linking material. That is, the porous hydroxyapatite microspheres were not treated with sucrose polyether. Compared with Example 1, the resilience of Example 8 was lower than that of Example 1, the compression set was higher than that of Example 1, and the tear strength was lower than that of Example 1. This shows that the polyhydroxy structure of sucrose polyether can connect with porous hydroxyapatite microspheres on the one hand, and can be compatible with polyether polyol on the other hand, improving the crosslinking effect of hydroxyapatite microspheres with polyether polyol and isocyanate. Through the formed connecting phase interface, the cell wall merging or rupture is inhibited, the uniformity of the cell is improved, thereby improving the elasticity, cushioning and tear resistance of polyurethane elastomer.

[0063] This specific embodiment is merely an explanation of this application and is not intended to limit it. After reading this specification, those skilled in the art can make modifications to this embodiment without contributing any inventive step, but such modifications are protected by patent law as long as they fall within the scope of the claims of this application.

Claims

1. A high-performance polyurethane elastomer for high-resilience electric vehicle seats, characterized in that, The raw materials include the following parts by weight: 60-80 parts of polyether polyol, 40-60 parts of curing agent, 1-2 parts of foaming agent, 0.5-1 part of catalyst, 3-6 parts of chain extender, 1-2 parts of plasticizer, 0.5-1 part of stabilizer, 2-6 parts of nanofiller, 1-4 parts of nano binder, and 1-2 parts of flame retardant.

2. The high-performance polyurethane elastomer for high-resilience electric vehicle seats according to claim 1, characterized in that: The nanofiller consists of modified zirconium phosphate and modified mesoporous silica in a mass ratio of 1:1-2.

3. The high-performance polyurethane elastomer for high-resilience high-speed train seats according to claim 2, characterized in that, The modified zirconium phosphate is prepared by treating zirconium phosphate with polyetheramine at a mass ratio of 1:0.3-0.

6.

4. The high-performance polyurethane elastomer for high-resilience high-speed train seats according to claim 2, characterized in that, The modified mesoporous silica was prepared by loading perfluoropolyether diol onto mesoporous silica in a mass ratio of 1:0.1-0.25:0.1-0.25 and then coating it with polycaprolactone diol.

5. The high-performance polyurethane elastomer for high-resilience train seats according to claim 1, characterized in that, The nanolinking material is composed of nanocellulose and hydroxyapatite microspheres in a mass ratio of 1:0.2-0.

5.

6. The high-performance polyurethane elastomer for high-resilience high-speed train seats according to claim 5, characterized in that, The nanocellulose is prepared by treating nanocellulose filaments with an ethylenediamine solution.

7. The high-performance polyurethane elastomer for high-resilience high-speed train seats according to claim 5, characterized in that, The hydroxyapatite microspheres were prepared by loading sucrose polyether onto porous hydroxyapatite microspheres in a mass ratio of 1:0.1-0.

2.

8. The high-performance polyurethane elastomer for high-resilience high-speed train seats according to claim 1, characterized in that, The plasticizer is composed of dioctyl phthalate and tri(butoxyethyl) phosphate in a mass ratio of 1:0.1-0.

3.

9. The high-performance polyurethane elastomer for high-resilience electric vehicle seats according to claim 1, characterized in that, The stabilizer is composed of carbodiimide and hydroxyl silicone oil in a mass ratio of 1:0.5-1.

10. A method for preparing a high-resilience high-performance polyurethane elastomer for high-performance vehicle seats according to any one of claims 1-9, characterized in that, Includes the following steps: S1. Mix polyether polyol, nano-linking material, nano-filler and flame retardant evenly, then add plasticizer, chain extender and stabilizer and mix evenly, finally add foaming agent and catalyst and mix evenly, and after degassing, obtain the mixture. S2. Mix the mixture and curing agent evenly, pour it into the mold, and then cure it to obtain the finished product.

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