Impact-resistant aluminum alloy composite material and preparation method thereof

Abstract

The invention discloses an impact-resistant aluminum alloy composite material and a preparation method thereof, and relates to the technical field of metal-based composite materials. The aluminum alloy material comprises the following components in percentage by mass: 0.8%-1.5% of carbon nanotubes, 0.3%-0.7% of hexagonal boron nitride, 0.6%-1.0% of Mg, 0.9%-1.3% of Si, 0.1%-0.2% of Mn, 0.2%-0.6% of Cu, 0.1%-0.2% of Zr and the balance of Al. According to the preparation method, an optimized dry grinding method powder metallurgy process is adopted, the spherical aluminum powder is subjected to ball milling to form the lamellas, the carbon nanotubes are mechanically clamped between the lamellas, physical wrapping and mechanical locking can be achieved, and the dispersion effect and the firmness of interface bonding are improved. By introducing carbon nanotubes and hexagonal boron nitride with different dimensions, a multifunctional internal framework is constructed for an aluminum alloy matrix, so that the mechanical property and the conduction function of the aluminum alloy matrix are improved. High-energy ball milling and low-energy ball milling are carried out separately, the integrity of a reinforcement structure is kept, grain boundary dislocation can be effectively prevented, the force transmission and bearing sharing effects are achieved, and the heat conductivity is improved.

Description

Technical Field

[0001] This invention relates to the field of metal matrix composites, and more specifically, to an impact-resistant aluminum alloy composite material and its preparation method. Background Technology

[0002] With the rapid development of the automotive industry, lightweighting has become a key technological path to improve vehicle fuel economy, increase the driving range of new energy vehicles, and improve environmental performance. Aluminum alloys, due to their low density, excellent impact resistance, good corrosion resistance, and mature processing technology, occupy an important position in the automotive industry and are widely used in components such as the body-in-white, the three-electric system (motor, electronic control, and battery), and the chassis of new energy vehicles, gradually becoming the standard or preferred material for these structures. However, the relatively low elastic modulus of aluminum alloys (approximately 70 GPa) limits their application in critical load-bearing structural components of automobiles and restricts further lightweighting development. In particular, for 6-series aluminum alloys, which account for a large proportion of aluminum used in automobiles, it is essential to maintain excellent machinability while improving the modulus, and ensure that elongation does not decrease while tensile strength and yield strength are increased.

[0003] Furthermore, in the raw material preparation process, the uniform dispersion of the reinforcing phase and its interfacial bonding with the matrix are key challenges in improving material performance. Traditional reinforcing phases, such as brittle and hard nano-ceramic particles, while improving strength, are prone to causing stress concentration during processing, affecting the material's plasticity and overall processing performance, thus limiting the application of aluminum alloy composites in harsh conditions such as impact resistance. Therefore, developing a novel impact-resistant aluminum alloy composite material, by optimizing the selection, distribution, and interfacial design of the reinforcing phase, to improve its impact resistance, processing adaptability, and thermal conductivity while ensuring comprehensive performance of high modulus, high strength, and high elongation, has become an urgent need in the field of automotive lightweighting technology.

[0004] In view of this, the present invention is proposed. Summary of the Invention

[0005] The purpose of this invention is to provide an impact-resistant aluminum alloy composite material and its preparation method. An optimized dry grinding powder metallurgy process is employed to ball-mill spherical aluminum powder into layers, with carbon nanotubes (CNTs) mechanically sandwiched between these layers. This achieves both physical encapsulation and mechanical locking, improving dispersion and interfacial bonding strength. By introducing 1D carbon nanotubes and 2D hexagonal boron nitride (h-BN) of different dimensions, a multifunctional internal framework is constructed for the aluminum alloy matrix, thereby enhancing its mechanical properties and thermal conductivity.

[0006] This invention is implemented as follows: In a first aspect, the present invention provides an impact-resistant aluminum alloy composite material, which comprises the following components by mass percentage: 0.8%-1.5% carbon nanotubes, 0.3%-0.7% lamellar hexagonal boron nitride, 0.6%-1.0% Mg, 0.9%-1.3% Si, 0.1%-0.2% Mn, 0.2%-0.6% Cu, and 0.1%-0.2% Zr, with the balance being Al.

