An aluminum matrix composite and a method for producing the same

Abstract

The application provides an aluminum matrix composite material and a preparation method thereof, and the preparation method comprises the following steps: step 1: mixing pretreated B4C particle powder with an aluminum matrix to obtain A material; the chemical composition of the aluminum matrix is as follows in terms of mass percentage: Zn: 6-12 wt%, Mg: 1.5-2.5 wt%, Cu: 1-2.5 wt%, impurities not more than 0.5 wt%, and the balance being Al; the mass ratio of the B4C particle powder and the aluminum matrix is ensured to be 15-25 wt% of the reinforcing phase B4C and 75-85 wt% of the aluminum matrix in the aluminum matrix composite material prepared; step 2: performing hot-press sintering treatment on the A material in a vacuum environment to obtain an ingot; and step 3: performing homogenization, hot extrusion and heat treatment on the ingot to obtain the aluminum matrix composite material. The application effectively reduces the problem of element segregation; reduces the process cost, simplifies the process flow; and improves the strength of the aluminum matrix composite material on the basis of equivalent modulus and reasonable plasticity and toughness.

Description

TECHNICAL FIELD

[0001] The present application relates to the technical field of metal matrix composite material preparation and processing, in particular to an aluminum matrix composite material and a preparation method thereof. BACKGROUND

[0002] Particle reinforced aluminum matrix composites (PRAMC) are prepared by compositing ceramic particles such as SiC into an aluminum and alloy matrix, and have characteristics such as high specific strength, high specific stiffness, wear resistance, low expansion, etc., and are key materials in the fields of aerospace and transportation. However, the PRAMC widely used in the prior art is mostly based on Al-Mg-Si series (6xxxAl) and Al-Cu-Mg series (2xxxAl) alloys, and the strength of the PRAMC is only about 500 MPa due to the strength limitation of the aluminum matrix, and it is relatively difficult to meet the needs of equipment upgrading. As an improvement, Al-Zn-Mg-Cu series (7xxxAl) alloys have the highest strength in the aluminum alloy family. Some commercial brands, such as 7075Al and 7050Al, have a strength of up to 600 MPa. As an improvement, high-alloyed 7055Al and 7034Al prepared by spray deposition and other methods have a strength of more than 700 MPa (Research Progress of Spray Forming Ultra-high Strength Al-Zn-Mg-Cu Alloy, China Nonferrous Metals, Vol. 32, No. 5). Therefore, if the Al-Zn-Mg-Cu series alloy is used as the matrix, PRAMC with higher strength levels can be expected.

[0003] At present, the mainstream methods for preparing PRAMC include casting, liquid infiltration, powder metallurgy, etc. The first two methods belong to liquid methods, and the aluminum alloy matrix is in a molten state during the preparation process, which can easily cause the agglomeration of the reinforcing phase and serious reinforcing phase-matrix interface reaction, thereby affecting the performance of the PRAMC. In comparison, the powder metallurgy method is a method of mixing ceramic particles and metal powder uniformly, and then preparing a dense ingot under high temperature (generally between the solid and liquid phases of the aluminum matrix) and high pressure, which has the advantages of weak interface reaction and uniform dispersion of the reinforcing phase, and is an ideal method for preparing PRAMC with high strength, toughness and modulus.

[0004] However, there are still many difficulties in preparing Al-Zn-Mg-Cu PRAMC by powder metallurgy. On the one hand, although the interfacial reaction of PRAMC prepared by powder metallurgy is weaker than that prepared by casting and infiltration, there is still element segregation at the interface between the reinforcing phase and the aluminum matrix. For example, the surface of the most commonly used SiC particles in PRAMC is usually covered with a layer of SiO2 impurities. During the preparation of the composite, Mg elements in the aluminum matrix are prone to react with them, resulting in interfacial segregation of Mg. When using Al-Zn-Mg-Cu alloy as the matrix, this segregation is more likely to occur due to the high content of alloying elements. Al-Zn-Mg-Cu alloy and its composite mainly rely on the formation of nano precipitates by alloying elements to improve strength, and element interfacial segregation will lead to the formation of precipitates. The strength and plasticity are deteriorated. Some documents report that in SiC / 7085Al composite, due to the interfacial segregation of Mg element, its strength is even lower than that of 7085Al alloy, and its plasticity is less than 1 / 3 of 7085Al alloy (An investigation on particle weakening in T6-treated SiC / Al-Zn-Mg-Cu composites, Materials Characterization 158 (2019) 109966). On the other hand, in order to ensure full alloying during the powder metallurgy process, alloy powder is often used as raw material (as shown in Chinese patents CN02158747, 2002.12.2 and CN202011073867, 2020.10.09). That is, the aluminum alloy is first melted into an ingot, and then atomized into powder. In this way, the process flow is inevitably increased, and the cost is also increased. Although some commercial alloy powders, such as 7075Al, can be produced on a large scale to reduce costs, due to the existence of interfacial element segregation in PRAMC, the composition of commercial aluminum alloy cannot be directly used, and special composition design is required.

[0005] In summary, the existing powder metallurgy preparation of Al-Zn-Mg-Cu aluminum matrix composite at least has the following technical problems:

[0006] (1) Due to the existence of element segregation at the interface between the reinforcing phase and the aluminum matrix, the strength and plasticity of PRAMC are reduced, and the strength and plasticity are deteriorated.

[0007] (2) The process flow is relatively complex and the cost is relatively high, which is not suitable for industrial production. SUMMARY

[0008] Therefore, the present application provides an aluminum matrix composite material and a preparation method thereof, and the main purpose is to prepare an ultra-high-strength and high-modulus Al-Zn-Mg-Cu PRAMC by a powder metallurgy method, so as to solve the problem that the strength and plasticity of the PRAMC are reduced and the strength and plasticity are deteriorated due to the element segregation at the interface between the reinforcing phase and the aluminum matrix in the prior art.

[0009] To solve the above problems, the present application provides a preparation method of an aluminum matrix composite material, comprising the following steps:

[0010] Step 1): mixing the pretreated B4C particle powder and the aluminum matrix to obtain A material;

[0011] The chemical composition of the aluminum matrix is as follows in terms of mass percentage: Zn: 6-12wt%, Mg: 1.5-2.5wt%, Cu: 1-2.5wt%, impurities not more than 0.5wt%, and the balance being Al;

[0012] The mass ratio of the B4C particle powder and the aluminum matrix ensures that the mass fraction of the reinforcing phase B4C in the prepared aluminum matrix composite material is 15-25wt%, and the mass fraction of the aluminum matrix is 75-85wt%;

[0013] Step 2): performing hot-pressing sintering treatment on the A material in a vacuum environment to obtain an ingot;

[0014] Step 3): performing homogenization, hot extrusion and heat treatment on the ingot to obtain the aluminum matrix composite material.

