High-thermal-conductivity aluminum-based composite material having adjustable coefficient of thermal expansion and preparation method therefor

Abstract

The present invention relates to the field of composite materials. Disclosed are a high-thermal-conductivity aluminum-based composite material having an adjustable coefficient of thermal expansion and a preparation method therefor. The material comprises a negative thermal expansion reinforcement, a high-thermal-conductivity reinforcement and an aluminum matrix; the total volume content of the negative thermal expansion reinforcement and the high-thermal-conductivity reinforcement is 10-70 vol.%, the volume content of the negative thermal expansion reinforcement is 5-65 vol.%, the volume content of the high-thermal-conductivity reinforcement is 5-65 vol.%, and the balance is the aluminum matrix; the negative thermal expansion reinforcement is one or a combination of two or more of a ceramic material, an intermetallic compound, and an alloy each having a negative average coefficient of linear expansion or a negative coefficient of volume expansion at t°C, wherein -100°C<t<300°C; the high-thermal-conductivity reinforcement is one or a combination of two or more of inorganic non-metallic materials having a thermal conductivity higher than that of the aluminum matrix; and the aluminum matrix is one or a combination of two or more of an aluminum alloy or pure aluminum having a mass percentage of aluminum of 50% or more. The present invention uses solid-phase sintering technology, thereby accurately controlling the volume fraction.

Description

A high thermal conductivity aluminum-based composite material with adjustable coefficient of thermal expansion and its preparation method Technical Field

[0001] This invention relates to a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion and its preparation method, belonging to the field of composite material technology. Background Technology

[0002] With the advent of the 5G era and the continuous advancement of microelectronics technology, electronic devices are rapidly developing towards high integration, high power, and lightweight design, placing higher demands on the overall performance of electronic packaging materials. Research on materials that match the thermal expansion coefficient of semiconductor components and possess high thermal conductivity, low density, and good mechanical properties is becoming increasingly widespread.

[0003] Currently, fourth-generation electronic packaging materials such as Si / Al and SiC / Al aluminum-based composites possess low coefficients of thermal expansion, high thermal conductivity, low density, and good mechanical properties, leading to their wide application in electronic packaging, aerospace, and rail transportation. However, to match semiconductor materials such as Si and GaAs, the content of Si or SiC reinforcements in Si / Al and SiC / Al aluminum-based composites needs to be as high as 70 vol.% or more to meet the requirement of low coefficients of thermal expansion. However, the high ceramic content results in the composite material having almost no plasticity, leading to problems such as high brittleness, difficult processing, and weak weldability.

[0004] Compared to materials with low coefficients of thermal expansion such as Si or SiC, the discovery of negative thermal expansion materials provides a solution for controlling the coefficient of thermal expansion of composite materials from negative to positive over a wider temperature range. However, due to their extremely low intrinsic thermal conductivity, AM2O8 series negative thermal expansion materials can easily result in low overall thermal conductivity of composite materials when used alone.

[0005] To address the aforementioned issues, hybrid reinforcement is an effective solution for designing and preparing aluminum matrix composites with low coefficients of thermal expansion and high thermal conductivity. It can coordinate the properties of different reinforcements to obtain composites with excellent overall performance. Currently, the main problems in preparing aluminum matrix composites with hybrid reinforcements of negative thermal expansion and other reinforcements are as follows: 1) Most existing aluminum matrix composites with hybrid reinforcements of negative thermal expansion and other reinforcements are prepared using liquid-phase infiltration. This method is difficult to achieve the preparation of composites with low volume fraction (e.g., below 30-40 vol.%) of reinforcement and precise control of the volume fraction. For example, patent document CN114231783B successfully improved the strength of the composite material while maintaining low expansion characteristics by introducing high-strength ceramic particles and ZrW2O8 particles into the aluminum matrix. However, this patent indicates that the liquid-phase infiltration method for preparing hybrid reinforced composites is suitable for preparing composites with high volume fraction (above 60 vol.%) of reinforcement. Patent document CN110846597B discloses a silicon carbide nanowire hybrid reinforced zirconium tungstate / aluminum composite material and its preparation method. The method involves uniformly mixing zirconium tungstate particles and silicon carbide nanowires, and then preparing the composite material using a pressure infiltration method (liquid phase infiltration). This results in a minimum thermal expansion coefficient of 2 × 10⁻⁶ for the prepared silicon carbide nanowire hybrid reinforced zirconium tungstate / aluminum composite material. -6 K -1 Furthermore, compared to composites prepared from single zirconium tungstate, the mechanical properties are improved, solving the problem of poor mechanical properties in existing zirconium tungstate / aluminum composites. The volume fraction of the silicon carbide nanowire-reinforced zirconium tungstate reinforcement reaches 30-60%. As can be seen from these two patents, the volume fraction of the reinforcement in the liquid-phase infiltration process cannot be lower than 30%, and it cannot overcome the inherent process defects of liquid-phase infiltration, such as the difficulty in precisely controlling the volume fraction. In addition, both patents are hybrid reinforcement designs based on improving the strength of the composite material, not hybrid reinforcement designs based on the comprehensive thermophysical properties of the composite material. 2) Compared to liquid-phase infiltration or pressure infiltration, solid-phase sintering is more advantageous for controlling the low volume fraction and precision of the reinforcement in low-expansion aluminum-based composites. However, there are currently few research reports on solid-phase sintering processes for low-expansion aluminum-based composites, which cannot meet the technical requirements. Patent documents CN105886823A and CN115870504A both use spark plasma sintering to prepare zirconium tungstate / aluminum composites, but they only address the sintering of a single zirconium tungstate negative thermal expansion reinforcement and an aluminum matrix composite, and the volume fraction of the zirconium tungstate reinforcement is above 50 vol.%. There are no reports on solid-state sintering of aluminum matrix composites with low volume fraction and / or mixed reinforcement with negative thermal expansion reinforcement and other reinforcements.

