High-thermal-conductivity aluminum-based composite material with adjustable thermal expansion coefficient and preparation method of high-thermal-conductivity aluminum-based composite material

Abstract

The invention discloses a high-thermal-conductivity aluminum-based composite material with an adjustable thermal expansion coefficient and a preparation method, and belongs to the field of composite materials. The material comprises a negative thermal expansion reinforcing body, a high thermal conductivity reinforcing body and an aluminum matrix, the total volume content of the negative thermal expansion reinforcing body and the high thermal conductivity reinforcing body accounts for 10-70 vol.%, the volume content of the negative thermal expansion reinforcing body accounts for 5-65 vol.%, the volume content of the high thermal conductivity reinforcing body accounts for 5-65 vol.%, and the balance is the aluminum matrix. The negative thermal expansion reinforcer is one or a combination of more than two of a ceramic material, an intermetallic compound and an alloy, and the average linear expansion coefficient or the volume expansion coefficient of the ceramic material, the intermetallic compound and the alloy is negative when t DEG C is greater than-100 DEG C and less than 300 DEG C; the high-thermal-conductivity reinforcer is one or a combination of more than two of inorganic non-metallic materials with the thermal conductivity higher than that of the aluminum matrix; and the aluminum matrix is one or a combination of more than two of aluminum alloy or pure aluminum in which the mass percentage of aluminum is more than 50%. The solid-phase sintering technology is adopted, and the volume fraction is accurately controlled.

Description

Technical Field

[0001] The invention relates to a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient and a preparation method thereof, belonging to the technical field of composite materials. Background Art

[0002] With the advent of the 5G era, the continuous advancement of microelectronics technology, and the rapid development of electronic equipment towards high integration, high power and lightweight, higher requirements are placed on the overall performance of electronic packaging materials. Research on materials that match the thermal expansion coefficient of semiconductor components and have high thermal conductivity, low density and good mechanical properties is becoming more and more extensive.

[0003] At present, the fourth generation of electronic packaging materials such as Si / Al, SiC / Al and other aluminum-based composite materials have low thermal expansion coefficient, high thermal conductivity, low density and good mechanical properties, and are widely used in electronic packaging, aerospace and rail transportation. However, in order to match semiconductor materials such as Si and GaAs, the content of Si or SiC and other reinforcements in Si / Al, SiC / Al and other aluminum-based composite materials needs to be as high as 70vol.% or more to meet the requirements of low thermal expansion coefficient, but the high ceramic content makes the composite material almost non-plastic as a whole, and there are problems such as greater brittleness, difficult processing, and weak welding performance.