[0007] In some preferred embodiments, it comprises the following components by mass percentage: 1.0%-1.2% carbon nanotubes, 0.3%-0.5% lamellar hexagonal boron nitride, 0.8%-1.0% Mg, 0.9%-1.1% Si, 0.1%-0.15% Mn, 0.2%-0.4% Cu, and 0.1%-0.2% Zr, with the balance being Al.

[0008] Secondly, the present invention provides a method for preparing an impact-resistant aluminum alloy composite material, comprising the following steps: mixing aluminum powder and additives and performing a first ball milling to obtain a mixed lamellar powder; adding a predetermined proportion of carbon nanotubes, lamellar hexagonal boron nitride, Mg, Si, Mn, Cu and Zr to the mixed lamellar powder and mixing, and performing a second ball milling to obtain a mixed powder; performing a third ball milling of the mixed powder to obtain an aluminum alloy mixed powder, and then performing a degreasing treatment; pressing the degreased composite powder into a green blank, and then sequentially performing sintering, hot extrusion, solution treatment and aging treatment to obtain an aluminum alloy composite material.

[0009] In some preferred embodiments, the additive is stearic acid; the first ball milling is carried out under an argon atmosphere using a planetary ball mill with Ø15-20mm zirconia grinding balls, a ball-to-material ratio of (5-10):1, a rotation speed of 150-300 rpm, and a time of 2-5 hours.

[0010] In some preferred embodiments, the second ball milling is carried out under an argon atmosphere using a planetary ball mill with 3-8mm zirconia grinding balls, a ball-to-material ratio of (10-15):1, a rotation speed of 150-300 rpm, and a time of 1-6 hours.

[0011] In some preferred embodiments, the third ball milling is carried out under an argon atmosphere using a planetary ball mill with 3-8mm zirconia grinding balls, a ball-to-material ratio of (15-20):1, a rotation speed of 300-500 rpm, and a time of 1-2 hours.

[0012] In some preferred embodiments, the degreasing process involves holding the aluminum alloy mixed powder in a vacuum furnace at 350-400°C for 1-2 hours, maintaining a vacuum environment during the holding process, and continuously evacuating the vacuum until no volatile gases escape.

[0013] In some preferred embodiments, the green body is obtained by filling the mold cavity of a molding press with a degreased mixed powder and holding it under pressure of 500-700 MPa for 60-90 seconds.

[0014] In some preferred embodiments, the sintering is performed by sintering the green billet in a tube furnace under an argon atmosphere at a sintering temperature of 550-570°C for 1-2 hours; the hot extrusion is performed by extruding the sintered billet at 400-450°C at an extrusion ratio of (15-20):1.

[0015] In some preferred embodiments, the solution treatment is performed at a temperature of 520-540°C for 1-2 hours; the aging treatment is performed at a temperature of 170-180°C for 8-18 hours.

[0016] The present invention has the following beneficial effects: This invention employs powder metallurgy technology, employing a microstructure design of stacked micro- and nano-sheets to achieve a denser composite material. In this composite, carbon nanotubes (h-BN) and hexagonal boron nitride (CNTs) are interspersed on the aluminum crystal surfaces, acting not only as reinforcements to prevent dislocations but also creating a multi-dimensional synergistic effect. The h-BN sheets bear in-plane loads, while the CNTs can withstand axial loads and transfer loads from one h-BN sheet to another through their high aspect ratio, forming a multi-scale stress transfer system. Simultaneously, solid-state diffusion during extrusion promotes interfacial bonding, thereby enhancing the strength at the interface. The modulus, tensile strength, and yield strength of this composite are significantly improved, while maintaining high strength and toughness, resulting in a substantial improvement in the mechanical properties of the aluminum-based composite. Due to the thermal conductivity of CNTs, the material's heat dissipation effect is enhanced. The application of this high-performance composite material can further reduce the weight of components, achieving energy conservation and emission reduction, increasing vehicle range, while the heat dissipation effect prevents product failure under high loads. In addition, this composite material has good machinability and can be made into various forms such as plates, profiles, forgings and wire harnesses, forming a complete system integrating materials, processes and processing. Attached Figure Description

[0017] To more clearly illustrate the technical solutions of the embodiments of the present invention, the accompanying drawings used in the embodiments will be briefly introduced below. It should be understood that the following drawings only show some embodiments of the present invention and should not be regarded as a limitation on the scope. For those skilled in the art, other related drawings can be obtained based on these drawings without creative effort.

