Processing technology of aluminum-based multi-phase composite ductile strengthening rail for new energy vehicle sunroof

Abstract

The application discloses a processing technology of an aluminum-based multi-phase composite toughening reinforcing guide rail for a sunroof of a new energy vehicle, and comprises the following steps: S1, nano-aluminum nitride pretreatment; S2, nano-aluminum nitride surface coating; S3, preparation of a silica coating layer; S4, nano-aluminum nitride composite modification; S5, smelting of an aluminum alloy; S6, stainless steel fiber addition and casting; S7, homogenization treatment; and S8, subsequent treatment. The continuous skeleton structure formed by the stainless steel fiber can disperse local stress concentration and avoid local plastic deformation when force is applied. The nano-aluminum nitride@silica-silane particle is dispersedly distributed between the aluminum alloy matrix and the fiber gap, hinders dislocation movement through dispersion strengthening, and reduces fatigue crack initiation sites. Under the synergistic action of the two, the tensile strength and impact toughness of the material are greatly improved, and the guide rail is suitable for use of a large sunroof.

Description

Technical Field

[0001] This invention belongs to the field of new energy vehicle technology, and in particular relates to the processing technology of aluminum-based multiphase composite toughness-reinforced guide rails for sunroofs of new energy vehicles. Background Technology

[0002] With the rapid expansion of the new energy vehicle market, sunroof systems have evolved from traditional luxury car features to a core element enhancing vehicle product competitiveness. The installation rate of panoramic sunroofs and panoramic sunroofs has exceeded 65%, becoming a mainstream feature in new energy vehicles. As the core load-bearing and transmission component of the sunroof system, the sunroof rail undertakes crucial functions such as guiding the opening and closing of the glass, load transfer, and sealing. Its performance directly affects the sunroof's operational stability, quietness, service life, and overall vehicle safety redundancy, making it a key element in ensuring a balance between "open experience" and "vehicle performance."

[0003] Traditional single aluminum alloy guide rails are not strong enough, and in high and low temperature cycling environments (-40℃ to +40℃), they are prone to internal stress due to the mismatch of the material's thermal expansion coefficients, which can cause guide rail deformation and slippage, affecting the operational stability of the sunroof system and making them unsuitable for use with large-area, high-load panoramic sunroof guide rails. Summary of the Invention

[0004] To address the problems in the prior art, the present invention proposes the following technical solution:

[0005] S1, nano-aluminum nitride pretreatment;

[0006] After adding nano-aluminum nitride particles to anhydrous ethanol solution, polyethylene glycol 6000 of 0.5% by mass of aluminum nitride was added. The mass ratio of aluminum nitride to anhydrous ethanol was 1:20. After ultrasonic dispersion for 30 min, 1 mol / L nitric acid of 3% by mass of aluminum nitride was added to adjust the pH of the solution to 3-4 in order to activate the hydroxyl groups on the surface of aluminum nitride.

[0007] S2, nano-aluminum nitride surface coating;

[0008] A mixture of tetraethyl orthosilicate and anhydrous ethanol is slowly added dropwise to the solution from step S1 at a rate of 1 mL / min. The mixture of tetraethyl orthosilicate and anhydrous ethanol accounts for 30%-60% of the mass of nano-aluminum nitride, and the mass ratio of tetraethyl orthosilicate to anhydrous ethanol is 1:3. Then, ammonia water is added dropwise to adjust the pH of the solution to 8-9, which triggers the hydrolysis and condensation of tetraethyl orthosilicate on the surface of nano-aluminum nitride to generate silicon dioxide.

[0009] S3. Prepare a silica coating layer;

[0010] The solution from step S2 was heated to 50°C and stirred for 2 hours. The solution was then filtered to collect the particles. The particles were washed and dried multiple times with anhydrous ethanol. Subsequently, the particles were calcined at 300-350°C for 1 hour under nitrogen protection to form a 2-5 nm thick silica coating layer on the surface of the nano-aluminum nitride particles, thus producing nano-aluminum nitride@silica particles.