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

[0005] In view of the above problems, hybrid reinforcement is an effective solution for designing and preparing aluminum-based composite materials with low expansion coefficient and high thermal conductivity, which can coordinate the characteristics of different reinforcements to obtain composite materials with excellent comprehensive performance. At present, the main problems in the preparation of hybrid reinforced aluminum-based composite materials with negative thermal expansion reinforcements and other reinforcements are as follows: 1) Most of the existing hybrid reinforced aluminum-based composite materials with negative thermal expansion reinforcements and other reinforcements are prepared by liquid phase infiltration, which is difficult to achieve the preparation of low volume fraction (such as less than 30~40vol.%) reinforcement composite materials and precise control of volume fraction. For example, patent document CN114231783B successfully achieved the improvement of the strength of the composite material while ensuring low expansion characteristics by introducing high-strength ceramic particles and ZrW2O8 particles into the aluminum matrix. However, the patent shows that the preparation of hybrid reinforced composite materials by liquid phase infiltration is suitable for the preparation of high volume fraction (more than 60vol.%) reinforcement content. Patent document CN110846597B proposes a silicon carbide nanowire hybrid reinforced zirconium tungstate / aluminum composite material and a preparation method thereof, wherein zirconium tungstate particles and silicon carbide nanowires are mixed evenly, and then the composite material is prepared by pressure infiltration (liquid phase infiltration), so that the thermal expansion coefficient of the prepared silicon carbide nanowire hybrid reinforced zirconium tungstate / aluminum composite material can reach a minimum of 2×10 -6 K -1 , and the mechanical properties of the composite material prepared from single zirconium tungstate are improved, solving the problem of poor mechanical properties of existing zirconium tungstate / aluminum composite materials, in which the volume fraction of silicon carbide nanowire hybrid reinforced zirconium tungstate reinforcement reaches 30-60%. It can be seen from the above two patents that the volume fraction of the reinforcement in the liquid phase infiltration process cannot be lower than 30%, and it is impossible to get rid of the inherent process defects of liquid phase infiltration, such as the difficulty in accurately controlling the volume fraction. In addition, both patents are hybrid reinforcement designs based on improving the strength of composite materials, not hybrid reinforcement designs based on the comprehensive thermal physical properties of composite materials. 2) Compared with liquid phase infiltration or pressure infiltration, the use of solid phase sintering for low expansion aluminum-based composite materials is more conducive to controlling the low volume fraction and accuracy of the reinforcement, but there are currently few reports on the solid phase sintering process of low expansion aluminum-based composite materials, which cannot meet the technical needs. For example, patent documents CN105886823A and CN115870504A both use spark plasma sintering to prepare zirconium tungstate / aluminum composite materials, but only focus on the sintering of a single zirconium tungstate negative thermal expansion reinforcement and an aluminum-based composite material, and the volume fraction of the zirconium tungstate reinforcement is above 50 vol.%, and there is no report on the solid phase sintering of aluminum-based composite materials with low volume fraction and / or negative thermal expansion reinforcements and other reinforcements.

[0006] Therefore, when using a variety of reinforcements to prepare aluminum-based composite materials with low expansion coefficient and high thermal conductivity, how to achieve precise control of the reinforcement volume fraction from low to high becomes a technical problem that needs to be solved. Summary of the invention

[0007] The present invention aims at how to achieve precise control of the volume fraction of reinforcements from low to high when preparing aluminum-based composite materials with low expansion coefficient and high thermal conductivity using multiple reinforcements, and proposes a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient and a preparation method.

[0008] The present invention provides a high thermal conductivity aluminum-based composite material with an adjustable thermal expansion coefficient, comprising: a negative thermal expansion reinforcement, a high thermal conductivity reinforcement and an aluminum matrix, wherein the total volume content of the negative thermal expansion reinforcement and the high thermal conductivity reinforcement is 10-70 vol.%, wherein the volume content of the negative 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;

[0009] The negative thermal expansion reinforcement is one or a combination of two or more ceramic materials, intermetallic compounds, and alloys whose average linear expansion coefficient or volume expansion coefficient is negative when t°C, -100°C<t<300°C; the high thermal conductivity reinforcement is one or a combination of two or more inorganic non-metallic materials whose thermal conductivity is higher than that of the aluminum matrix; the aluminum matrix is ​​one or a combination of two or more aluminum alloys or pure aluminum with an aluminum mass percentage of more than 50wt%, and the purity of pure aluminum is more than 99.0wt%.

[0010] Optionally, the ceramic material is selected from at least one of the following chemical formulas: chemical formula aα2O8, wherein 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, wherein 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 c2γ3O 12 , where c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, Lu, and γ represents one or more of the chemical elements W and Mo; 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; chemical formula eε2P3O 12, where e represents one or more of the chemical elements Na, K, Nb, Rb, Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; 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; chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; 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; chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd; chemical formula j B(CN)4, wherein j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, wherein 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, wherein l represents one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partial replacement of Mn in the 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;

[0011] 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 an intermetallic compound formed by partial substitution of the Fe position, Co position or Mn position in the above chemical formula by 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;

[0012] The alloy is selected from at least one of the following element combinations: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb.

[0013] Optionally, the inorganic non-metallic material is selected from at least one of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond.

[0014] 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.

[0015] The present invention also provides a method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient, comprising the following steps:

[0016] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0017] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0018] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, keeping the temperature or keeping the temperature under pressure for solid phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material.