[0015] The aforementioned preparation method of the aluminum matrix composite material, in step 1): the aluminum matrix is mixed by aluminum powder, zinc powder, magnesium powder and copper powder.

[0016] The aforementioned preparation method of the aluminum matrix composite material, in step 1):

[0017] The B4C particle powder is baked to obtain the pretreated B4C particle powder;

[0018] Preferably, the baking temperature is controlled to be 190-210℃, and the baking time is controlled to be 8-12 hours.

[0019] The aforementioned preparation method of the aluminum matrix composite material, in step 1):

[0020] The D 50 of the B4C particle powder is controlled to be 5-30μm;

[0021] The D 50 of the aluminum powder is controlled to be 8-40μm;

[0022] Preferably, the D 50The ratio of D of the B4C particle powder to D of the B4C particle powder is less than 5. 50 The ratio of D of the B4C particle powder to D of the B4C particle powder is less than 5.

[0023] The method for preparing the aluminum matrix composite material as claimed in the preceding claim, in step 2), the specific control parameters for homogenizing the billet are:

[0024] The hot-press sintering process comprises a first-stage hot-press sintering process and a second-stage hot-press sintering process performed in sequence;

[0025] The first-stage hot-press sintering process comprises:

[0026] The A material is pressed to 50% of the theoretical under-pressing amount at a temperature of 380-420℃ and is kept at the temperature to obtain the B material;

[0027] The second-stage hot-press sintering process comprises:

[0028] When the content of Zn in the aluminum matrix is 6wt%≤Zn≤8wt%, the B material is pressed to the final height at a temperature of 540-560℃ and is kept at the temperature.

[0029] When the content of Zn in the aluminum matrix is 8wt%<Zn≤12wt%, the B material is pressed to the final height at a temperature of 500-520℃ and is kept at the temperature.

[0030] The method for preparing the aluminum matrix composite material as claimed in the preceding claim, in step 3), the specific control parameters for homogenizing the billet are:

[0031] The temperature of the billet is controlled to be 400-470℃, and the billet is taken out after furnace cooling and is air-cooled.

[0032] The method for preparing the aluminum matrix composite material as claimed in the preceding claim, in step 3), the specific control parameters for hot-extruding the billet are:

[0033] The temperature of the billet is controlled to be 370-420℃, and the extrusion ratio is controlled to be not less than 9:1.

[0034] The method for preparing the aluminum matrix composite material as claimed in the preceding claim, in step 3),

[0035] When the content of Zn in the aluminum matrix is 6wt%≤Zn≤8wt%, the heat treatment comprises solid solution treatment and aging treatment in sequence; specifically:

[0036] The solid solution treatment comprises loading into the furnace at a temperature of 420-470℃, keeping at the temperature for 1-2 hours, and water quenching;

[0037] The aging treatment comprises loading into the furnace at a temperature of 100-120℃, keeping at the temperature for 8-48 hours, and air-cooling;

[0038] If the mass percentage is taken into account, when 8wt%<Zn≤12wt% in the aluminum matrix, the heat treatment is sequentially adopted by double-stage solid solution treatment and double-stage aging treatment; specifically:

[0039] Double-stage solid solution treatment: loading at a temperature of 420-450℃, holding for 1-2 hours; the temperature in the furnace is increased to 470-485℃ within 15 minutes, holding for 1-2 hours, and water quenching;

[0040] Double-stage aging treatment: loading at a temperature of 80-100℃, holding for 8-16 hours, increasing the temperature in the furnace to 120-160℃ within 15 minutes, holding for 8-12 hours, and furnace cooling.

[0041] The application further provides an aluminum matrix composite material, in which, in mass percentage: the mass fraction of the reinforcing phase B4C is 15-25wt%, and the mass fraction of the aluminum matrix is 75-85wt%.

[0042] The aluminum matrix comprises the following chemical components in mass percentage: Zn 6-12wt%, Mg 1.5-2.5wt%, Cu 1-2.5wt%, impurities not more than 0.5wt%, and the balance of Al.

[0043] Preferably, in the aluminum matrix composite material: the interface between the B4C particles and the aluminum matrix is clean; the B4C particles are uniformly distributed; the alloy elements in the aluminum matrix are uniformly distributed; the precipitated phase in the aluminum matrix is dispersedly distributed, and the diameter of the precipitated phase is less than 10nm.

[0044] Preferably, the yield strength of the aluminum matrix composite material is not less than 500MPa, the tensile strength is not less than 600MPa, the elastic modulus is not less than 95GPa, and the elongation is not less than 3%.

[0045] The aluminum matrix composite material is prepared by the preparation method of any one of the aluminum matrix composite materials.

[0046] The aforementioned aluminum matrix composite material, the chemical components of the impurities include one or more of Fe, Mn, Cr and Ti.

[0047] Compared with the prior art, the aluminum matrix composite material and the preparation method thereof provided by the application have at least the following beneficial effects.

[0048] In one aspect, the present application provides a method for preparing an aluminum matrix composite material, mainly comprising the following steps: mixing pre-processed B4C particle powder with an aluminum matrix to obtain A material (in mass percentage, the chemical composition of the aluminum matrix is: Zn 6-12wt%, Mg 1.5-2.5wt%, Cu 1-2.5wt%, impurities not more than 0.5wt%, and the balance is aluminum; the mass ratio of B4C particle powder to aluminum matrix is ensured to make the mass fraction of the reinforcing phase B4C in the prepared aluminum matrix composite material 15-25wt%, and the mass fraction of the aluminum matrix 75-85wt%); performing hot-pressing sintering treatment on the A material in a vacuum environment to obtain an ingot; performing homogenization, hot extrusion and heat treatment on the ingot to obtain the aluminum matrix composite material. It needs to be explained about the above steps that: on the one hand, the present application selects pre-processed B4C particle powder as the reinforcing phase, and since the surface oxygen content of the B4C particle powder is less, it is not easy to react with the Mg element in the aluminum matrix during the preparation process, so that the interface of Mg is not easy to segregate, thereby reducing the element segregation of PRAMC. On the other hand, the strength is improved by increasing the content of Zn element, and the plasticity and toughness of PRAMC are ensured within a reasonable range by strictly limiting the content of Mg element which is easy to cause brittle segregation and the content of Fe, Mn and Cr elements which are easy to form impurity phases. In summary, through the above raw material ratio design of the present application, the problem of deterioration of the strength and plasticity of PRAMC due to the element segregation at the interface between the reinforcing phase and the aluminum matrix in the prior art can be solved.