[0018] Figure 1 This is a 20µm metallographic image of the aluminum alloy composite material in the embodiments of this application; Figure 2This is a 10µm metallographic image of the aluminum alloy composite material in the embodiments of this application; Figure 3 This is a schematic diagram of the aluminum alloy door sill beam in an embodiment of this application. Detailed Implementation

[0019] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. Where specific conditions are not specified in the embodiments, conventional conditions or conditions recommended by the manufacturer shall apply. Reagents or instruments whose manufacturers are not specified are all conventional products that can be purchased commercially.

[0020] The following provides a detailed description of the impact-resistant aluminum alloy composite material and its preparation method proposed in this application.

[0021] In a first aspect, the present invention provides an impact-resistant aluminum alloy composite material, which comprises the following components by mass percentage: 0.8%-1.5% carbon nanotubes, 0.3%-0.7% lamellar hexagonal boron nitride, 0.6%-1.0% Mg, 0.9%-1.3% Si, 0.1%-0.2% Mn, 0.2%-0.6% Cu, and 0.1%-0.2% Zr, with the balance being Al.

[0022] Preferably, it comprises the following components by mass percentage: 1.0%-1.2% carbon nanotubes, 0.3%-0.5% lamellar hexagonal boron nitride, 0.8%-1.0% Mg, 0.9%-1.1% Si, 0.1%-0.15% Mn, 0.2%-0.4% Cu, and 0.1%-0.2% Zr, with the balance being Al.

[0023] This invention employs powder metallurgy technology, with a microstructure designed as a stacked micro-nano sheet configuration, which is more compact. In this composite material, CNTs and h-BN are interspersed on the aluminum crystal surface. In addition to acting as reinforcements to prevent dislocations, the multi-dimensional synergistic effect enables load transfer, and the solid diffusion during the extrusion process promotes interfacial bonding, enhancing the strength at the interface and improving the overall mechanical and thermal conductivity of the material.

[0024] Currently, to improve the modulus and toughness of aluminum alloys, reinforcing phases are added to enhance their load-bearing capacity. Commonly used reinforcing phases for aluminum alloys include ordinary aluminum alloy reinforcing phases (Mg2Si, MgZn2, Al2Cu, etc.) with moduli of 75–120 GPa, and ceramic reinforcing phases (SiC, Al2O3, B4C, etc.) with moduli of 360–450 GPa. However, if the grain size and microscopic defects of these brittle and hard phases are not properly controlled, their mechanical properties can be affected. Nanosheet hexagonal boron nitride (h-BN), with a structure similar to graphite, possesses excellent lubricity, high thermal conductivity, electrical insulation, chemical stability, and high-temperature stability. h-BN nanosheets can play a role in dispersion strengthening and grain refinement, improving the hardness, elastic modulus, and tensile strength of aluminum alloys. Its density is approximately 2.28 g / cm³. 3 The modulus is 800-1000 GPa; the theoretical modulus of carbon nanotubes is 1.34 TPa, and the theoretical elastic modulus of graphene is 1.0 TPa. The modulus of graphene-carbon materials is much higher than that of commonly used reinforcing phases, and they also have extremely strong flexibility.

[0025] Simultaneously employing nano-h-BN and CNTs as reinforcements, carbon nanotubes (CNTs) have a density of only 1.8 g / cm³, 10% lower than carbon fiber and 30% lighter than aluminum alloys. While improving modulus and tensile strength, they can also enhance toughness to a certain extent while maintaining good processing performance. Adding nano-h-BN reinforcement achieves multi-dimensional and multi-scale synergistic reinforcement. The h-BN sheets bear in-plane loads, while CNTs can bear axial loads and transfer loads from one h-BN sheet to another through their high aspect ratio, forming a multi-scale stress transfer system. h-BN is cheaper than CNTs, and both are used in smaller quantities as reinforcements. With the industrial upgrading of carbon nanotubes, reducing raw material usage and processing costs through lightweighting can further reduce production costs, making them an excellent choice for metal matrix reinforcements. This multi-dimensional synergistic effect has greater potential for the technological development of aluminum matrix composites.