[0006] Therefore, when preparing aluminum matrix composites with low coefficient of thermal expansion and high thermal conductivity using various reinforcements, how to accurately control the volume fraction of the reinforcement from low to high has become a technical problem that needs to be solved.

[0007] Summary of the Invention

[0008] This invention addresses the challenge of precisely controlling the volume fraction of aluminum matrix composites with adjustable thermal expansion coefficients and high thermal conductivity when preparing such composites using various reinforcing agents. It proposes a method for preparing a high thermal conductivity aluminum matrix composite with an adjustable thermal expansion coefficient.

[0009] This invention provides a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion, comprising: a negative thermal expansion reinforcement, a high thermal conductivity reinforcement, and an aluminum matrix. The total volume percentage of the negative thermal expansion reinforcement and the high thermal conductivity reinforcement is 10–70 vol.%, wherein the volume percentage of the negative thermal expansion reinforcement is 5–65 vol.%, the volume percentage of the high thermal conductivity reinforcement is 5–65 vol.%, and the remainder is the aluminum matrix.

[0010] Negative thermal expansion reinforcement is one or more of the following: ceramic materials, intermetallic compounds, and alloys with a negative average linear expansion coefficient or volumetric expansion coefficient at t℃ (-100℃ < t < 300℃); high thermal conductivity reinforcement is one or more of the following: inorganic non-metallic materials with thermal conductivity higher than that of the aluminum matrix; aluminum matrix is ​​one or more of the following: aluminum alloys or pure aluminum with an aluminum mass percentage of 50wt% or more, and the purity of the pure aluminum is 99.0wt% or more.

[0011] Optionally, the ceramic material is selected from at least one of the following chemical formulas: chemical formula aα₂O₈, where a represents one or more of the chemical elements Zr, Hf, Sn, Ti, Eu, Er, and Yb, and α represents one or more of the chemical elements W, Mo, and V; chemical formula bβ₂O₇, where b represents one or more of the chemical elements Zr, Th, and Ce, and β represents one or more of the chemical elements P, Mo, and V; chemical formula c₂γ₃O₇ 12 In the formula, c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, and Lu, and γ represents one or more of the chemical elements W and Mo; the chemical formula dδO5, where d represents one or more of the chemical elements Nb and Ta, and δ represents one or more of the chemical elements V and P; the chemical formula eε2P3O 12In the formula, e represents one or more of the chemical elements Na, K, Nb, Rb, and Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; the chemical formula f2ζ2O7, where f represents one or more of the chemical elements Cu, Mn, Fe, Co, Ni, Mg, and Zn, and ζ represents one or more of the chemical elements P and V; the chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; the chemical formula hθF6, where h represents one or more of the chemical elements Ca, Mn, Fe, Zn, Co, Ni, Mg, Yb, and Ti, and θ represents one or more of the chemical elements Zr, Hf, and Nb; the chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd. One or more; chemical formula jB(CN)4, where j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, where k represents one or more of the chemical elements Y, Fe, Ga, Sc, Ti, La, Sm, Ho, Lu, Er, Cs, Rb, Cd, Mn, Co, Ni, and Zn, and τ represents one or more of the chemical elements Fe, Co, Pt, Cd, Ni, Cu, and Zn; chemical formula Mn3lN, where l is one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partially replacing the Mn position in chemical formula Mn3lN with any one or two of the elements V, Cr, Fe, Co, Ni, Cu, and Zn;

[0012] Zn[Ag(CN)2]2、CaZr4P6O 24 , Si(NCN)2, ReO3, SiO2, Cu2O, Ag2O, ScF3;

[0013] Intermetallic compounds are selected from at least one of the following chemical formulas: Zr y Nb 1-y Fe2, Hf y Nb 1-y Fe2, Hf 1-y Ta y Fe2, Sc 1-y Ti y Fe2, CrTe y Se 1-y LaFe 13-x Si x LaFe 13-x Al x , Mn3Ge, Mn-Co-Ge series, Fe-Mn-Ga series, Ni-Mn-Ga series, RCo2, R2Fe 14 B, R2Fe 17 , RCo3, RFe 12 , R3Fe 29In the chemical formula, y is any value from 0 to 1, x is any value from 0 to 13, and R is one or more rare earth elements; and intermetallic compounds formed by partially replacing the Fe, Co, or Mn sites in the above chemical formula with any one or two elements selected from Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, and Ta.

[0014] The alloy is selected from at least one of the following combinations of elements: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb.

[0015] Optionally, the inorganic non-metallic material is selected from at least one of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond.

[0016] Optionally, the aluminum alloy is selected from at least one of Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, and Al-Mn alloy.