[0049] Further, the present application limits the D50 of the B4C particle powder and the Al powder to 10-30μm, so that the particle dispersion of B4C is more uniform. 50 , and further makes the particle dispersion of B4C more uniform.

[0050] Further, the present application selects the element powders of Al, Zn, Mg and Cu which are low in price as raw materials; the process of first smelting and then atomizing and powdering can be avoided, thereby reducing the cost and shortening the production process; in addition, using the element powders of Al, Zn, Mg and Cu as raw materials to prepare PRAMC can arbitrarily control the composition according to actual needs, thereby improving the flexibility of material design.

[0051] Further, since the aluminum matrix selects pure Al, pure Zn, pure Mg and pure Cu powders, it is difficult to fully realize alloying in the powder metallurgy process. To solve this problem, the present application designs a multi-stage press sintering process according to the composition characteristics of the Al-Zn-Mg-Cu matrix: first, the first press sintering is performed at low temperature (near the melting point of Zn element) to make the powders tightly combined and promote the alloying of Zn element; then, the second press sintering is performed at high temperature (near the melting point of the alloy system used) to obtain an ingot with uniform element distribution and density.

[0052] Further, the present application reduces or eliminates the intracrystalline segregation by limiting the data of specific temperature, time, taking-out temperature and extrusion ratio, and further improves the uniformity of the organization and composition by making the intracrystalline organization of the blank ingot more uniform through homogenizing and hot extruding the blank ingot in combination with the above-mentioned features of the aluminum-based composite material.

[0053] Further, when the Zn content is low, single-stage solid solution and aging treatment is adopted, the solid solution treatment makes the coarse second phase dissolve, and the aging treatment makes the nano precipitated phase form in the crystal, thereby improving the strength. When the Zn content is high, the low-melting-point MgZn2 second phase in the material also increases correspondingly, so as to avoid overburning caused by the melting of the MgZn2 phase due to single-stage solid solution. Therefore, two-stage solid solution treatment is adopted. When the Zn content is high, the tendency of Zn to segregate at the grain boundaries during the aging process will also increase. In order to reduce the grain boundary segregation of Zn, two-stage aging treatment is adopted, thereby promoting the nucleation of the Zn-rich precipitated phase in the crystal and making the precipitated phase grow. BRIEF DESCRIPTION OF DRAWINGS

[0054] In order to more clearly illustrate the embodiments of the present application or the technical solutions in the prior art, the drawings needed to be used in the following embodiment or prior art description will be briefly introduced. The drawings in the following description are only exemplary, and other drawings can be derived from the provided drawings without paying creative labor for those skilled in the art.

[0055] Figure 1 is a schematic diagram of the interface microstructure of the aluminum-based composite material in Example 1 of the aluminum-based composite material and the preparation method of the present application;

[0056] Figure 2 is a schematic diagram of the element distribution of the aluminum-based composite material in Example 1 of the aluminum-based composite material and the preparation method of the present application;

[0057] Figure 3 is a schematic diagram of the distribution of B4C of the aluminum-based composite material in Example 1 of the aluminum-based composite material and the preparation method of the present application;

[0058] Figure 4 is a schematic diagram of the distribution of the precipitated phase of the aluminum-based composite material in Example 1 of the aluminum-based composite material and the preparation method of the present application;

[0059] Figure 5 is a schematic diagram of the interface microstructure in Comparative Example 2 of the aluminum-based composite material and the preparation method of the present application. DETAILED DESCRIPTION

[0060] Clearly, the described embodiments are only a part of the embodiments of the present application, rather than all the embodiments. The description of the at least one example embodiment is actually only illustrative in nature, and by no means constitutes any limitation on the present application and its application or use. Based on the embodiments in the present application, all other embodiments obtained by those of ordinary skill in the art without creative labor fall within the scope of protection of the present application.

[0061] It is still extremely challenging to realize the low-cost powder metallurgy preparation of the super-high-strength and high-modulus Al-Zn-Mg-Cu series PRAMC, ensure alloying uniformity and clean interface, and further optimization is needed.

[0062] The present application provides an aluminum matrix composite material and a preparation method thereof, and the main inventive concept is as follows: in the aspect of the type of the reinforcing phase, in order to reduce the problem of Mg interface segregation caused by the existence of oxygen-containing substances on the surface of the ceramic particle reinforcing phase (SiC, Al2O3, etc.) commonly used in PRAMC, the present application limits the reinforcing phase to B4C particles with less surface oxygen content. In the aspect of composition design, the present application mainly improves the strength by increasing the content of Zn element, and ensures that the plasticity and toughness are within a reasonable range by strictly limiting the content of Mg element which is prone to cause brittle segregation and the content of Fe, Mn, Cr, Ti and other elements which are prone to produce impurity phases. In order to realize low cost, the present application uses elemental powders of Al, Zn, Mg and Cu as raw materials. The price of elemental powder is much lower than that of alloy powder, and the alloy composition can be flexibly adjusted according to the actual application requirements, but it is difficult to fully realize alloying in the powder metallurgy process. To solve this problem, the present application designs a multi-stage press sintering process according to the composition characteristics of the Al-Zn-Mg-Cu matrix: first, a first press sintering is carried out at a low temperature (near the melting point of Zn element) to make the powder tightly combined and promote the alloying of Zn element; then a second press sintering is carried out at a high temperature (near the melting point of the alloy system used) to obtain a compact billet with uniform element distribution. According to the aluminum matrix composite material prepared by the present application, the alloying elements are uniformly distributed, the interface between the reinforcing phase and the aluminum matrix is clean, the modulus is comparable to that of traditional Al-Mg-Si and Al-Cu-Mg series PRAMC, and the strength is significantly higher. Moreover, the method is simple and easy to implement, and is suitable for industrial production.