[0019] Optionally, in step S1, the negative expansion reinforcement powder is one or a combination of two or more of a ceramic powder, an intermetallic compound powder, and an alloy powder, whose average linear expansion coefficient or volume expansion coefficient is negative at t°C, -100°C < t < 300°C, and the average particle size of the negative thermal expansion reinforcement powder is 0.1-500 μm;

[0020] The high thermal conductivity reinforcement powder is one or a combination of two or more inorganic non-metallic powders having a thermal conductivity higher than that of the aluminum matrix, and the average particle size of the high thermal conductivity reinforcement powder is 0.1-500 μm;

[0021] 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 more than 50wt%, the purity of pure aluminum is more than 99.0wt%, and the average particle size of the aluminum matrix powder is 0.1~500μm.

[0022] Optionally, in step S3, solid phase sintering is performed in any one of a vacuum sintering furnace, an atmosphere sintering furnace, a hot pressing sintering furnace, a hot isostatic pressing furnace or a spark plasma sintering furnace.

[0023] Optionally, in a vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace, or hot isostatic pressing furnace, the furnace environment is 1×10 -2 ~50Pa vacuum environment or air pressure of 1~1×10 3 A protective gas among nitrogen, argon and helium of Pa. The sintering mold used is a cylindrical graphite or steel mold, which is axially compressible. The inner diameter of the sintering mold is 6-300mm. The pressure applied during the sintering process is 0-200MPa, the temperature is 400-720℃, and the insulation time is 30-120min.

[0024] Optionally, in a spark plasma sintering furnace, the furnace environment is 1×10 -4 ~100Pa vacuum environment or air pressure of 10~1×10 3 A protective gas among nitrogen, argon and helium of Pa. The sintering mold used is a cylindrical graphite or steel mold, which is axially compressible. The inner diameter of the sintering mold is 6-150mm. The pressure applied during the sintering process is 30-200MPa, the temperature is 400-640℃, and the insulation time is 5-100min.

[0025] Optionally, in a spark plasma sintering furnace, a pressure of 70-200 MPa, a temperature of 400-470° C., and a holding time of 10-100 min are applied during the sintering process.

[0026] Compared with the prior art, the advantages of the present invention are:

[0027] 1. The advantage of the present invention is that the aluminum-based composite material is reinforced by using a negative thermal expansion reinforcement and a high thermal conductivity reinforcement. Compared with a composite material prepared by a single negative thermal expansion reinforcement, the material of the present invention maintains a low thermal expansion coefficient while having high thermal conductivity, and has better comprehensive performance.

[0028] 2. Compared with a single high thermal conductivity or negative thermal expansion ceramic reinforcement reinforced aluminum matrix, the present invention can achieve full play of the high thermal conductivity, low density and other characteristics of the aluminum matrix under the premise of relatively low total reinforcement content through the synergistic effect of two reinforcements with different properties, thereby obtaining a composite material with better performance.

[0029] 3. The present invention adopts solid phase sintering technology, and avoids interface reaction by regulating the sintering process to obtain a denser composite material and more accurately control the volume fraction.

[0030] 4. The present invention provides a hybrid reinforced aluminum-based composite material with high thermal conductivity and adjustable thermal expansion coefficient and a preparation method thereof. The method is simple, fast, highly operational, and easy to implement in engineering applications, solving the problem that existing electronic packaging materials are difficult to maintain low thermal expansion and high thermal conductivity. BRIEF DESCRIPTION OF THE DRAWINGS

[0031] In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the following briefly introduces the drawings required for use in the description of the embodiments. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without creative work.

[0032] Figure 1 is the microstructure diagram of the aluminum-based composite material of Example 4;

[0033] Figure 2 is a thermal expansion curve diagram of the Al-Si alloy and the aluminum-based composite material of Example 4;

[0034] In the figure, 1 is the high thermal conductivity reinforcement SiC; 2 is the negative thermal expansion reinforcement ZrW2O8; 3 is the Al-Si alloy matrix. DETAILED DESCRIPTION

[0035] In order to make the invention purpose, technical scheme and beneficial technical effect of the present invention clearer, the present invention is described in detail below in conjunction with specific embodiments. It should be understood that the embodiments described in this specification are only for explaining the present invention, not for limiting the present invention.