[0017] This invention also provides a method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion, comprising the following steps:

[0018] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0019] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0020] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm or apply pressure to perform solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0021] Optionally, in step S1, the negative expansion reinforcement powder is one or more of the following: ceramic powder, intermetallic compound powder, and alloy powder, with a negative average linear expansion coefficient or volume expansion coefficient at t℃ (-100℃ < t < 300℃), and the average particle size of the negative thermal expansion reinforcement powder is 0.1 to 500 μm.

[0022] The high thermal conductivity reinforcing powder is one or more of inorganic non-metallic powders with thermal conductivity higher than that of the aluminum matrix, and the average particle size of the high thermal conductivity reinforcing powder is 0.1 to 500 μm.

[0023] The aluminum matrix powder is one or more of aluminum alloy powder or pure aluminum powder with an aluminum mass percentage of 50 wt% or more, the purity of the pure aluminum is 99.0 wt% or more, and the average particle size of the aluminum matrix powder is 0.1 to 500 μm.

[0024] Optionally, in step S3, solid-state sintering is carried out in any one of the following devices: vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace, hot isostatic pressing furnace, or spark plasma sintering furnace.

[0025] Optionally, in vacuum sintering furnaces, atmosphere sintering furnaces, hot pressing furnaces, and hot isostatic pressing furnaces, the furnace environment is 1×10⁻⁶. -2 A vacuum environment of ~50 Pa or a gas pressure of 1 to 1×10 3 Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–300 mm. The pressure applied during the sintering process is 0–200 MPa, the temperature is 400–720 °C, and the holding time is 30–120 min.

[0026] Optionally, in the spark plasma sintering furnace, the furnace environment is 1×10 -4 A vacuum environment of ~100 Pa or an atmospheric pressure of 10 to 1×10 3 Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–150 mm. The pressure applied during the sintering process is 30–200 MPa, the temperature is 400–640 °C, and the holding time is 5–100 min.

[0027] Optionally, in the spark plasma sintering furnace, the pressure applied during sintering is 70–200 MPa, the temperature is 400–470 °C, and the holding time is 10–100 min.

[0028] Compared with the prior art, the advantages of the present invention are as follows:

[0029] 1. The advantage of this invention is that it uses both negative thermal expansion reinforcement and high thermal conductivity reinforcement to jointly reinforce aluminum matrix composites. Compared with composites prepared by a single negative thermal expansion reinforcement, the material of this invention maintains a low coefficient of thermal expansion while having high thermal conductivity, resulting in superior overall performance.

[0030] 2. Compared with a single high thermal conductivity or negative thermal expansion ceramic reinforcement for aluminum matrix, the present invention achieves a composite material with superior performance by leveraging the synergistic effect of two reinforcements with different properties, while maintaining a relatively low total reinforcement content, so as to fully utilize the high thermal conductivity and low density characteristics of the aluminum matrix.

[0031] 3. This invention employs solid-state sintering technology, which avoids interfacial reactions and obtains a relatively dense composite material by controlling the sintering process, and precisely controls the volume fraction.

[0032] 4. This invention provides a hybrid reinforced aluminum matrix composite material with high thermal conductivity and adjustable coefficient of thermal expansion and its preparation method. The method is simple, fast, highly operable, and easy to implement in engineering applications, solving the problem that existing electronic packaging materials are difficult to maintain low thermal expansion while also having high thermal conductivity. Attached Figure Description

[0033] To more clearly illustrate the technical solutions in the embodiments of the present invention, the accompanying drawings used in the description of the embodiments will be briefly introduced below. Obviously, the accompanying drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0034] Figure 1 is a microstructure diagram of the aluminum-based composite material in Example 4;

[0035] Figure 2 shows the thermal expansion curves of the Al-Si alloy and aluminum-based composite material in Example 4;

[0036] In the figure, 1 represents SiC, a high thermal conductivity reinforcement; 2 represents ZrW2O8, a negative thermal expansion reinforcement; and 3 represents the Al-Si alloy matrix. Detailed Implementation

[0037] To make the objectives, technical solutions, and beneficial effects of this invention clearer, the invention will be described in detail below with reference to specific embodiments. It should be understood that the embodiments described in this specification are merely illustrative and not intended to limit the scope of the invention.

[0038] This invention provides a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion. The material has a low coefficient of expansion and high thermal conductivity, comprising a negative thermal expansion reinforcement, a high thermal conductivity reinforcement, and an aluminum matrix. The total volume percentage of the negative thermal expansion reinforcement and the high thermal conductivity reinforcement is 10–70 vol.%, wherein the volume percentage of the negative thermal expansion reinforcement is 5–65 vol.%, the volume percentage of the high thermal conductivity reinforcement is 5–65 vol.%, and the balance is the aluminum matrix.

[0039] The negative thermal expansion reinforcement is one or more of the following: ceramic materials, intermetallic compounds, and alloys, where the average linear expansion coefficient or volumetric expansion coefficient is negative at t℃ (-100℃ < t < 300℃).