[0063] The main scheme of the present application is as follows

[0064] For reference Figures 1-4 According to the embodiments of the present application, a preparation method of an aluminum matrix composite material is provided, which comprises the following steps:

[0065] Step 1: mixing the pretreated B4C particle powder and the aluminum matrix to obtain A material;

[0066] wherein the chemical composition of the aluminum matrix is, in mass percentage: Zn: 6-12wt%, Mg: 1.5-2.5wt%, Cu: 1-2.5wt%, impurities no more than 0.5wt%, and the balance being aluminum;

[0067] The mass ratio of B4C particle powder to aluminum matrix ensures that the aluminum matrix composite prepared has B4C: 15-25wt%, and aluminum matrix: 75-85wt%.

[0068] Step 2: heat-press sintering treatment of A material in a vacuum environment to obtain an ingot;

[0069] Step 3: homogenization, hot extrusion, and heat treatment of the ingot to obtain an aluminum matrix composite.

[0070] Further, in step 1, the B4C powder is baked at a temperature of 190-210°C, and the baking time is selected as 8-12 hours as needed, and the crystal water on the surface of the particles is removed by baking to further reduce element interfacial segregation.

[0071] Further, the aluminum matrix is formed by mixing aluminum powder, zinc powder, magnesium powder, and copper powder.

[0072] Further, in step 2, the B4C particle powder and the aluminum matrix are mixed by mechanical mixing to improve the uniformity of the mixing; as an embodiment, the speed of the machine is controlled to be 50 rpm, and the time is 6 hours.

[0073] Further, in step 2, a multi-stage pressure sintering process is designed according to the composition characteristics of the aluminum matrix (Al-Zn-Mg-Cu); specifically:

[0074] When 6wt%≤Zn≤8wt%, first, a first pressure sintering is performed at a temperature of 380-420°C (near the melting point of the Zn element); the A material is pressed to 50% of the theoretical under-pressing amount (the difference between the original height of the A material and the final height after the heat-press sintering to form a dense ingot); thereby the gap between the powders can be reduced, and the diffusion of the Zn element can be promoted.

[0075] Then, the A material is kept at the temperature for a certain time, and the time is 1 hour per 1 kg of material.

[0076] Then, a second pressure sintering is performed on the A material at a temperature of 540-560°C (near the melting point of the aluminum matrix of the corresponding composition); the A material is pressed to the final height, and kept at the temperature for a certain time, and the time is also 1 hour per 1 kg of material; thereby the alloying of the Zn element is promoted.

[0077] When 8wt% < Zn < 12wt%, first pressurize to 50% of the theoretical under-pressing amount at 380-420 DEG C and perform heat preservation, the time is calculated according to 1 kg of material for 1 hour; considering that the increase of Zn content leads to the decrease of the melting point of the aluminum matrix, then press to the final height at 500-520 DEG C and perform heat preservation, the time is calculated according to 1 kg of material for 1 hour. The present application controls the different temperature parameters in the multi-stage press sintering process according to the different Zn content, thereby obtaining the compact billets with uniform element distribution, and improving the strength of the prepared aluminum matrix composite material.

[0078] Further, in step 3, the homogenization temperature of the billet is 400-470 DEG C, and after heat preservation, air cooling is taken. When the billet is hot extruded, the billet temperature is 370-420 DEG C, the temperature of the outlet is controlled to be 420-450 DEG C, and the extrusion ratio is not less than 9:1. In this way, the uniformity and compactness of the billet are improved.

[0079] The heat treatment in step 3 of the preparation method of the aluminum matrix composite material of the present application is specifically as follows:

[0080] When 6wt% < Zn < 8wt% in the aluminum matrix, the billet is subjected to solid solution treatment and aging treatment: the solid solution treatment is 420-470 DEG C, heat preservation for 1-2 hours, water quenching; the aging treatment is 100-120 DEG C, heat preservation for 8-48 hours, air cooling.

[0081] The solid solution treatment can make the coarse second phase dissolve, and the aging treatment can make the nano precipitated phase form in the crystal, thereby improving the strength of the billet.

[0082] When 8wt% < Zn < 12wt% (higher) in the aluminum matrix, the low melting point MgZn2 second phase in the material also increases correspondingly, in order to avoid overburning caused by the melting of MgZn2 phase due to single-stage solid solution, therefore, the present application adopts two-stage solid solution treatment: first, heat the furnace to 420-450 DEG C, heat preservation for 1-2 hours; increase the temperature to 470-485 DEG C in 15 minutes, heat preservation for 1-2 hours, water quenching.

[0083] When 8wt% < Zn < 12wt% (higher) in the aluminum matrix, the tendency of Zn to segregate at the grain boundary during the aging process will also increase. In order to reduce the grain boundary segregation of Zn, the present application adopts two-stage aging treatment: first, heat the furnace to 80-100 DEG C, heat preservation for 8-16 hours, thereby promoting the nucleation of Zn-rich precipitated phase in the crystal; then increase the temperature to 120-160 DEG C in 15 minutes, then heat preservation for 8-12 hours, furnace cooling, so that the precipitated phase grows.

[0084] In summary, the application improves the strength of the aluminum-based composite material by the above-mentioned heat treatment of the ingot according to the different content of Zn in the aluminum matrix, the prepared aluminum-based composite material has good interface bonding between the reinforcing phase and the aluminum matrix, no obvious element segregation, uniform composition distribution, good reinforcing phase dispersion, and fine intracrystalline precipitated phase with a size less than 10 nm.

[0085] The application further provides an aluminum-based composite material.

[0086] The B4C particle powder in the aluminum-based composite material is 15-25wt%, and the aluminum matrix is 75-85wt% in terms of mass percentage.

[0087] The chemical composition of the aluminum matrix is Zn: 6-12wt%, Mg: 1.5-2.5wt%, Cu: 1-2.5wt%, impurities less than 0.5wt%, and the balance is aluminum in terms of mass percentage.

[0088] Further, the mass percentage of a single impurity element in the application is less than 0.1%.

[0089] The application mainly improves the strength by increasing the content of Zn, and strictly controls the content of Mg element which is prone to interface segregation and brittleness and the content of Fe, Mn, Cr, Ti and other elements which are prone to produce impurity phases, so as to ensure that the plasticity and toughness of the prepared aluminum-based composite material are within a reasonable range.