[0036] The present invention provides a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient. The material has a low expansion coefficient and high thermal conductivity, and 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 accounts for 10-70 vol.%, wherein the volume content of the negative expansion reinforcement accounts for 5-65 vol.%, the volume content of the high thermal conductivity reinforcement accounts for 5-65 vol.%, and the balance is the aluminum matrix.

[0037] The negative thermal expansion reinforcement is one or a combination of two or more of a ceramic material, an intermetallic compound, and an alloy whose average linear expansion coefficient or volume expansion coefficient is negative at t°C, -100°C<t<300°C.

[0038] Specifically, the negative thermal expansion reinforcement is selected from: (1) ceramic material: chemical formula aα2O8, wherein a represents one or more chemical elements of Zr, Hf, Sn, Ti, Eu, Er, Yb, α represents one or more chemical elements of W, Mo, V; chemical formula bβ2O7, wherein b represents one or more chemical elements of Zr, Th, Ce, β represents one or more chemical elements of P, Mo, V; chemical formula c2γ3O 12 , where c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, Lu, and γ represents one or more of the chemical elements W and Mo; 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; chemical formula eε2P3O 12 , where e represents one or more of the chemical elements Na, K, Nb, Rb, Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; 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; chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; 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; chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd; chemical formula j B(CN)4, wherein j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, wherein 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, wherein l represents one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partial replacement of Mn in the 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.

[0039] (2) Intermetallic compound selected from: Zr y Nb 1-y Fe2、Hf y Nb1-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 etc., wherein y is any value between 0 and 1, x is any value between 0 and 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 partial replacement of the Fe position, Co position or Mn position in the above intermetallic compounds by any one or two elements of Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, and Ta.

[0040] (3) The alloy is selected from: Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, Ti-Nb, etc.

[0041] The high thermal conductivity reinforcement is one or a combination of two or more inorganic non-metallic materials having a thermal conductivity higher than that of the aluminum matrix, such as one or a combination of two or more of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond;

[0042] The aluminum matrix is ​​an aluminum alloy or pure aluminum with an aluminum mass percentage of more than 50wt%, such as Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, Al-Mn alloy, pure aluminum, or a combination of more than two thereof, and the purity of pure aluminum is more than 99.0wt%.

[0043] It should be noted that the negative thermal expansion reinforcement exhibits the property of "heat shrinkage and cold expansion" within the operating temperature range of electronic components. In this temperature range, the average linear expansion coefficient and the volume expansion coefficient are both negative. The negative thermal expansion material is compounded with other positive thermal expansion materials in the aluminum-based composite material to prepare a material with a controllable thermal expansion coefficient, such as a zero expansion material. The material of the high thermal conductivity reinforcement is a material with a higher thermal conductivity. The high thermal conductivity reinforcement is compounded with other materials with a lower thermal conductivity in the aluminum-based composite material to prepare a material with a higher thermal conductivity. Within the allowable range of the volume content of the above-mentioned negative thermal expansion reinforcement and the high thermal conductivity reinforcement, by adjusting their volume ratio, an aluminum-based composite material with different thermal expansion coefficients and thermal conductivities that meets the use conditions is obtained, such as a 10vol% ZrW2O8+10vol% SiC+80vol% Al-Si alloy matrix, whose thermal conductivity is 147.1W / mK and thermal expansion coefficient is 12.6ppm / ℃; 10vol% ZrW2O8 +40vol%SiC+50vol%Al-Si alloy matrix, its thermal conductivity is 131.1W / mK, thermal expansion coefficient is 9.7ppm / ℃; 40vol%ZrW2O8+10vol%SiC+50vol%Al-Si alloy matrix, its thermal conductivity is 63.1W / mK, thermal expansion coefficient is 6.2ppm / ℃; 30vol%ZrW2O8+20vol%SiC+50vol%Al-Si alloy matrix, its The thermal conductivity is 87.2W / mK and the thermal expansion coefficient is 7.6ppm / ℃; the thermal conductivity of 30vol%ZrW2O8+30vol%SiC+40vol%Al-Si alloy matrix is ​​68.7W / mK and the thermal expansion coefficient is 5.1ppm / ℃; the thermal conductivity of 20vol%Cu2P2O7+30vol%SiC+50vol%Al-Si alloy matrix is ​​54.2W / mK and the thermal expansion coefficient is 7.6ppm / ℃.