[0040] Specifically, the negative thermal expansion reinforcement is selected from: (1) ceramic materials: chemical formula aα2O8, where a represents one or more of the chemical elements Zr, Hf, Sn, Ti, Eu, Er, Yb, and α represents one or more of the chemical elements W, Mo, V; chemical formula bβ2O7, where b represents one or more of the chemical elements Zr, Th, Ce, and β represents one or more of the chemical elements P, Mo, V; chemical formula c2γ3O 12 In the formula, c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, and Lu, and γ represents one or more of the chemical elements W and Mo; the chemical formula dδO5, where d represents one or more of the chemical elements Nb and Ta, and δ represents one or more of the chemical elements V and P; the chemical formula eε2P3O 12 In the formula, e represents one or more of the chemical elements Na, K, Nb, Rb, and Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; the chemical formula f2ζ2O7, where f represents one or more of the chemical elements Cu, Mn, Fe, Co, Ni, Mg, and Zn, and ζ represents one or more of the chemical elements P and V; the chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; the chemical formula hθF6, where h represents one or more of the chemical elements Ca, Mn, Fe, Zn, Co, Ni, Mg, Yb, and Ti, and θ represents one or more of the chemical elements Zr, Hf, and Nb; the chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd. One or more; chemical formula jB(CN)4, where j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, where k represents one or more of the chemical elements Y, Fe, Ga, Sc, Ti, La, Sm, Ho, Lu, Er, Cs, Rb, Cd, Mn, Co, Ni, and Zn, and τ represents one or more of the chemical elements Fe, Co, Pt, Cd, Ni, Cu, and Zn; chemical formula Mn3lN, where l is one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partially replacing the Mn position in chemical formula Mn3lN with any one or two of the elements V, Cr, Fe, Co, Ni, Cu, and Zn;

[0041] Zn[Ag(CN)2]2、CaZr4P6O 24 , Si(NCN)2, ReO3, SiO2, Cu2O, Ag2O, ScF3, ZrW2O8, ZrMo2O8, ZrV2O8, Cu2P2O7, Cu2V2O7, etc.

[0042] (2) Intermetallic compounds are selected from: Zr y Nb 1-yFe2, Hf y Nb 1-y Fe2, Hf 1-y Ta y Fe2, Sc 1- y Ti y Fe2, CrTe y Se 1-y LaFe 13-x Si x LaFe 13-x Al x , Mn3Ge, Mn-Co-Ge series, Fe-Mn-Ga series, Ni-Mn-Ga series, RCo2, R2Fe 14 B, R2Fe 17 , RCo3, RFe 12 , R3Fe 29 In the chemical formula, y is any value from 0 to 1, x is any value from 0 to 13, and R is one or more rare earth elements, such as rare earth elements La, Ce, Dy, Ho, Yb, etc.; and intermetallic compounds formed by partially replacing the Fe, Co, or Mn sites in the above-mentioned intermetallic compounds with any one or two elements selected from Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, and Ta.

[0043] (3) The alloys are selected from: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb, etc.

[0044] The high thermal conductivity reinforcement is one or more of the inorganic non-metallic materials with thermal conductivity higher than that of the aluminum matrix, such as one or more of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond.

[0045] The aluminum matrix is ​​one or more of aluminum alloys or pure aluminum with an aluminum mass percentage of 50 wt% or more, such as Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, Al-Mn alloy, or pure aluminum, with the purity of pure aluminum being 99.0 wt% or more.

[0046] It should be noted that negative thermal expansion reinforced materials exhibit the property of "thermal contraction and cold expansion" within the operating temperature range of electronic components. Within this temperature range, both the average linear expansion coefficient and the volumetric expansion coefficient are negative. Negative thermal expansion materials are combined with other positive thermal expansion materials in aluminum matrix composites to prepare materials with controllable coefficients of thermal expansion, such as zero-expansion materials. High thermal conductivity reinforcements are materials with relatively high thermal conductivity. These high thermal conductivity reinforcements are combined with other materials with lower thermal conductivity in aluminum matrix composites to prepare materials with relatively high thermal conductivity. Furthermore, within the allowable volume content range of the aforementioned negative thermal expansion reinforcements and high thermal conductivity reinforcements, by adjusting their volume ratio, aluminum matrix composites with different coefficients of thermal expansion and thermal conductivity that meet the application requirements can be obtained. For example, a 10 vol% ZrW₂O₈ + 10 vol% SiC + 80 vol% Al-Si alloy matrix has a thermal conductivity of 147.1 W / mK and a coefficient of thermal expansion of 12.6 ppm / ℃; a 10 vol% ZrW₂O₈ + 40 vol% SiC + 50 vol% Al-Si alloy matrix has a thermal conductivity of 1... The thermal conductivity of the following alloy matrices is 31.1 W / mK and the coefficient of thermal expansion is 9.7 ppm / ℃: 40 vol% ZrW2O8 + 10 vol% SiC + 50 vol% Al-Si alloy matrix; the thermal conductivity of the following alloy matrices is 87.2 W / mK and the coefficient of thermal expansion is 7.6 ppm / ℃: 30 vol% ZrW2O8 + 20 vol% SiC + 50 vol% Al-Si alloy matrix; the thermal conductivity of the following alloy matrices is 68.7 W / mK and the coefficient of thermal expansion is 5.1 ppm / ℃: 31.1 W / mK and 9.7 ppm / ℃: ...

[0047] This invention also provides a method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion, comprising the following steps:

[0048] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0049] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0050] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm or apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0051] Specifically, in step S1, firstly, the total volume is calculated according to the dimensions of the aluminum matrix composite material to be prepared; then, the volumes of the negative expansion reinforcement, the high thermal conductivity reinforcement, and the aluminum matrix are calculated according to their volume fractions; finally, the weights of the respective materials are calculated based on the volumes and true densities of the negative expansion reinforcement, the high thermal conductivity reinforcement, and the aluminum matrix.