[0026] Secondly, this invention proposes a method for preparing impact-resistant aluminum alloy composite materials, comprising the following steps: S1. Mix aluminum powder and additives and ball mill for the first time to obtain mixed lamellar powder.

[0027] In some preferred embodiments, the additive is stearic acid; the first ball milling is performed using a planetary ball mill with 15-20mm zirconia grinding balls, a ball-to-material ratio of (5-10):1, a rotation speed of 150-300 rpm, and a time of 2-5 hours. The first ball milling mainly aims to form the spherical Al powder into layers under the impact force provided by the larger grinding balls, providing a larger deposition space for CNTs and nano-h-BN, and resulting in more uniform dispersion and a layered composition. Furthermore, argon gas at 1 atm is used as a protective gas during the first ball milling process.

[0028] S2. Add carbon nanotubes, layered hexagonal boron nitride, Mg, Si, Mn, Cu and Zr in a set ratio to the mixed lamellar powder, mix, and then ball mill for a second time to obtain the mixed powder.

[0029] In some preferred embodiments, the second ball milling is carried out in a high-purity argon atmosphere using a planetary ball mill with Ø3-8mm zirconia grinding balls, a ball-to-material ratio of (10-15):1, a rotation speed of 150-300 rpm, and a time of 1-6 hours. The second ball milling uses smaller grinding balls, which, due to their large number, provide a large number of collision contact points. The CNTs and h-BN are dispersed mainly through shearing and friction, avoiding damage to the CNTs and aluminum sheets from high impact forces.

[0030] S3. The mixed powder is ball-milled for the third time to obtain aluminum alloy mixed powder, and then degreasing treatment is performed.

[0031] In some preferred embodiments, the third ball milling is carried out under a high-purity argon atmosphere using a planetary ball mill with Ø3-8mm zirconia grinding balls, a ball-to-material ratio of (15-20):1, a rotation speed of 300-500 rpm, and a time of 1-2 hours. This third ball milling employs a high-energy ball milling process, which not only further crushes and refines the aluminum powder, increasing its specific surface area, but also allows CNTs and h-BN to be more uniformly distributed in the aluminum matrix, thereby forming a denser and more uniform composite material precursor.

[0032] In some preferred embodiments, the degreasing process involves holding the aluminum alloy mixed powder at 350-400°C in a vacuum furnace for 1-2 hours, maintaining a vacuum environment during the holding process, and continuously evacuating the vacuum until no volatile gases escape, thereby removing oleic acid and water vapor.

[0033] S4. The degreased composite powder is pressed into a green blank, and then subjected to sintering, hot extrusion, solution treatment and aging treatment in sequence to obtain aluminum alloy composite material.

[0034] In some preferred embodiments, the green body is obtained by filling the mold cavity of a molding press with a degreased mixed powder and holding it under pressure of 500-700 MPa for 60-90 seconds.

[0035] In an optional embodiment, the sintering is performed by sintering the green billet in a tube furnace at a temperature of 550-570°C under a high-purity argon atmosphere for 1-2 hours; the hot extrusion is performed by extruding the sintered billet at 400-450°C at an extrusion ratio of (15-20):1.

[0036] In an optional embodiment, the above-mentioned molding material is solution treated in a furnace with a forced air circulation system and an integrated quenching tank at a temperature of 520-540°C for 1-2 hours, followed by rapid water quenching; then treated in an aging furnace at a temperature of 170-180°C for 8-18 hours to obtain an impact-resistant material with high modulus and good processing performance.

[0037] The inventors employed an optimized dry grinding powder metallurgy process to ball-mill a spherical matrix into lamellar layers. The lamellar powder has a larger specific surface area than spherical powder, providing more "landing points" for the adhesion of CNTs and nano-h-BN. The mechanical clamping of CNTs between the lamellar layers achieves physical encapsulation and mechanical locking, improving dispersion and interfacial bonding strength. Using 1D CNTs and 2D h-BN of different dimensions, a multifunctional internal framework is constructed for the aluminum alloy matrix, enhancing its mechanical properties and conductivity. To reduce damage to the reinforcement, high-energy ball milling (lamellar formation) and low-energy ball milling (powder mixing) are separated to maintain structural integrity. This allows the reinforcement to prevent grain boundary dislocations and facilitate the transfer of force and heat, effectively sharing load and dissipating heat.