[0044] The present invention also provides a method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient, comprising the following steps:

[0045] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0046] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0047] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, keeping the temperature or keeping the temperature under pressure for solid phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0048] Specifically, in step S1, first, the total volume is calculated according to the size of the aluminum-based composite material to be prepared; then, the respective volumes of the negative expansion reinforcement, the high thermal conductivity reinforcement and the aluminum matrix are calculated according to the volume fraction; finally, the weight of each material is calculated according to the volume and true density of the negative expansion reinforcement, the high thermal conductivity reinforcement and the aluminum matrix.

[0049] The negative thermal expansion reinforcement powder is one or a combination of two or more of a ceramic powder, an intermetallic compound powder, and an alloy powder, whose average linear expansion coefficient or volume expansion coefficient is negative at t°C, -100°C < t < 300°C, and the average particle size of the negative thermal expansion reinforcement powder is 0.1~500μm. Specifically, the negative thermal expansion reinforcement powder is selected from: (1) ceramic powder: chemical formula aα2O8, wherein 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, and V; chemical formula bβ2O7, wherein 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 c2γ3O 12 , where c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, Lu, and γ represents one or more of the chemical elements W and Mo; 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; chemical formula eε2P3O 12, where e represents one or more of the chemical elements Na, K, Nb, Rb, Cs, and ε represents one or more of the chemical elements Zr, Ti, and Hf; 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; chemical formula g2O(PO4)2, where g represents one or more of the chemical elements U and Th; 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; chemical formula i(CN)2, where i represents one or more of the chemical elements Zn and Cd; chemical formula j B(CN)4, wherein j represents one or more of the chemical elements Cu and Ag; chemical formula kτ(CN)6, wherein 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, wherein l represents one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, and Fe, and compounds formed by partial replacement of Mn in the 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 powder is 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 29etc., wherein y is any value between 0 and 1, x is any value between 0 and 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 partial replacement of the Fe, Co or Mn positions in the above intermetallic compounds by any one or two elements selected from the group consisting of Si, Al, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Y, Zr, Nb, Mo, Hf, and Ta; (3) alloy powders selected from the group consisting of Fe-Ni, Fe-Pt, Cr-Fe, Ni-Ti, and Ti-Nb.

[0050] The high thermal conductivity reinforcement powder is one or a combination of two or more inorganic non-metallic powders having a thermal conductivity higher than that of the aluminum matrix, such as one or a combination of two or more of SiC, Si3N4, AlN, graphite, carbon fiber, graphene, and diamond, and the average particle size of the powder is 0.1~500μm.

[0051] The aluminum matrix powder is an aluminum alloy powder or a combination of one or more of pure aluminum powders with an aluminum mass percentage of more than 50wt%, such as Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Zn alloy, Al-Mn alloy, and pure aluminum, wherein the purity of pure aluminum is more than 99.0wt%, and the average particle size of the aluminum matrix powder is 0.1~500μm.

[0052] Specifically, in step S3, the solid phase sintering is performed in any one of a vacuum sintering furnace, an atmosphere sintering furnace, a hot pressing sintering furnace, a hot isostatic pressing furnace or a spark plasma sintering furnace.

[0053] In vacuum sintering furnace, atmosphere sintering furnace, hot pressing sintering furnace and hot isostatic pressing furnace, the furnace environment is 1×10 -2 ~50Pa vacuum environment or air pressure of 1~1×10 3 A protective gas among nitrogen, argon and helium of Pa. The sintering mold used is a cylindrical graphite or steel mold, which is axially compressible. The inner diameter of the sintering mold is 6-300mm. The pressure applied during the sintering process is 0-200MPa, the temperature is 400-720℃, and the insulation time is 30-120min.