[0052] The negative thermal expansion reinforcing powder is one or more of the following: ceramic powder, intermetallic compound powder, and alloy powder, with a negative average linear expansion coefficient or volume expansion coefficient at t℃ (-100℃ < t < 300℃). The average particle size of the negative thermal expansion reinforcing powder is 0.1~500μm. Specifically, the negative thermal expansion reinforcing powder is selected from: (1) ceramic powder: chemical formula aα2O8, where a represents one or more of the chemical elements Zr, Hf, Sn, Ti, Eu, Er, Yb, and α represents one or more of the chemical elements W, Mo, V; chemical formula bβ2O7, where b represents one or more of the chemical elements Zr, Th, Ce, and β represents one or more of the chemical elements P, Mo, V; chemical formula c2γ3O 12 In the formula, c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, and Lu, and γ represents one or more of the chemical elements W and Mo; the chemical formula dδO5, where d represents one or more of the chemical elements Nb and Ta, and δ represents one or more of the chemical elements V and P; the chemical formula eε2P3O 12In the formula, e represents one or more of the chemical elements Na, K, Nb, Rb, and Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; the chemical formula f2ζ2O7, where f represents one or more of the chemical elements Cu, Mn, Fe, Co, Ni, Mg, and Zn, and ζ represents one or more of the chemical elements P and V; the chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; the chemical formula hθF6, where h represents one or more of the chemical elements Ca, Mn, Fe, Zn, Co, Ni, Mg, Yb, and Ti, and θ represents one or more of the chemical elements Zr, Hf, and Nb; the chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd; the chemical formula j B(CN)4, where j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, where k represents one or more of the chemical elements Y, Fe, Ga, Sc, Ti, La, Sm, Ho, Lu, Er, Cs, Rb, Cd, Mn, Co, Ni, and Zn, and τ represents one or more of the chemical elements Fe, Co, Pt, Cd, Ni, Cu, and Zn; chemical formula Mn3lN, where l is one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partial substitution of the Mn position in chemical formula Mn3lN by any one or two of the elements V, Cr, Fe, Co, Ni, Cu, and Zn; Zn[Ag(CN)2]2, CaZr4P6O 24 、Si(NCN)2, ReO3, SiO2, Cu2O, Ag2O, ScF3, ZrW2O8, ZrMo2O8, ZrV2O8, Cu2P2O7, Cu2V2O7, etc.; (2) Intermetallic compound powders are selected from: Zr y Nb 1-y Fe2, Hf y Nb 1-y Fe2, Hf 1-y Ta y Fe2, Sc 1-y Ti y Fe2, CrTe y Se 1-y LaFe 13-x Si x LaFe 13-x Al x , Mn3Ge, Mn-Co-Ge series, Fe-Mn-Ga series, Ni-Mn-Ga series, RCo2, R2Fe 14 B, R2Fe 17 , RCo3, RFe 12 , R3Fe 29In the chemical formula, y is any value from 0 to 1, x is any value from 0 to 13, and R is one or more rare earth elements, such as rare earth elements La, Ce, Dy, Ho, Yb, etc.; and intermetallic compounds formed by replacing the Fe site, Co site, or Mn site in the above intermetallic compounds with any one or two elements from Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, Ta; (3) Alloy powder is selected from: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb, etc.

[0053] The high thermal conductivity reinforcing powder is one or more of the inorganic non-metallic powders with thermal conductivity higher than that of the aluminum matrix, such as one or more of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond, with an average particle size of 0.1 to 500 μm.

[0054] The aluminum matrix powder is one or more of the following: aluminum alloy powder or pure aluminum powder with an aluminum mass percentage of 50 wt% or more, such as Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, Al-Mn alloy, or pure aluminum. The purity of the pure aluminum is 99.0 wt% or more, and the average particle size of the aluminum matrix powder is 0.1 to 500 μm.

[0055] Specifically, in step S3, the solid-state sintering is carried out in any one of the following equipment: vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace, hot isostatic pressing furnace, or spark plasma sintering furnace.

[0056] The furnace environment in vacuum sintering furnaces, atmosphere sintering furnaces, hot pressing furnaces, and hot isostatic pressing furnaces is 1×10⁻⁶. -2 A vacuum environment of ~50 Pa or a gas pressure of 1 to 1×10 3 Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–300 mm. The pressure applied during the sintering process is 0–200 MPa, the temperature is 400–720 °C, and the holding time is 30–120 min.

[0057] The furnace environment in the spark plasma sintering furnace is 1×10 -4 A vacuum environment of ~100 Pa or an atmospheric pressure of 10 to 1×10 3Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–150 mm. The pressure applied during the sintering process is 30–200 MPa, the temperature is 400–640 °C, and the holding time is 5–100 min; or the pressure is 70–200 MPa, the temperature is 400–470 °C, and the holding time is 10–100 min.

[0058] First, the hybrid reinforcement preparation method of the present invention can achieve flexible matching of the two thermophysical properties of aluminum matrix composites: thermal conductivity and coefficient of thermal expansion. Second, the solid-state sintering method of the present invention can prepare aluminum matrix composites with low volume fraction reinforcement and can control the accuracy of volume fraction.