[0090] The reinforcing phase used in the application is B4C ceramic particles, compared with SiC, Al2O3 and other ceramic particles, the surface oxygen content of B4C ceramic particles is less, which can to some extent reduce the problem of Mg interface segregation caused by the existence of oxygen-containing substances on the surface of the ceramic particle reinforcing phase (SiC, Al2O3, etc.) commonly used in PRAMC.

[0091] Further, in the aluminum-based composite material of the application, the B4C ceramic particles D 50 Optionally 5-30um; the aluminum powder D 50 Optionally 8-40um;

[0092] And / or, the aluminum powder D 50 The ratio of the B4C particle D 50 Is less than 5.

[0093] In this way, the B4C ceramic particles are uniformly dispersed.

[0094] The application uses Al, Zn, Mg and Cu element powder as raw materials. The price of the element powder is much lower than that of the existing alloy powder, thereby controlling the cost.

[0095] The aluminum-based composite material and the preparation method thereof of the application are further described in detail through specific examples and comparative examples.

[0096] Example 1

[0097] This example prepares an aluminum matrix composite material, which mainly comprises the following steps:

[0098] Step 1) 15wt% B4C particles are selected as the reinforcing phase and mixed with 85wt% aluminum matrix to obtain A material; wherein the aluminum matrix contains 8.5wt% Zn, 1.7wt% Mg, 1.7wt% Cu, and the rest is aluminum; the aluminum matrix is a powder formed by mixing the components (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0099] The D 50 of the B4C particles is 8 μm, and the D 50 of the aluminum is 13 μm.

[0100] The B4C particles are dried by keeping the temperature at 190℃ for 8 hours.

[0101] The dried B4C particles are mechanically mixed with the aluminum matrix, and the rotating speed is controlled at 50 rpm for 6 hours to obtain mixed powder B. The mixed powder B is packaged into a stainless steel mold and cold-pressed at room temperature with a pressure of 10 MPa to obtain a cold-pressed mold.

[0102] Step 2) The cold-pressed mold is placed in a vacuum hot pressing furnace with a vacuum degree of 10 -2 Pa order of magnitude. The temperature is kept at 400℃ for 50% of the theoretical reduction, and the temperature is kept for 1 kg of material for 1 hour. Then the temperature is raised to 520℃, and the final height is reduced, and the temperature is kept for 1 kg of material for 1 hour. After the billet is cooled to room temperature, it is taken out of the mold.

[0103] Step 3) The billet is subjected to homogenization treatment at a temperature of 450℃ for 24 hours, and then air-cooled and hot-extruded into a rod at a temperature of 420℃ with an extrusion ratio of 15:1.

[0104] Then, heat treatment is carried out:

[0105] Double-stage solid solution treatment: the furnace is loaded at a temperature of 450℃ and kept for 1 hour; the temperature in the furnace is raised to 475℃ within 15 minutes, kept for 1 hour, and water quenched;

[0106] Double-stage aging treatment: the furnace is loaded at a temperature of 100℃ and kept for 16 hours; the temperature in the furnace is raised to 120℃ within 15 minutes, kept for 8 hours, and furnace cooled. Thus, the aluminum matrix composite material of the present application is obtained.

[0107] The interface microstructure of the aluminum matrix composite material prepared in this example is shown in Figure 1 . The element distribution map of the aluminum matrix composite material is shown in Figure 2As shown. B4C particle distribution is as follows. Figure 3 As shown, the distribution of precipitated phases in the aluminum matrix is ​​as follows: Figure 4 As shown.

[0108] from Figure 1 As can be seen from the above, the aluminum-based composite material prepared in Example 1 of the present invention has good interfacial bonding between the reinforcing phase and the aluminum matrix.

[0109] from Figure 2 As can be seen from the above, the elemental composition of the aluminum-based composite material prepared in Example 1 of the present invention is relatively uniformly distributed.

[0110] from Figure 3 As can be seen from the above, in the aluminum-based composite material prepared in Example 1 of the present invention, the B4C particles are uniformly distributed in the aluminum matrix.

[0111] from Figure 4 As can be seen from the above, in the aluminum-based composite material prepared in Example 1 of the present invention, the precipitated phase is fine, dispersed, and its size does not exceed 10 nm.

[0112] The aluminum-based composite material obtained in Example 1 was subjected to performance testing, and the following data were obtained:

[0113] The modulus is 98 GPa, the yield strength is 560 MPa, the tensile strength is 630 MPa, and the elongation is 4%.

[0114] Example 2

[0115] This embodiment prepares an aluminum-based composite material, mainly including the following steps:

[0116] Step 1) By mass percentage, 15 wt% of B4C particles are selected as the reinforcing phase and mixed with 85 wt% of aluminum matrix to obtain material A; wherein, the aluminum matrix contains Zn: 11.5 wt%, Mg: 2.2 wt%, Cu: 1.0 wt%, and aluminum balance; the aluminum matrix is ​​a powder formed by mixing the various components (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0117] Among them, the D of B4C particles 50 The diameter of aluminum is 8 μm. 50 It is 13μm.

[0118] The B4C particles were dried by keeping them at 190°C for 8 hours.

[0119] The dried B4C particles were mechanically mixed with an aluminum matrix at a speed of 50 rpm for 6 hours to obtain mixed powder B. Mixed powder B was then encapsulated in a stainless steel mold and cold-pressed at room temperature under a pressure of 10 MPa to obtain the cold-pressed mold.

[0120] Step 2) Put the cold-pressed mold into a vacuum hot-pressing furnace with a vacuum degree of 10 -2 Pa. Keep the temperature at 400℃ and press to 50% of the theoretical pressing amount, and keep the temperature for 1 kg of material for 1 hour. Then, increase the temperature to 520℃, press to the final height, and keep the temperature for 1 kg of material for 1 hour. After the billet cools to room temperature, it is removed from the mold.

[0121] Step 3) Homogenize the billet at a temperature of 450℃ for 24 hours, and then air cool to room temperature. Hot extrude the billet into a rod at a temperature of 370℃ with an extrusion ratio of 15:1.

[0122] Then, perform heat treatment:

[0123] Two-stage solid solution treatment: load at a temperature of 450℃, keep the temperature for 1 hour; increase the temperature in the furnace to 475℃ within 15 minutes, keep the temperature for 1 hour, and water quench;

[0124] Two-stage aging treatment: load at a temperature of 100℃, keep the temperature for 16 hours, increase the temperature in the furnace to 140℃ within 15 minutes, keep the temperature for 5 hours, and furnace cool. Thus, an aluminum-based composite material of the present application is obtained.