[0054] In the spark plasma sintering furnace, the furnace environment is 1×10 -4 ~100Pa vacuum environment or air pressure of 10~1×10 3A protective gas among nitrogen, argon and helium of 0.04 Pa. The sintering mold used is a cylindrical graphite or steel mold, which 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 insulation time is 5-100 min; if the pressure is 70-200 MPa, the temperature is 400-470 °C, and the insulation time is 10-100 min.

[0055] Firstly, the hybrid reinforcement preparation method of the present invention can achieve flexible matching of the two thermophysical properties of thermal conductivity and thermal expansion coefficient of aluminum-based composite materials; secondly, the solid phase sintering method of the present invention can prepare aluminum-based composite materials with low volume fraction reinforcement and can control the accuracy of the volume fraction.

[0056] Example 1

[0057] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC accounts for 20 vol.%, wherein the volume content of the negative expansion reinforcement ZrW2O8 accounts for 10 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 10 vol.%, and the balance is the Al-Si alloy matrix.

[0058] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0059] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0060] Prefabricated aluminum matrix composite volume 3.14cm 3 , weigh 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.

[0061] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0062] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0063] Solid phase sintering is carried out in a discharge plasma furnace in a vacuum environment of 10Pa. The sintering mold used is cylindrical graphite. The inner diameter of the sintering mold is 20mm. The pressure applied during the sintering process is 30MPa. The temperature during the sintering process is 500°C and the holding time is 10min.

[0064] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0065] Example 2

[0066] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC accounts for 50 vol.%, wherein the volume content of the negative expansion reinforcement ZrW2O8 accounts for 10 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 40 vol.%, and the remainder is the Al-Si alloy matrix.

[0067] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0068] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0069] Prefabricated aluminum matrix composite volume 678.58cm 3 , weigh 346.08g of negative expansion reinforcement ZrW2O8 powder, 871.30g of high thermal conductivity reinforcement SiC powder, and 909.30g of Al-Si alloy powder. The average particle size of ZrW2O8 powder is 100μm, the average particle size of SiC powder is 5μm, and the average particle size of Al-Si alloy powder is 500μm.

[0070] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0071] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0072] Solid phase sintering is carried out in a spark plasma furnace with an environment of 1×10 -1The sintering mold used was a cylindrical graphite in a vacuum environment of 120 mm in diameter. The pressure applied during the sintering process was 80 MPa. The temperature during the sintering process was 550°C and the holding time was 100 min.

[0073] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0074] Example 3

[0075] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC accounts for 50 vol.%, wherein the volume content of the negative expansion reinforcement ZrW2O8 accounts for 40 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 10 vol.%, and the balance is the Al-Si alloy matrix.

[0076] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0077] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0078] Prefabricated aluminum matrix composite volume 201.06cm 3 , weigh 410.17g of negative expansion reinforcement ZrW2O8 powder, 64.54g of high thermal conductivity reinforcement SiC powder, and 269.42g of Al-Si alloy powder. The average particle size of ZrW2O8 powder is 5μm, the average particle size of SiC powder is 80μm, and the average particle size of Al-Si alloy powder is 250μm.

[0079] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0080] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0081] Solid phase sintering is carried out in a spark plasma furnace with an environment of 1×10 -1 Pa vacuum environment, the sintering mold used is cylindrical graphite, axially compressible, the inner diameter of the sintering mold is 80mm, the pressure applied during the sintering process is 50MPa, the temperature is 550℃, and the holding time is 40min.

[0082] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0083] Example 4

[0084] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC accounts for 50 vol.%, wherein the volume content of the negative expansion reinforcement ZrW2O8 accounts for 30 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 20 vol.%, and the balance is the Al-Si alloy matrix.

[0085] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0086] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0087] Prefabricated aluminum matrix composite volume 0.39cm 3 , weigh 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.

[0088] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0089] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0090] Solid phase sintering is carried out in a spark plasma furnace with an environment of 1×10 -4 Pa vacuum environment, the sintering mold used is cylindrical graphite; the inner diameter of the sintering mold is 10 mm, the pressure applied during the sintering process is 40 MPa, the temperature during the sintering process is 500°C, and the insulation time is 5 min.