[0011] S4, nano-aluminum nitride composite modification;

[0012] The nano-aluminum nitride@silica particles prepared in step S3 were added to anhydrous ethanol at a mass ratio of 1:20. After ultrasonic dispersion for 20 min, 10%-15% of KH-550 silane coupling agent (by mass of nano-aluminum nitride@silica) was added. The mixture was heated to 60℃ and stirred for 1.5 h. After filtration, washing and drying, “aluminum nitride@silica-silane” composite modified aluminum nitride particles were obtained.

[0013] S5, smelting aluminum alloys;

[0014] Aluminum alloy is added to a vacuum melting furnace, vacuumed to ≤10Pa and then purged with argon for protection. The temperature is raised to 720℃-760℃ to completely melt the aluminum alloy. Then the temperature is lowered to the semi-solid temperature range and held. The aluminum alloy accounts for 92%-94% of the total mass. Step S4 is added to prepare composite modified aluminum nitride particles, which account for 2%-3% of the total mass. The particles are stirred at 300r / min for 30min to ensure uniform dispersion.

[0015] S6, stainless steel fiber addition and casting;

[0016] Stainless steel fibers are alkali-washed and acid-washed to remove the surface oxide layer. After being coated with an aluminum-silicon alloy layer, they are added to a vacuum melting furnace. The stainless steel fibers account for 3%-5% of the total mass. The stirring speed is adjusted to 200 r / min and stirred for 20 min. The composite modified aluminum nitride particles and stainless steel fibers are uniformly dispersed in the aluminum alloy melt to form a continuous and interwoven reinforcing phase network structure. After being stirred evenly, the mixture is poured into a mold to form a composite billet.

[0017] S7. Homogenization treatment;

[0018] The composite billet is placed in a heating furnace and held at 460℃-480℃ for 6-10 hours. It is then furnace cooled or air cooled to room temperature to eliminate component segregation and optimize the uniformity of the microstructure.

[0019] S8. Subsequent processing;

[0020] The preheated billet is hot-extruded into shape, and then subjected to solution treatment, graded aging heat treatment, precision machining and surface treatment to finally obtain the finished guide rail.

[0021] As a preferred embodiment of the above technical solution, the aluminum-silicon alloy layer plating on the surface of the stainless steel fiber in step S6 includes the following:

[0022] Stainless steel fibers with the oxide layer removed are dispersed and immersed in molten aluminum-silicon alloy at 720℃-750℃ and held for 3-5 minutes to uniformly coat the fiber surface with an aluminum-silicon alloy layer of 1-3μm thickness. After removal, the fibers are rapidly cooled to room temperature, washed multiple times with deionized water, dried at 120℃ for 2 hours, and then annealed at 300℃ for 30 minutes under nitrogen protection.

[0023] As a preferred embodiment of the above technical solution, the nano-aluminum nitride particles have a particle size of 50-200 nm and a purity of ≥99.5%.

[0024] As a preferred embodiment of the above technical solution, the stainless steel fiber is of type 304 or 316, and the stainless steel fiber has a diameter of 5-10μm and a length of 50-80μm.

[0025] As a preferred embodiment of the above technical solution, the aluminum alloy is 6061 or 7075. When the aluminum alloy is 6061, its semi-solid insulation temperature is 590℃-620℃. When the aluminum alloy is 7075, its semi-solid insulation temperature is 620℃-640℃.

[0026] As a preferred embodiment of the above technical solution, in steps S1 and S4, the ultrasonic dispersion power is 300W and the frequency is 40kHz.

[0027] As a preferred embodiment of the above technical solution, in step S3, anhydrous ethanol is completely removed by washing, drying, and calcination. Polyethylene glycol 6000, nitric acid, and ammonia are discharged with the washing waste liquid or evaporated during the drying process, and are ultimately completely removed without residue.