[0038] The features and performance of the present invention will be further described in detail below with reference to embodiments.

[0039] Example 1 This embodiment provides an impact-resistant aluminum alloy composite material, which comprises the following components by mass percentage: CNT 1.2%, h-BN 0.6%, Mg 0.8%, Si 1.0%, Mn 0.2%, Cu 0.5%, and Zr 0.15%, with the balance being Al.

[0040] Its preparation method includes the following steps: S1. Prepare the raw material powders according to the mass ratio of various elements. CNT layer number ≤15, diameter 20~50nm, length 5~15µm, spherical aluminum powder 10~50µm.

[0041] S2. The prepared Al micro-nano raw material powder is mixed using a mixer. A planetary ball mill with medium to large zirconia grinding balls (Ф20mm), a ball-to-material ratio of 8:1, and a rotation speed of 150 rpm is used for 3 hours. The entire process is carried out with high-purity argon as the protective gas to obtain mixed sheet powder.

[0042] S3. Add the appropriate amounts of CNT, h-BN, Mg, Si, Mn, Cu, and Zr to the above powder, replace with small-sized grinding balls (Ф5mm), the ball-to-powder ratio is 15:1, the rotation speed is 200rpm, and the time is 3h. The entire process uses high-purity argon as the protective gas to obtain the mixed powder.

[0043] S4. The above mixed powder is subjected to high-energy ball milling with a ball-to-powder ratio of 15:1 to 20:1, a rotation speed of 300 to 500 rpm, and a time of 1.5 hours. The entire process is carried out with high-purity argon as the protective gas to obtain the mixed powder.

[0044] S5. Heat the ball-milled composite powder in a vacuum furnace to 400°C, keep it at that temperature for 1.5 hours, and continue to evacuate the vacuum until no gas is released, in order to remove impurities such as oleic acid and water vapor.

[0045] S6. The mixed powder is fed into the mold cavity of the molding press through the powder feeding mechanism and pressed to obtain a green body. The pressure is 600 MPa and the pressure is held for 60s to obtain the green body.

[0046] S7. The green billet is sintered in a tube furnace at a temperature of 560℃ for 1.5 hours in a high-purity argon atmosphere.

[0047] S8. Extrusion molding: The sintered billet is extruded at 430℃ with an extrusion ratio of 18:1.

[0048] S9. The above-mentioned molding material is solution treated in a furnace with a forced air circulation system and an integrated quenching tank at a temperature of 530°C for 1 hour, followed by rapid water quenching.

[0049] S10. The aluminum alloy composite material is processed in an aging furnace at 175℃ for 14 hours to obtain an impact-resistant aluminum alloy composite material. Figure 1 and Figure 2 As shown.

[0050] Experimental Example 1 The aluminum alloy composite material prepared in Example 1 was examined under a metallographic microscope, and the results are as follows: Figure 1 and Figure 2 As shown.

[0051] according to Figure 1 and Figure 2As shown, the composite matrix exhibits a uniform and dense stacked micro / nanosheet structure. Carbon nanotubes (CNTs) and hexagonal boron nitride (h-BN) reinforcements are highly uniformly dispersed within the aluminum matrix, without significant agglomeration. The reinforcing phase exhibits good interfacial bonding with the aluminum matrix, effectively interpenetrating between aluminum grain boundaries and crystal planes. This microstructure not only helps to hinder dislocation movement but also further promotes interfacial bonding strength through solid-state diffusion during subsequent extrusion. This uniform dispersion and strong interfacial bonding microstructure provides a direct structural basis for achieving a synergistic improvement in high modulus, high strength, thermal conductivity, and good toughness in the material.

[0052] The aluminum alloy composite material prepared in Example 1 and the 6-series aluminum alloy material 6351-T6 were used to prepare a door sill beam, such as... Figure 3 As shown in Table 1, the tensile strength, elongation at break, hardness, and elastic modulus were tested.