[0125] Test the performance of the aluminum-based composite material obtained in Example 2, and obtain the following data:

[0126] The modulus of the composite material is 98 GPa, the yield strength is 680 MPa, the tensile strength is 740 MPa, and the elongation is 3%.

[0127] Example 3

[0128] This example prepares an aluminum-based composite material, which mainly includes the following steps:

[0129] Step 1) Mix 20wt% of B4C particles as a reinforcing phase with 80wt% of an aluminum matrix to obtain A material; wherein the aluminum matrix contains Zn: 6.5wt%, Mg: 1.8wt%, Cu: 1.7wt%, and the rest is aluminum; and the aluminum matrix is a powder formed by mixing various components (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0130] The D 50 of the B4C particles is 8μm, and the D 50 of the aluminum is 13μm.

[0131] Dry the B4C particles by keeping the temperature at 190℃ for 8 hours.

[0132] The dried B4C particles are mechanically mixed with the aluminum matrix, the rotating speed is controlled at 50 rpm, and the time is 6 hours to obtain mixed powder B. The mixed powder B is packaged into a stainless steel mold, cold pressed at room temperature with a pressure of 10 MPa to obtain a cold-pressed mold.

[0133] Step 2) The cold-pressed mold is placed in a vacuum hot pressing furnace, the vacuum degree is 10 -2 Pa order of magnitude. The temperature is kept at 400℃, and the theoretical amount of pressing is 50%, and the time is kept at 1 kg of material for 1 hour. Then the temperature is raised to 560℃, the final height is pressed, and the time is kept at 1 kg of material for 1 hour. After the billet is cooled to room temperature, it is taken out of the mold.

[0134] Step 3) Hot extrusion into a rod at a temperature of 420℃, and the extrusion ratio is 15:1.

[0135] Then heat treatment is carried out:

[0136] Solution treatment: loaded into the furnace at a temperature of 470℃, kept for 1 hour; water quenching;

[0137] Ageing treatment: loaded into the furnace at a temperature of 120℃, kept for 24 hours, and air cooled. Thus an aluminum matrix composite material of the present application is obtained.

[0138] The aluminum matrix composite material obtained in Example 3 is tested for performance, and the following data is obtained:

[0139] The modulus of the composite material is 102 GPa, the yield strength is 530 MPa, the tensile strength is 630 MPa, and the elongation is 5%.

[0140] Example 4

[0141] An aluminum matrix composite material is prepared in this example, which mainly includes the following steps:

[0142] Step 1) 15wt% B4C particles are selected as the reinforcing phase and mixed with 85wt% aluminum matrix to obtain A material; wherein the aluminum matrix contains Zn: 8.5wt%, Mg: 2.2wt%, Cu: 2.2wt%, and the rest is aluminum; the aluminum matrix is a powder formed by mixing various components (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0143] The D 50 of the B4C particles is 8μm, and the D 50 of the aluminum is 13μm.

[0144] The B4C particles are dried at a temperature of 190℃ for 8 hours.

[0145] The dried B4C particles are mechanically mixed with the aluminum matrix, the rotating speed is controlled at 50 rpm, and the time is 6 hours to obtain mixed powder B. The mixed powder B is packaged into a stainless steel mold, cold pressed at room temperature, and the pressure is 10 MPa to obtain a cold-pressed mold.

[0146] Step 2) The cold-pressed mold is placed in a vacuum hot pressing furnace, the vacuum degree is 10 -2 Pa order of magnitude. The temperature is kept at 400℃, and the theoretical amount of pressing is 50%, and the time is kept at 1 kg of material for 1 hour. Then the temperature is raised to 520℃, the final height is pressed, and the time is kept at 1 kg of material for 1 hour. After the billet is cooled to room temperature, it is taken out of the mold.

[0147] Step 3) The billet is homogenized at a temperature of 450℃ for 24 hours, and then hot extruded into a rod at a temperature of 420℃, and the extrusion ratio is 15:1.

[0148] Then heat treatment is carried out:

[0149] Two-stage solid solution treatment: furnace temperature is 450℃, and the temperature is kept for 1 hour; the temperature in the furnace is raised to 475℃ within 15 minutes, and the temperature is kept for 1 hour, and then water quenching;

[0150] Two-stage aging treatment: furnace temperature is 80℃, and the temperature is kept for 16 hours; the temperature in the furnace is raised to 120℃ within 15 minutes, and the temperature is kept for 8 hours, and then furnace cooling. Thus the aluminum matrix composite material of the application is obtained.

[0151] The aluminum matrix composite material obtained in Example 4 is tested for performance, and the following data is obtained:

[0152] The modulus of the composite material is 98 GPa, the yield strength is 610 MPa, the tensile strength is 730 MPa, and the elongation is 5%.

[0153] Comparative Example 1

[0154] Comparative Example 1 does not use the first stage of hot pressing sintering treatment compared with Example 1.

[0155] Step 1) 15wt% B4C particles are selected as the reinforcing phase and mixed with 85wt% aluminum matrix to obtain A material; wherein the aluminum matrix contains Zn: 8.5wt%, Mg: 1.7wt%, Cu: 1.7wt%, and the rest is aluminum; the aluminum matrix is a powder mixed with each component (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0156] The D 50 of the B4C particles is 8μm, and the D 50 of the aluminum is 13μm.

[0157] The B4C particles are dried by keeping at a temperature of 190℃ for 8 hours.

[0158] The dried B4C particles are mechanically mixed with the aluminum matrix at a rotation speed of 50 rpm for 6 hours to obtain mixed powder B. The mixed powder B is packaged into a stainless steel mold and cold-pressed at a pressure of 10 MPa at room temperature to obtain a cold-pressed mold.

[0159] Step 2) The cold-pressed mold is placed in a vacuum hot-pressing furnace at a vacuum degree of 10 -2 Pa order of magnitude. Directly pressed to the final height at a temperature of 520℃, and kept for 1 hour per 1 kg of material. After the billet is cooled to room temperature, it is taken out of the mold.

[0160] Step 3) The billet is homogenized at a temperature of 450℃ for 24 hours, and then air-cooled after being taken out. The billet is hot-extruded into a rod at a temperature of 420℃ with an extrusion ratio of 15:1.