[0059] Example 1

[0060] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC is 20 vol.%, of which the volume percentage of the negative thermal expansion reinforcement ZrW2O8 is 10 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 10 vol.%, and the balance is the Al-Si alloy matrix.

[0061] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0062] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0063] The volume of the prefabricated aluminum matrix composite material is 3.14 cm³. 3 Weigh out 1.60g of negative expansion reinforcement ZrW2O8 powder, 1.01g of high thermal conductivity reinforcement SiC powder, and 6.74g of aluminum matrix Al-Si alloy powder. The average particle size of ZrW2O8 powder is 0.1μm, the average particle size of SiC powder is 0.1μm, and the average particle size of Al-Si alloy powder is 0.1μm.

[0064] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0065] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0066] Solid-state sintering was carried out in a spark plasma furnace under a vacuum environment of 10 Pa. The sintering mold used was a cylindrical graphite mold with an inner diameter of 20 mm. The pressure applied during sintering was 30 MPa, the temperature was 500 °C, and the holding time was 10 min.

[0067] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0068] Example 2

[0069] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC is 50 vol.%, of which the volume percentage of the negative thermal expansion reinforcement ZrW2O8 is 10 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 40 vol.%, and the balance is the Al-Si alloy matrix.

[0070] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0071] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0072] The volume of the prefabricated aluminum matrix composite material is 678.58 cm³. 3 346.08 g of negative expansion reinforced ZrW2O8 powder, 871.30 g of high thermal conductivity reinforced SiC powder, and 909.30 g of Al-Si alloy powder were weighed. The average particle size of ZrW2O8 powder is 100 μm, the average particle size of SiC powder is 5 μm, and the average particle size of Al-Si alloy powder is 500 μm.

[0073] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0074] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0075] Solid-state sintering was carried out in a spark plasma furnace with an internal environment of 1×10⁻⁶. -1The vacuum environment was controlled at 80 MPa, and the sintering mold used was a cylindrical graphite mold with an inner diameter of 120 mm. The pressure applied during the sintering process was 80 MPa, the temperature was 550 °C, and the holding time was 100 min.

[0076] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0077] Example 3

[0078] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC is 50 vol.%, of which the volume percentage of the negative thermal expansion reinforcement ZrW2O8 is 40 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 10 vol.%, and the balance is the Al-Si alloy matrix.

[0079] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0080] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0081] The volume of the prefabricated aluminum matrix composite material is 201.06 cm³. 3 410.17 g of negative expansion reinforcement ZrW2O8 powder, 64.54 g of high thermal conductivity reinforcement SiC powder, and 269.42 g of Al-Si alloy powder were weighed. The average particle size of ZrW2O8 powder is 5 μm, the average particle size of SiC powder is 80 μm, and the average particle size of Al-Si alloy powder is 250 μm.

[0082] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0083] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0084] Solid-state sintering was carried out in a spark plasma furnace with an internal environment of 1×10⁻⁶. -1 The sintering environment was in a vacuum of 50 MPa. The sintering mold used was a cylindrical graphite mold that was axially compressible. The inner diameter of the sintering mold was 80 mm. The pressure applied during the sintering process was 50 MPa, the temperature was 550 °C, and the holding time was 40 min.

[0085] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0086] Example 4

[0087] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC is 50 vol.%, of which the volume percentage of the negative thermal expansion reinforcement ZrW2O8 is 30 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 20 vol.%, and the balance is the Al-Si alloy matrix.

[0088] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0089] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0090] The volume of the prefabricated aluminum matrix composite material is 0.39 cm³. 3 Weigh out 60g of negative expansion reinforcement ZrW2O8 powder, 0.25g of high thermal conductivity reinforcement SiC powder, and 0.52g of Al-Si alloy powder. The average particle size of ZrW2O8 powder is 70μm, the average particle size of SiC powder is 0.1μm, and the average particle size of Al-Si alloy powder is 500μm.

[0091] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0092] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0093] Solid-state sintering was carried out in a spark plasma furnace with an internal environment of 1×10⁻⁶. -4 The vacuum environment was controlled at 40 MPa, and the sintering mold used was a cylindrical graphite mold with an inner diameter of 10 mm. The pressure applied during sintering was 40 MPa, the temperature was 500 °C, and the holding time was 5 min.

[0094] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0095] Figure 1 shows the microstructure of the aluminum-based composite material in Example 4. Label 1 represents the high thermal conductivity reinforcement SiC, label 2 represents the negative thermal expansion reinforcement ZrW₂O₈, and label 3 represents the Al-Si alloy matrix. Figure 2 shows the thermal expansion curves of the Al-Si alloy and the aluminum-based composite material in Example 4. The measured thermal expansion coefficient of the Al-Si alloy was 21.0 ppm / ℃ within the temperature range of -100℃ to 50℃, while that of the aluminum-based composite material was 7.6 ppm / ℃. This indicates that the addition of the negative thermal expansion reinforcement ZrW₂O₈ to the Al-Si alloy reduced the thermal expansion coefficient of the composite material.

[0096] Example 5

[0097] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC is 60 vol.%, of which the volume percentage of the negative thermal expansion reinforcement ZrW2O8 is 30 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 30 vol.%, and the balance is the Al-Si alloy matrix.