[0028] As a preferred embodiment of the above technical solution, in step S4, the anhydrous ethanol is completely evaporated and removed during the drying process, leaving no residue.

[0029] The beneficial effects of this invention are as follows:

[0030] 1. In the reinforcing phase network structure, stainless steel fibers form a continuous skeleton structure, which acts as the "main reinforcing phase" to bear the main external force. It can disperse local stress concentration and avoid local plastic deformation under stress. Meanwhile, nano-aluminum nitride@silica-silane particles are dispersed in the aluminum alloy matrix and fiber gaps. While refining the matrix grains, they also hinder dislocation movement through "dispersion strengthening" and reduce fatigue crack initiation sites. Under the synergistic effect of the two, the brittleness tendency of the aluminum alloy matrix at low temperature is alleviated, and the tensile strength and impact toughness of the material are greatly improved, thus making it suitable for use in the guide rail of large skylights.

[0031] 2. Nano-aluminum nitride, as the core reinforcing phase, provides strength and wear resistance to the material by utilizing its high hardness, excellent thermal conductivity, and nano-size effect. The silica coating layer on the surface of nano-aluminum nitride blocks direct contact between aluminum nitride and molten aluminum, preventing hydrolysis and oxidation of aluminum nitride at high temperatures. On the other hand, it improves the interfacial wettability between the reinforcing phase and the matrix by utilizing the chemical compatibility between silica and the aluminum matrix. The silane coupling agent can improve the dispersibility of nanoparticles in molten aluminum and prevent agglomeration. At the same time, one end of the nanoparticles forms chemical bonds with silica through siloxy groups, dehydrating and condensing to graft onto the silica surface. The other end is compatible with the aluminum alloy interface through organic segments. This changes the physical-mechanical bond between nano-aluminum nitride and aluminum matrix into a chemical covalent bond, preventing interfacial separation under stress.

[0032] 3. During the hot-dip galvanizing process of stainless steel fibers, atomic diffusion occurs between the aluminum-silicon alloy layer and the aluminum alloy substrate at high temperatures. The aluminum atoms in the aluminum-silicon alloy and the aluminum atoms in the substrate interpenetrate, forming a metallurgical bonding layer without obvious gaps. Under stress, the load can be evenly transferred to the substrate through the aluminum-silicon alloy layer, avoiding local stress concentration, thereby enhancing the load-bearing capacity of the fiber skeleton. The silicon phase contained in the aluminum-silicon alloy layer has high hardness, which can enhance the wear resistance of the fiber surface and reduce the frictional loss between the fiber and the substrate when the sunroof guide rail slides. Furthermore, as an "intermediate transition layer", the aluminum-silicon alloy layer has an electrode potential close to that of the aluminum alloy substrate, which can eliminate the potential difference, block the formation of corrosion cells, and effectively prevent interface corrosion problems. Attached Figure Description

[0033] Figure 1 The diagram shown is a process flow chart of an embodiment;

[0034] Figure 2 The table shown is a performance test table of the guide rail based on 6061 aluminum alloy in the embodiment.

[0035] Figure 3 The table shown is a performance test chart of the guide rail based on 7075 aluminum alloy in the embodiment. Detailed Implementation

[0036] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions of the present invention will be clearly and completely described below in conjunction with the embodiments and the accompanying drawings. Example

[0037] Figure 1 The processing technology of aluminum-based multiphase composite toughness-reinforced guide rails for sunroofs in new energy vehicles includes the following steps:

[0038] S1, nano-aluminum nitride pretreatment;

[0039] After adding nano-aluminum nitride particles to an anhydrous ethanol solution, 0.5% (by weight of aluminum nitride) of polyethylene glycol 6000 was added, with a mass ratio of aluminum nitride to anhydrous ethanol of 1:20. The mixture was ultrasonically dispersed at 300W and 40kHz for 30 minutes. Then, 3% (by weight of aluminum nitride) of 1mol / L nitric acid was added to adjust the pH of the solution to 3-4 to activate the hydroxyl groups on the surface of the aluminum nitride. The nano-aluminum nitride particles had a particle size of 50-200nm and a purity of ≥99.5%.