[0091] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0092] Figure 1This is the microstructure diagram of the aluminum-based composite material of Example 4, where 1 is the high thermal conductivity reinforcement SiC, 2 is the negative thermal expansion reinforcement ZrW2O8, and 3 is the Al-Si alloy matrix. Figure 2 The thermal expansion curves of the Al-Si alloy and the aluminum-based composite material in Example 4 show that the thermal expansion coefficient of the Al-Si alloy is 21.0 ppm / °C in the range of -100°C to 50°C, and the thermal expansion coefficient of the aluminum-based composite material is 7.6 ppm / °C. It can be seen that adding the negative thermal expansion reinforcement ZrW2O8 to the Al-Si alloy reduces the thermal expansion coefficient of the composite material.

[0093] Example 5

[0094] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement ZrW2O8, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement ZrW2O8 and the high thermal conductivity reinforcement SiC accounts for 60 vol.%, wherein the volume content of the negative expansion reinforcement ZrW2O8 accounts for 30 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 30 vol.%, and the balance is the Al-Si alloy matrix.

[0095] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0096] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0097] Prefabricated aluminum matrix composite volume 25.13cm 3 , weigh 38.45g of negative expansion reinforcement ZrW2O8 powder, 24.20g of high thermal conductivity reinforcement SiC powder, and 26.94g of Al-Si alloy powder. The average particle size of ZrW2O8 powder is 8μm, the average particle size of SiC powder is 70μm, and the average particle size of Al-Si alloy powder is 250μm.

[0098] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0099] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0100] Solid phase sintering is carried out in a spark plasma furnace with an environment of 1×10 -3Pa vacuum environment, the sintering mold used is cylindrical graphite; the inner diameter of the sintering mold is 40 mm, the pressure applied during the sintering process is 50 MPa, the temperature during the sintering process is 500°C, and the insulation time is 20 min.

[0101] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0102] Example 6

[0103] A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises a negative thermal expansion reinforcement Cu2P2O7, a high thermal conductivity reinforcement SiC and an Al-Si alloy matrix, wherein the total volume content of the negative thermal expansion reinforcement Cu2P2O7 and the high thermal conductivity reinforcement SiC accounts for 50 vol.%, wherein the volume content of the negative expansion reinforcement Cu2P2O7 accounts for 20 vol.%, the volume content of the high thermal conductivity reinforcement SiC accounts for 30 vol.%, and the remainder is the Al-Si alloy matrix.

[0104] A method for preparing a high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient comprises the following steps:

[0105] Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly;

[0106] Prefabricated aluminum matrix composite volume 392.70cm 3 , weigh 471.24g of negative expansion reinforcement Cu2P2O7 powder, 252.11g of high thermal conductivity reinforcement SiC powder, and 526.22g of Al-Si alloy powder. The average particle size of Cu2P2O7 powder is 70μm, the average particle size of SiC powder is 3μm, and the average particle size of Al-Si alloy powder is 400μm.

[0107] Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder;

[0108] Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, maintaining heat and applying pressure to perform solid-phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material;

[0109] Solid phase sintering is carried out in a spark plasma furnace with an environment of 1×10 -1 The sintering mold used was a cylindrical graphite in a vacuum environment of 1.04 Pa; the inner diameter of the sintering mold was 100 mm; the pressure applied during the sintering process was 30 MPa; the temperature during the sintering process was 550°C; and the insulation time was 50 min.

[0110] The thermal conductivity of the prepared aluminum-based composite material was tested by a thermal conductivity meter, and the thermal expansion coefficient of the prepared aluminum-based composite material was tested by a linear thermal expansion meter. The test results are shown in Table 1.