[0161] Then, heat treatment is performed:

[0162] Double-stage solid solution treatment: loaded into the furnace at a temperature of 450℃ and kept for 1 hour; the temperature in the furnace is raised to 475℃ within 15 minutes and kept for 1 hour, and then water-quenched;

[0163] Double-stage aging treatment: loaded into the furnace at a temperature of 100℃ and kept for 16 hours; the temperature in the furnace is raised to 120℃ within 15 minutes and kept for 8 hours, and then furnace-cooled. Thus, the first comparative aluminum matrix composite material is obtained.

[0164] The first aluminum matrix composite material obtained in Comparative Example 1 is tested for performance, and the following data are obtained:

[0165] The modulus of the first aluminum matrix composite material is 98 GPa, the yield strength is 530 MPa, the tensile strength is 600 MPa, and the elongation is 3%.

[0166] Here, the modulus and strength of the first comparative aluminum matrix composite material prepared in Comparative Example 1 are good, but the effect is not as good as that of Example 1 because the multi-stage hot-pressing sintering scheme is not used.

[0167] Comparative Example 2;

[0168] In this comparative example, the B4C particles are replaced by SiC particles.

[0169] Step 1) 15wt% SiC particles are selected as the reinforcing phase and mixed with 85wt% aluminum matrix to obtain A material; wherein the aluminum matrix contains 8.5wt% Zn, 1.7wt% Mg, 1.7wt% Cu, and the rest is aluminum; the aluminum matrix is a powder formed by mixing various components (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0170] wherein the D50 of the SiC particles is 8 pm, the D50 of the aluminum is 13 pm. 50 50 wherein the D50 of the SiC particles is 8 pm, the D50 of the aluminum is 13 pm.

[0171] The SiC particles were dried by keeping them at a temperature of 190 °C for 8 hours.

[0172] The dried SiC particles were mechanically mixed with the aluminum matrix, the rotation speed was controlled at 50 rpm, and the time was 6 hours, to obtain a mixed powder B. The mixed powder B was packaged into a stainless steel mold, and cold-pressed at room temperature with a pressure of 10 MPa to obtain a cold-pressed mold.

[0173] Step 2) The cold-pressed mold was placed in a vacuum hot-pressing furnace, the vacuum degree was 10 -2 Pa order of magnitude. The temperature was kept at 400 °C for 1 hour to press to 50% of the theoretical pressing amount, and then the temperature was raised to 520 °C, and the final height was pressed, and the temperature was kept for 1 hour according to the time of 1 kg of material for 1 hour. After the billet was cooled to room temperature, it was taken out of the mold.

[0174] Step 3) The billet was homogenized at a temperature of 450 °C for 24 hours, and then air-cooled after being taken out, and then hot-extruded into a rod at a temperature of 420 °C, and the extrusion ratio was 15:1.

[0175] Then heat treatment was carried out:

[0176] Two-stage solid solution treatment: loaded into the furnace at a temperature of 450 °C, kept for 1 hour; the temperature in the furnace was raised to 475 °C within 15 minutes, kept for 1 hour, and water quenched;

[0177] Two-stage aging treatment: loaded into the furnace at a temperature of 100 °C, kept for 16 hours, the temperature in the furnace was raised to 120 °C within 15 minutes, kept for 8 hours, and furnace-cooled. Thus, the second comparative aluminum matrix composite material was obtained.

[0178] Figure 5 The microstructure of the interface of the second comparative aluminum matrix composite material obtained in Comparative Example 2 is shown. It can be seen that there is element segregation at the interface.

[0179] The second comparative aluminum matrix composite material obtained in Comparative Example 2 was tested for performance, and the following data were obtained:

[0180] The modulus of the second comparative aluminum matrix composite material was 98 GPa, the yield strength was 480 MPa, the tensile strength was 550 MPa, and the elongation was 4%.

[0181] ​By comparison, it can be obtained that the second comparative aluminum matrix composite of Comparative Example 2 has segregation at the interface between the SiC particles and the aluminum matrix, resulting in a decrease in the elements for forming precipitates, and thus the strength of the second comparative aluminum matrix composite of Comparative Example 2 is weaker than that of the aluminum matrix composite of Example 1 of the present application.

[0182] Comparative Example 3

[0183] In Comparative Example 3, the two-stage solid solution and two-stage aging process of the present application is not used when the content of Zn is greater than 8wt%.

[0184] Step 1) 15wt% of B4C particles are selected as the reinforcing phase and mixed with 85wt% of an aluminum matrix to obtain A material; wherein the aluminum matrix contains Zn: 8.5wt%, Mg: 2.2wt%, Cu: 2.2wt%, and the rest is aluminum; and the aluminum matrix is a powder formed by mixing each component (Zn powder, Mg powder, Cu powder, and aluminum powder).

[0185] The D 50 of the B4C particles is 8μm, and the D 50 of the aluminum is 13μm.

[0186] The B4C particles are dried by keeping the temperature at 190℃ for 8 hours.

[0187] The dried B4C particles are mechanically mixed with the aluminum matrix, and the rotating speed is controlled at 50rpm for 6 hours to obtain mixed powder B. The mixed powder B is packaged into a stainless steel mold and cold-pressed at room temperature with a pressure of 10MPa to obtain a cold-pressed mold.

[0188] Step 2) the cold-pressed mold is placed in a vacuum hot-pressing furnace with a vacuum degree of 10 -2 Pa order of magnitude. The temperature is kept at 400℃ to press to 50% of the theoretical pressing amount, and the temperature is kept for 1kg of material for 1 hour. Then the temperature is increased to 520℃, and the final height is pressed, and the temperature is kept for 1kg of material for 1 hour. After the billet is cooled to room temperature, it is taken out of the mold.

[0189] Step 3) the billet is subjected to homogenization treatment at a temperature of 450℃ for 24 hours, and then air-cooled. After that, the billet is hot-extruded into a rod at a temperature of 420℃ with an extrusion ratio of 15:1.

[0190] After that, heat treatment is performed:

[0191] The solution treatment is to load the furnace at a temperature of 470℃, keep the temperature for 2 hours, and then water quenching;

[0192] The aging treatment is loading into the furnace at a temperature of 120 DEG C, keeping for 24 hours, and furnace cooling. Thus the third aluminum matrix composite material of the present application is obtained. The third comparative aluminum matrix composite material obtained from Comparative Example 3 is tested for performance, and the following data are obtained:

[0193] The modulus of the third comparative aluminum matrix composite material is 98 GPa, the yield strength is 665 MPa, the tensile strength is 733 MPa, and the elongation is 2.3%.