[0040] During the pretreatment of nano-aluminum nitride, the nano-aluminum nitride particles are ultrasonically dispersed in anhydrous ethanol, changing from an aggregated state to uniformly dispersed single particles / small aggregates. Polyethylene glycol 6000 is dissolved in anhydrous ethanol to form a uniformly dispersed dispersant system, which is adsorbed on the surface of aluminum nitride particles to prevent agglomeration. After the addition of nitric acid, the hydroxyl groups (-OH) on the surface of aluminum nitride are activated through protonation, increasing the number of active sites on the particle surface.

[0041] S2, nano-aluminum nitride surface coating;

[0042] A mixture of tetraethyl orthosilicate and anhydrous ethanol is slowly added dropwise to the solution from step S1 at a rate of 1 mL / min. The mixture of tetraethyl orthosilicate and anhydrous ethanol accounts for 30%-60% of the mass of nano-aluminum nitride, and the mass ratio of tetraethyl orthosilicate to anhydrous ethanol is 1:3. Then, ammonia water is added dropwise to adjust the pH of the solution to 8-9, which triggers the hydrolysis and condensation of tetraethyl orthosilicate on the surface of nano-aluminum nitride to generate silicon dioxide.

[0043] After adjusting the pH of the solution to 8-9 with ammonia, tetraethyl orthosilicate undergoes a hydrolysis-condensation reaction: tetraethyl orthosilicate is gradually hydrolyzed to generate silanol (-Si-OH). The silanol molecules undergo condensation reactions with each other and with the hydroxyl groups on the surface of aluminum nitride to form Si-O-Si covalent bonds, generating a silicon dioxide (SiO2) coating layer precursor on the surface of aluminum nitride.

[0044] S3. Prepare a silica coating layer;

[0045] The solution in step S2 is heated to 50°C and stirred for 2 hours. The solution is then filtered to collect the particles, which are washed multiple times with anhydrous ethanol and dried. Subsequently, the particles are calcined at 300-350°C for 1 hour under nitrogen protection to form a 2-5 nm thick silica coating on the surface of the nano-aluminum nitride particles, thus producing nano-aluminum nitride@silica particles. In step S3, the anhydrous ethanol is completely removed through washing, drying, and calcination. Polyethylene glycol 6000, nitric acid, and ammonia are discharged with the washing waste liquid or volatilized during the drying process, and are ultimately completely removed without residue.

[0046] After calcination, the silica coating layer dehydrates and densifies, forming a stable silica shell layer with a thickness of 2-5 nm, eliminating internal pores in the coating layer and enhancing the bonding force between the silica shell layer and the aluminum nitride core.

[0047] S4, nano-aluminum nitride composite modification;

[0048] The nano-aluminum nitride@silica particles prepared in step S3 were added to anhydrous ethanol at a mass ratio of 1:20. After ultrasonic dispersion at 300W and 40kHz for 20 minutes, 10%-15% of KH-550 silane coupling agent (by mass) of the nano-aluminum nitride@silica particles was added. The mixture was heated to 60℃ and stirred for 1.5 hours. After filtration, washing, and drying, "aluminum nitride@silica-silane" composite modified aluminum nitride particles were obtained. In step S4, the anhydrous ethanol was completely evaporated and removed during the drying process, leaving no residue.

[0049] Nano-aluminum nitride@silica particles are ultrasonically dispersed in anhydrous ethanol to form a uniform dispersion. Then, the amino group (-NH2) of KH-550 silane coupling agent undergoes a dehydration condensation reaction with the hydroxyl group (-Si-OH) on the silica surface to form Si-O-Si covalent bonds. The silane coupling agent is grafted onto the particle surface, and after grafting, the particle surface changes from hydrophilic to hydrophobic, improving the compatibility with the aluminum alloy matrix.