[0098] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0099] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0100] The volume of the prefabricated aluminum matrix composite material is 25.13 cm³. 3 38.45 g of negative expansion reinforcement ZrW2O8 powder, 24.20 g of high thermal conductivity reinforcement SiC powder, and 26.94 g of Al-Si alloy powder were weighed. The average particle size of ZrW2O8 powder is 8 μm, the average particle size of SiC powder is 70 μm, and the average particle size of Al-Si alloy powder is 250 μm.

[0101] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0102] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0103] Solid-state sintering was carried out in a spark plasma furnace with an internal environment of 1×10⁻⁶. -3The vacuum environment was controlled by Pa, and the sintering mold used was a cylindrical graphite mold with an inner diameter of 40 mm. The pressure applied during the sintering process was 50 MPa, the temperature was 500 °C, and the holding time was 20 min.

[0104] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0105] Example 6

[0106] A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes a negative thermal expansion reinforcement Cu2P2O7, a high thermal conductivity reinforcement SiC, and an Al-Si alloy matrix. The total volume percentage of the negative thermal expansion reinforcement Cu2P2O7 and the high thermal conductivity reinforcement SiC is 50 vol.%, of which the volume percentage of the negative thermal expansion reinforcement Cu2P2O7 is 20 vol.%, the volume percentage of the high thermal conductivity reinforcement SiC is 30 vol.%, and the balance is the Al-Si alloy matrix.

[0107] A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion includes the following steps:

[0108] Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly.

[0109] The volume of the prefabricated aluminum matrix composite material is 392.70 cm³. 3 471.24 g of negative expansion reinforcement Cu2P2O7 powder, 252.11 g of high thermal conductivity reinforcement SiC powder, and 526.22 g of Al-Si alloy powder were weighed. The average particle size of Cu2P2O7 powder is 70 μm, the average particle size of SiC powder is 3 μm, and the average particle size of Al-Si alloy powder is 400 μm.

[0110] Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder;

[0111] Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm and apply pressure to carry out solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

[0112] Solid-state sintering was carried out in a spark plasma furnace with an internal environment of 1×10⁻⁶. -1 The vacuum environment was controlled by Pa, and the sintering mold used was a cylindrical graphite mold with an inner diameter of 100 mm. The pressure applied during the sintering process was 30 MPa, the temperature was 550 °C, and the holding time was 50 min.

[0113] The thermal conductivity of the prepared aluminum-based composite material was tested using a thermal conductivity meter, and the coefficient of thermal expansion of the prepared aluminum-based composite material was tested using a linear thermal dilatometer. The test results are shown in Table 1.

[0114] Table 1. Thermophysical properties of aluminum-based composite materials in Examples 1-6

[0115] As can be seen from Examples 1-6, by selecting negative expansion reinforcement, high thermal conductivity reinforcement, and aluminum matrix with different materials and volume ratios, aluminum-based composite materials with thermal conductivity of 54.2-147.1 W / mK and coefficient of thermal expansion of 5.1-12.6 ppm / ℃ can be obtained. This patent, through hybrid reinforcement design, achieves a low coefficient of thermal expansion while greatly improving the thermal conductivity of aluminum-based composite materials. Specifically, as in Example 4, a low coefficient of thermal expansion of 7.6 ppm / ℃ is maintained while achieving a high thermal conductivity of 87.2 W / mK.

[0116] The above description is merely a specific embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any person skilled in the art can easily conceive of various equivalent modifications or substitutions within the technical scope disclosed in this invention, and these modifications or substitutions should all be covered within the scope of protection of this invention. Therefore, the scope of protection of this invention should be determined by the scope defined in the claims.

Claims

1. A high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion, characterized in that, The material comprises a negative thermal expansion reinforcement, a high thermal conductivity reinforcement, and an aluminum matrix. The total volume percentage of the negative thermal expansion reinforcement and the high thermal conductivity reinforcement is 10-70 vol.%, of which the volume percentage of the negative thermal expansion reinforcement is 5-65 vol.%, the volume percentage of the high thermal conductivity reinforcement is 5-65 vol.%, and the balance is the aluminum matrix. The negative thermal expansion reinforcement is one or more of the following: ceramic materials, intermetallic compounds, and alloys with a negative average linear expansion coefficient or volumetric expansion coefficient at t℃ (-100℃ < t < 300℃); the high thermal conductivity reinforcement is one or more of the following: inorganic non-metallic materials with a thermal conductivity higher than that of the aluminum matrix; the aluminum matrix is ​​one or more of the following: aluminum alloys or pure aluminum with an aluminum mass percentage of 50wt% or more, and the purity of the pure aluminum is 99.0wt% or more.