[0194] By comparing the present Comparative Example 3 with Example 4, it can be seen that since the two-stage solid solution and two-stage aging process defined in the present application is not used when the Zn content is greater than 8 wt%, although the yield strength of the third comparative aluminum matrix composite material obtained is slightly improved, the elongation has deteriorated to some extent.

[0195] In summary, the present application is an aluminum matrix composite material and a preparation method thereof. The present application realizes full alloying of element powders by controlling different multi-stage hot pressing and sintering according to element content. Compared with conventional Al-Mg-Si and Al-Cu-Mg composite materials, the aluminum matrix composite material prepared by the method of the present application has a strength increase of more than 100 MPa under the condition of equivalent modulus, and the plasticity and toughness are still within a reasonable range. Moreover, the present application is based on the prior art, and the aluminum alloy matrix is prepared from element powders to reduce production cost.

[0196] The above description is only the preferred embodiments of the present application, and does not limit the present application in any form. Any simple modification, equivalent change and modification made to the above embodiments according to the technical essence of the present application are still within the scope of the technical solutions of the present application.

Claims

1. A method for preparing an aluminum-based composite material, characterized in that, It includes the following steps: Step 1): Mix the pretreated B4C granules with the aluminum matrix to obtain material A; The chemical composition of the aluminum matrix, by mass percentage, is as follows: Zn: 6~12wt%, Mg: 1.5~2.5wt%, Cu: 1~2.5wt%, impurities not exceeding 0.5wt%, and the balance being Al; The mass ratio of B4C powder particles to aluminum matrix ensures that the mass fraction of the reinforcing phase B4C in the prepared aluminum matrix composite material is 15-25 wt%, and the mass fraction of the aluminum matrix is ​​75-85 wt%. The aluminum matrix is ​​composed of a mixture of aluminum powder, zinc powder, magnesium powder, and copper powder. Step 2): Hot pressing and sintering of material A under vacuum to obtain a billet; Step 3): Homogenize the billet, hot extrude it, and heat treat it to obtain an aluminum-based composite material; In step 1), the B4C granules are baked to obtain pretreated B4C granules; the baking temperature is controlled at 190-210℃ and the baking time is controlled at 8-12 hours. In step 2), the hot pressing sintering process includes a first-stage hot pressing sintering process and a second-stage hot pressing sintering process performed sequentially. The first stage of hot pressing and sintering treatment includes: Material A is pressurized to 50% of its theoretical compressibility at a temperature of 380~420℃ and kept at that temperature to obtain material B; The second stage of hot pressing and sintering treatment includes: By mass percentage, when the aluminum matrix contains 6wt%≤Zn≤8wt%, material B is pressed to its final height at a temperature of 540~560℃ and kept at that temperature. By mass percentage, when 8wt% < Zn ≤ 12wt% in the aluminum matrix, material B is pressed to its final height at a temperature of 500~520℃ and kept warm.

2. The method for preparing an aluminum-based composite material according to claim 1, characterized in that, In step 1): The D of the B4C particle powder 50 The micrometer size should be controlled to be 5~30μm. And / or, the D of the aluminum powder 50 The size is controlled to be 8~40μm.

3. The method for preparing an aluminum-based composite material according to claim 2, characterized in that, The aluminum powder D 50 D with B4C particle powder 50 The ratio is less than 5.

4. The method for preparing an aluminum-based composite material according to claim 1, characterized in that, In step 3), the specific control parameters for homogenizing the billet are as follows: The temperature of the billet is controlled at 400~470℃. After holding at this temperature, it is taken out and air-cooled.

5. The method for preparing an aluminum-based composite material according to claim 1, characterized in that, In step 3), the specific control parameters for hot extrusion of the billet are as follows: The temperature of the billet is controlled at 370~420℃, and the extrusion ratio is controlled at no less than 9:

1.

6. The method for preparing an aluminum-based composite material according to claim 1, characterized in that, In step 3); If calculated by mass percentage, when the aluminum matrix contains 6wt%≤Zn≤8wt%, the heat treatment should sequentially employ solution treatment followed by aging treatment; specifically: Solution treatment: Load the furnace at 420~470℃, hold for 1~2 hours, then water quench; Aging treatment: Load the furnace at 100~120℃, hold for 8~48 hours, and then air cool; If calculated by mass percentage, when 8wt% < Zn ≤ 12wt% in the aluminum matrix, the heat treatment should sequentially employ a two-stage solution treatment followed by a two-stage aging treatment; specifically: Two-stage solution treatment: Load the furnace at 420~450℃ and hold for 1~2 hours; within 15 minutes, raise the furnace temperature to 470~485℃ and hold for 1~2 hours, then water quench. Two-stage aging treatment: Load the furnace at 80~100℃, hold for 8~16 hours, raise the furnace temperature to 120~160℃ within 15 minutes, hold for 8~12 hours, and then cool the furnace.

7. An aluminum-based composite material, characterized in that, In the aluminum matrix composite material, by mass percentage: the mass fraction of the reinforcing phase B4C is 15~25wt%, and the mass fraction of the aluminum matrix is ​​75~85wt%. The aluminum matrix comprises, by mass percentage, the following chemical composition: Zn 6~12wt%, Mg 1.5~2.5wt%, Cu 1~2.5wt%, impurities not exceeding 0.5wt%, and the balance being Al; The aluminum-based composite material is prepared by the method for preparing aluminum-based composite materials according to any one of claims 1-6.

8. The aluminum-based composite material according to claim 7, characterized in that, In the aluminum-based composite material: the interface between B4C particles and the aluminum matrix is ​​clean; the B4C particles are uniformly distributed; the alloying elements in the aluminum matrix are uniformly distributed; the precipitated phases in the aluminum matrix are dispersedly distributed, and the diameter of the precipitated phases is less than 10 nm.

9. The aluminum-based composite material according to claim 7, characterized in that, The yield strength of the aluminum-based composite material is not less than 500 MPa, the tensile strength is not less than 600 MPa, the elastic modulus is not less than 95 GPa, and the elongation is not less than 3%.

10. An aluminum-based composite material according to claim 7, characterized in that, The chemical composition of the impurities includes one or more of Fe, Mn, Cr, and Ti.

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