[0053] Table 1. Performance Test Results

[0054] As shown in Table 1, the performance test results of this invention, compared with the traditional 6351-T6 aluminum alloy, demonstrate a comprehensive superiority in key mechanical properties. Its tensile strength and specified plastic elongation strength reach 512 MPa and 415 MPa, respectively, significantly higher than the comparative materials' 322 MPa and 298 MPa. This directly reflects the effective load transfer and dislocation pinning effect of CNTs and h-BN as reinforcing phases. More importantly, while significantly improving strength, the material's elongation at break remains at a relatively high level of 12.5%, indicating that its good toughness is preserved, successfully overcoming the common strength-plasticity inversion contradiction in traditional particle-reinforced aluminum matrix composites. Furthermore, the material's hardness (HBW) and elastic modulus are also increased to 145 and 78.7 GPa, respectively, showing a significant increase compared to the comparative materials, resulting in a weight reduction of over 15%. This high modulus characteristic is crucial for the lightweight design and impact resistance of key load-bearing structural components in automobiles.

[0055] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. An impact-resistant aluminum alloy composite material, characterized in that, It comprises the following components by mass percentage: 0.8%-1.5% carbon nanotubes, 0.3%-0.7% lamellar hexagonal boron nitride, 0.6%-1.0% Mg, 0.9%-1.3% Si, 0.1%-0.2% Mn, 0.2%-0.6% Cu, and 0.1%-0.2% Zr, with the balance being Al.

2. The impact-resistant aluminum alloy composite material according to claim 1, characterized in that, It comprises the following components by mass percentage: 1.0%-1.2% carbon nanotubes, 0.3%-0.5% lamellar hexagonal boron nitride, 0.8%-1.0% Mg, 0.9%-1.1% Si, 0.1%-0.15% Mn, 0.2%-0.4% Cu, and 0.1%-0.2% Zr, with the balance being Al.

3. A method for preparing an impact-resistant aluminum alloy composite material as described in claim 1 or 2, characterized in that, Includes the following steps: Aluminum powder and additives are mixed and ball-milled for the first time to obtain a mixed lamellar powder. Carbon nanotubes, lamellar hexagonal boron nitride, Mg, Si, Mn, Cu and Zr are added to the mixed lamellar powder in a set proportion and mixed, and then ball-milled for the second time to obtain a mixed powder. The mixed powder is ball-milled for the third time to obtain an aluminum alloy mixed powder, and then degreased. The degreased composite powder is pressed into a green blank, and then sintered, hot-extruded, solution-treated and aged in sequence to obtain an aluminum alloy composite material.

4. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The additive is stearic acid; the first ball milling is carried out under an argon atmosphere using a planetary ball mill with Ø15-20mm zirconia grinding balls, a ball-to-material ratio of (5-10):1, a rotation speed of 150-300 rpm, and a time of 2-5 hours.

5. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The second ball milling was carried out under an argon atmosphere using a planetary ball mill with 3-8mm zirconia grinding balls, a ball-to-material ratio of (10-15):1, a rotation speed of 150-300 rpm, and a time of 1-6 hours.

6. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The third ball milling was carried out under an argon atmosphere using a planetary ball mill with 3-8mm zirconia grinding balls, a ball-to-material ratio of (15-20):1, a rotation speed of 300-500 rpm, and a time of 1-2 hours.

7. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The degreasing process involves placing the aluminum alloy mixed powder in a vacuum furnace at 350-400℃ for 1-2 hours, maintaining a vacuum environment during the heat preservation process, and continuously evacuating the vacuum until no volatile gases escape.

8. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The green body is obtained by filling the mold cavity of a molding press with degreased mixed powder and holding it under pressure of 500-700 MPa for 60-90 seconds.

9. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The sintering process involves sintering the green billet in a tube furnace under an argon atmosphere at a temperature of 550-570℃ for 1-2 hours. The hot extrusion process involves extruding the sintered billet at 400-450℃ with an extrusion ratio of (15-20):

1.

10. The method for preparing an impact-resistant aluminum alloy composite material according to claim 3, characterized in that, The solution treatment is performed at a temperature of 520-540℃ for 1-2 hours; the aging treatment is performed at a temperature of 170-180℃ for 8-18 hours.

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