[0050] Nano-aluminum nitride, as the core reinforcing phase, provides strength and wear resistance to the material by utilizing its high hardness, excellent thermal conductivity, and nano-size effect. The silica coating layer on the surface of nano-aluminum nitride blocks direct contact between aluminum nitride and molten aluminum, preventing the hydrolysis and oxidation of aluminum nitride at high temperatures. On the other hand, it improves the interfacial wettability between the reinforcing phase and the matrix by utilizing the chemical compatibility between silica and the aluminum matrix. The silane coupling agent can improve the dispersibility of nanoparticles in the molten aluminum and prevent agglomeration. At the same time, it forms chemical bonds with silica through siloxy groups on one end, dehydrates and condenses to graft onto the silica surface, and is compatible with the aluminum alloy interface through organic segments on the other end. This transforms the physical-mechanical bond between nano-aluminum nitride and the aluminum matrix into a chemical covalent bond, preventing interfacial separation under stress.

[0051] S5, smelting aluminum alloys;

[0052] Aluminum alloy is added to a vacuum melting furnace, evacuated to ≤10Pa, and then protected with argon gas. The temperature is raised to 720℃-760℃ to completely melt the aluminum alloy. Subsequently, the temperature is lowered to the semi-solid temperature range and held. The aluminum alloy accounts for 92%-94% of the total mass. Composite modified aluminum nitride particles are added in step S4, accounting for 2%-3% of the total mass. The particles are stirred at 300r / min for 30min to ensure uniform dispersion. The aluminum alloy is 6061 or 7075. When the aluminum alloy is 6061, the semi-solid holding temperature is 590℃-620℃. When the aluminum alloy is 7075, the semi-solid holding temperature is 620℃-640℃.

[0053] The aluminum alloy charge is heated to 720℃-760℃, changing from a solid to a liquid state. Gases and impurities (oxide scale, non-metallic inclusions) in the aluminum melt are separated by physical floating / sinking to obtain pure aluminum melt. Then, it is cooled to a semi-solid temperature range and held at that temperature. The aluminum melt changes from a fully liquid state to a semi-solid slurry (solid-liquid coexistence state) of "liquid metal + solid grains". Composite modified aluminum nitride particles are evenly distributed in the aluminum melt through mechanical stirring.

[0054] S6, stainless steel fiber addition and casting;

[0055] Stainless steel fibers are alkali-washed and acid-washed to remove the surface oxide layer. After being coated with an aluminum-silicon alloy layer, they are added to a vacuum melting furnace. The stainless steel fibers account for 3%-5% of the total mass. The stirring speed is adjusted to 200 r / min and stirred for 20 min. The composite modified aluminum nitride particles and stainless steel fibers are uniformly dispersed in the aluminum alloy melt to form a continuous and interwoven reinforcing phase network structure. After being stirred evenly, the mixture is poured into a mold to form a composite billet.

[0056] In the reinforcing phase network structure, stainless steel fibers form a continuous skeleton structure, serving as the "main reinforcing phase" to bear the main external force. This disperses local stress concentration and prevents local plastic deformation under stress. Meanwhile, nano-aluminum nitride@silica-silane particles are dispersed in the aluminum alloy matrix and fiber gaps. While refining the matrix grains, they also hinder dislocation movement through "dispersion strengthening," reducing fatigue crack initiation sites. The synergistic effect of these two factors alleviates the brittleness tendency of the aluminum alloy matrix at low temperatures, significantly improving the tensile strength and impact toughness of the material, thus making it suitable for use in guide rails for large skylights.