2. The material according to claim 1, characterized in that, The ceramic material is selected from at least one of the following chemical formulas: aα₂O₈, where a represents one or more of the chemical elements Zr, Hf, Sn, Ti, Eu, Er, and Yb, and α represents one or more of the chemical elements W, Mo, and V; bβ₂O₇, where b represents one or more of the chemical elements Zr, Th, and Ce, and β represents one or more of the chemical elements P, Mo, and V; c₂γ₃O₇ 12 In the formula, c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, and Lu, and γ represents one or more of the chemical elements W and Mo; the chemical formula dδO5, where d represents one or more of the chemical elements Nb and Ta, and δ represents one or more of the chemical elements V and P; the chemical formula eε2P3O 12 In the formula, e represents one or more of the chemical elements Na, K, Nb, Rb, and Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; the chemical formula f2ζ2O7, where f represents one or more of the chemical elements Cu, Mn, Fe, Co, Ni, Mg, and Zn, and ζ represents one or more of the chemical elements P and V; the chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; the chemical formula hθF6, where h represents one or more of the chemical elements Ca, Mn, Fe, Zn, Co, Ni, Mg, Yb, and Ti, and θ represents one or more of the chemical elements Zr, Hf, and Nb; the chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd; the chemical formula j B(CN)4, where j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, where k represents one or more of the chemical elements Y, Fe, Ga, Sc, Ti, La, Sm, Ho, Lu, Er, Cs, Rb, Cd, Mn, Co, Ni, and Zn, and τ represents one or more of the chemical elements Fe, Co, Pt, Cd, Ni, Cu, and Zn; chemical formula Mn3lN, where l is one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partial substitution of the Mn position in chemical formula Mn3lN by any one or two of the elements V, Cr, Fe, Co, Ni, Cu, and Zn; Zn[Ag(CN)2]2, CaZr4P6O 24 , Si(NCN)2, ReO3, SiO2, Cu2O, Ag2O, ScF3; The intermetallic compound is selected from at least one of the following chemical formulas: Zr y Nb 1-y Fe2, Hf y Nb 1-y Fe2, Hf 1-y Ta y Fe2,Sc 1-y Ti y Fe2, CrTe y Se 1-y LaFe 13-x Si x LaFe 13-x Al x , Mn3Ge, Mn-Co-Ge series, Fe-Mn-Ga series, Ni-Mn-Ga series, RCo2, R2Fe 14 B, R2Fe 17 , RCo3, RFe 12 , R3Fe 29 In the chemical formula, y is any value from 0 to 1, x is any value from 0 to 13, and R is one or more rare earth elements; and intermetallic compounds formed by partially replacing the Fe, Co, or Mn sites in the above chemical formula with any one or two elements selected from Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, and Ta. The alloy is selected from at least one of the following element combinations: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb.

3. The material according to claim 1, characterized in that, The inorganic non-metallic material is selected from at least one of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond.

4. The material according to claim 1, characterized in that, The aluminum alloy is selected from at least one of Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, and Al-Mn alloy.

5. A method for preparing a high thermal conductivity aluminum-based composite material with an adjustable coefficient of thermal expansion, characterized in that, The method is used to prepare the material according to any one of claims 1 to 4, and the method includes the following steps: Step S1: Based on the volume fraction of the aluminum matrix composite material to be prepared, convert it to weight and weigh the negative expansion reinforcement powder, high thermal conductivity reinforcement powder and aluminum matrix powder accordingly. Step S2: Mix the three powders weighed in step S1 evenly to obtain composite powder; Step S3: Load the composite powder from step S2 into a sintering mold and move it into the furnace. Adjust the furnace environment, keep it warm or apply pressure to perform solid-phase sintering, cool it with the furnace, and take it out at room temperature to obtain the aluminum-based composite material.

6. The method according to claim 5, characterized in that, In step S1, the negative expansion reinforcing powder is one or more of ceramic powder, intermetallic compound powder, and alloy powder with a negative average linear expansion coefficient or volume expansion coefficient at t℃ (-100℃ < t < 300℃), and the average particle size of the negative thermal expansion reinforcing powder is 0.1 to 500 μm. The high thermal conductivity reinforcing powder is an inorganic non-metallic powder with a thermal conductivity higher than that of the aluminum matrix. The high thermal conductivity reinforcing powder has one or more of the following components, wherein the average particle size is 0.1–500 μm; The aluminum matrix powder is one or a combination of two or more of aluminum alloy powder or pure aluminum powder with an aluminum mass percentage of 50 wt% or more, the purity of the pure aluminum is 99.0 wt% or more, and the average particle size of the aluminum matrix powder is 0.1 to 500 μm.

7. The method according to claim 5, characterized in that, In step S3, the solid-state sintering is carried out in any one of the following equipment: vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace, hot isostatic pressing furnace, or spark plasma sintering furnace.

8. The method according to claim 7, characterized in that, In the aforementioned vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace, and hot isostatic pressing furnace, the furnace environment is 1×10⁻⁶. -2 A vacuum environment of ~50 Pa or a gas pressure of 1 to 1×10 3 Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–300 mm. The pressure applied during the sintering process is 0–200 MPa, the temperature is 400–720 °C, and the holding time is 30–120 min.

9. The method according to claim 7, characterized in that, In the aforementioned spark plasma sintering furnace, the furnace environment is 1×10⁻⁶. -4 A vacuum environment of ~100 Pa or an atmospheric pressure of 10 to 1×10 3 Pa is a protective gas among nitrogen, argon, and helium. The sintering mold used is a cylindrical graphite or steel mold that is axially compressible. The inner diameter of the sintering mold is 6–150 mm. The pressure applied during the sintering process is 30–200 MPa, the temperature is 400–640 °C, and the holding time is 5–100 min.

10. The method according to claim 9, characterized in that, The pressure applied during the sintering process is 70-200 MPa, the temperature is 400-470 °C, and the holding time is 10-100 min.

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