[0057] The aluminum-silicon alloy coating on the stainless steel fiber surface in step S6 includes the following:

[0058] Stainless steel fibers with the oxide layer removed are dispersed and immersed in molten aluminum-silicon alloy at 720℃-750℃ for 3-5 minutes, so that the fiber surface is uniformly coated with an aluminum-silicon alloy layer of 1-3 μm thickness. After removal, the fibers are rapidly cooled to room temperature, washed multiple times with deionized water, dried at 120℃ for 2 hours, and then annealed at 300℃ for 30 minutes under nitrogen protection. The stainless steel fibers are of type 304 or 316, with a diameter of 5-10 μm and a length of 50-80 μm.

[0059] After removing the oxide layer from the surface of the stainless steel fiber, it is dispersed and immersed in molten aluminum-silicon alloy at 720℃-750℃. The molten aluminum-silicon alloy wets the surface of the stainless steel fiber and forms a 1-3μm thick coating layer on the surface through physical adsorption and diffusion. After annealing, the grains of the aluminum-silicon alloy layer are refined, and the bonding force with the stainless steel fiber is improved.

[0060] During the hot-dip galvanizing process of stainless steel fibers, atomic diffusion occurs between the aluminum-silicon alloy layer and the aluminum alloy substrate at high temperatures. The aluminum atoms in the aluminum-silicon alloy and the aluminum atoms in the substrate interpenetrate, forming a metallurgical bonding layer without obvious gaps. Under stress, the load can be evenly transferred to the substrate through the aluminum-silicon alloy layer, avoiding local stress concentration and thus enhancing the load-bearing capacity of the fiber skeleton. The silicon phase contained in the aluminum-silicon alloy layer has high hardness, which can enhance the wear resistance of the fiber surface and reduce the frictional loss between the fiber and the substrate when the sunroof guide rail slides. Furthermore, as an "intermediate transition layer", the aluminum-silicon alloy layer has an electrode potential close to that of the aluminum alloy substrate, which can eliminate potential differences, block the formation of corrosion cells, and effectively prevent interface corrosion problems.

[0061] S7. Homogenization treatment;

[0062] The composite billet is placed in a heating furnace and held at 460℃-480℃ for 6-10 hours. It is then furnace cooled or air cooled to room temperature to eliminate component segregation and optimize the uniformity of the microstructure.

[0063] S8. Subsequent processing;

[0064] The preheated billet is hot-extruded into shape, and then subjected to solution treatment, graded aging heat treatment, precision machining and surface treatment to finally obtain the finished guide rail.

[0065] In steps S1 and S4, the ultrasonic dispersion power is 300W and the frequency is 40kHz.

[0066] The above embodiments are only used to illustrate the technical solutions of the present invention, and are not intended to limit it.

Claims

1. A processing technology for aluminum-based multiphase composite toughness-reinforced guide rails used in sunroofs of new energy vehicles, characterized in that, Includes the following steps: S1, nano-aluminum nitride pretreatment; After adding nano-aluminum nitride particles to anhydrous ethanol solution, polyethylene glycol 6000 of 0.5% by mass of aluminum nitride was added. The mass ratio of aluminum nitride to anhydrous ethanol was 1:

20. After ultrasonic dispersion for 30 min, 1 mol / L nitric acid of 3% by mass of aluminum nitride was added to adjust the pH of the solution to 3-4 in order to activate the hydroxyl groups on the surface of aluminum nitride. S2, nano-aluminum nitride surface coating; A mixture of tetraethyl orthosilicate and anhydrous ethanol is slowly added dropwise to the solution from step S1 at a rate of 1 mL / min. The mixture of tetraethyl orthosilicate and anhydrous ethanol accounts for 30%-60% of the mass of nano-aluminum nitride, and the mass ratio of tetraethyl orthosilicate to anhydrous ethanol is 1:

3. Then, ammonia water is added dropwise to adjust the pH of the solution to 8-9, which triggers the hydrolysis and condensation of tetraethyl orthosilicate on the surface of nano-aluminum nitride to generate silicon dioxide. S3. Prepare a silica coating layer; The solution from step S2 was heated to 50°C and stirred for 2 hours. The solution was then filtered to collect the particles. The particles were washed and dried multiple times with anhydrous ethanol. Subsequently, the particles were calcined at 300-350°C for 1 hour under nitrogen protection to form a 2-5 nm thick silica coating layer on the surface of the nano-aluminum nitride particles, thus producing nano-aluminum nitride@silica particles. S4, nano-aluminum nitride composite modification; The nano-aluminum nitride@silica particles prepared in step S3 were added to anhydrous ethanol at a mass ratio of 1:

20. After ultrasonic dispersion for 20 min, 10%-15% of KH-550 silane coupling agent (by mass of nano-aluminum nitride@silica) was added. The mixture was heated to 60℃ and stirred for 1.5 h. After filtration, washing and drying, "aluminum nitride@silica-silane" composite modified aluminum nitride particles were obtained. S5, smelting aluminum alloys; Aluminum alloy is added to a vacuum melting furnace, vacuumed to ≤10Pa and then purged with argon for protection. The temperature is raised to 720℃-760℃ to completely melt the aluminum alloy. Then the temperature is lowered to the semi-solid temperature range and held. The aluminum alloy accounts for 92%-94% of the total mass. Step S4 is added to prepare composite modified aluminum nitride particles, which account for 2%-3% of the total mass. The particles are stirred at 300r / min for 30min to ensure uniform dispersion. S6, stainless steel fiber addition and casting; Stainless steel fibers are alkali-washed and acid-washed to remove the surface oxide layer. After being coated with an aluminum-silicon alloy layer, they are added to a vacuum melting furnace. The stainless steel fibers account for 3%-5% of the total mass. The stirring speed is adjusted to 200 r / min and stirred for 20 min. The composite modified aluminum nitride particles and stainless steel fibers are uniformly dispersed in the aluminum alloy melt to form a continuous and interwoven reinforcing phase network structure. After being stirred evenly, the mixture is poured into a mold to form a composite billet. S7. Homogenization treatment; The composite billet is placed in a heating furnace and held at 460℃-480℃ for 6-10 hours. It is then furnace cooled or air cooled to room temperature to eliminate component segregation and optimize the uniformity of the microstructure. S8. Subsequent processing; The preheated billet is hot-extruded into shape, and then subjected to solution treatment, graded aging heat treatment, precision machining and surface treatment to finally obtain the finished guide rail.

2. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, The aluminum-silicon alloy coating on the stainless steel fiber surface in step S6 includes the following: Stainless steel fibers with the oxide layer removed are dispersed and immersed in molten aluminum-silicon alloy at 720℃-750℃ and held for 3-5 minutes to uniformly coat the fiber surface with an aluminum-silicon alloy layer of 1-3μm thickness. After removal, the fibers are rapidly cooled to room temperature, washed multiple times with deionized water, dried at 120℃ for 2 hours, and then annealed at 300℃ for 30 minutes under nitrogen protection.

3. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, The nano-aluminum nitride particles have a particle size of 50-200 nm and a purity of ≥99.5%.

4. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, The stainless steel fiber is of type 304 or 316, and the stainless steel fiber has a diameter of 5-10μm and a length of 50-80μm.

5. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, The aluminum alloy is of type 6061 or 7075. When the aluminum alloy is type 6061, its semi-solid insulation temperature is 590℃-620℃. When the aluminum alloy is type 7075, its semi-solid insulation temperature is 620℃-640℃.

6. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, In steps S1 and S4, the ultrasonic dispersion power is 300W and the frequency is 40kHz.

7. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, In step S3, anhydrous ethanol is completely removed through washing, drying, and calcination. Polyethylene glycol 6000, nitric acid, and ammonia are discharged with the washing waste liquid or evaporated during the drying process, and are ultimately completely removed without residue.

8. The processing technology of the aluminum-based multiphase composite toughness-reinforced guide rail for new energy vehicle sunroofs according to claim 1, characterized in that, In step S4, the anhydrous ethanol is completely evaporated and removed during the drying process, leaving no residue.

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