[0111] Table 1 Thermophysical properties of aluminum-based composite materials of Examples 1 to 6

[0112]

[0113] It can be seen from Examples 1 to 6 that by selecting negative expansion reinforcements, high thermal conductivity reinforcements, and aluminum substrates of different materials and volume ratios, aluminum-based composite materials with thermal conductivity of 54.2 to 147.1 W / mK and thermal expansion coefficient of 5.1 to 12.6 ppm / °C can be obtained. This patent greatly improves the thermal conductivity of aluminum-based composite materials while obtaining a low thermal expansion coefficient through hybrid reinforcement design, specifically, in Example 4, a low thermal expansion coefficient of 7.6 ppm / °C is maintained and a high thermal conductivity of 87.2 W / mK is obtained.

[0114] The above is only a specific embodiment of the present invention, but the protection scope of the present invention is not limited thereto. Any technician familiar with the technical field can easily think of various equivalent modifications or substitutions within the technical scope disclosed by the present invention, and these modifications or substitutions should be included in the protection scope of the present invention. Therefore, the protection scope of the present invention shall be based on the protection scope determined by the claims.

Claims

1. A high thermal conductivity aluminum-based composite material with adjustable thermal expansion coefficient, It is characterized in that The material comprises a negative thermal expansion reinforcement, a high thermal conductivity reinforcement and an aluminum matrix, wherein the total volume content of the negative thermal expansion reinforcement and the high thermal conductivity reinforcement is 10-70 vol.%, wherein 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 ceramic materials, intermetallic compounds, and alloys whose average linear expansion coefficient or volume expansion coefficient is negative when t°C, -100°C<t<300°C; the high thermal conductivity reinforcement is one or a combination of two or more inorganic non-metallic materials whose thermal conductivity is higher than the thermal conductivity of the aluminum matrix; the aluminum matrix is ​​one or a combination of two or more aluminum alloys or pure aluminum with an aluminum mass percentage of more than 50wt%, and the purity of pure aluminum is more than 99.0wt%.

2. The material according to claim 1, It is characterized in that The ceramic material is selected from at least one of the following chemical formulas: 2 O 8 , where a represents one or more of the chemical elements Zr, Hf, Sn, Ti, Eu, Er, Yb, α represents one or more of the chemical elements W, Mo, V; chemical formula bβ 2 O 7 , 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; the chemical formula c 2 γ 3 O 12 , where c represents one or more of the chemical elements Sc, Dy, Y, Er, Yb, Lu, and γ represents one or more of the chemical elements W and Mo; the chemical formula is dδO 5 , 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 is eε 2 P 3 O 12 , where e represents one or more of the chemical elements Na, K, Nb, Rb, Cs, and ε represents one or more of the chemical elements Zr, Ti, Hf; the chemical formula f 2 ζ 2 O 7 , 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 g 2 O(PO 4 ) 2 , where g represents one or more of the chemical elements U and Th; the chemical formula is hθF 6 , where h represents one or more of the chemical elements Ca, Mn, Fe, Zn, Co, Ni, Mg, Yb, Ti, and θ represents one or more of the chemical elements Zr, Hf, Nb; chemical formula i (CN) 2 , where i represents one or more of the chemical elements Zn and Cd; chemical formula jB(CN) 4 , where j represents one or more of the chemical elements Cu and Ag; the chemical formula is 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; the chemical formula Mn 3 lN, where l is one or more of Zn, Cu, Ga, Sn, Ge, Si, Ge, Fe, and the chemical formula is Mn 3 Compounds formed by partial replacement of the Mn position in lN by any one or two elements of V, Cr, Fe, Co, Ni, Cu, and Zn; Zn[Ag(CN) 2 ] 2 、CaZr 4 P 6 O 24 、Si(NCN) 2 、ReO 3 、SiO 2 , Cu 2 O、Ag 2 O、ScF 3 ; The intermetallic compound is selected from at least one of the following chemical formulas: Zr y Nb 1-y Fe 2 , Hf y Nb 1-y Fe 2 , Hf 1-y Ta y Fe 2 Sc 1-y Ti y Fe 2 CrTe y Se 1-y 、LaFe 13-x Si x 、LaFe 13-x Al x , Mn 3 Ge, Mn-Co-Ge series, Fe-Mn-Ga series, Ni-Mn-Ga series, RCo 2 , R 2 Fe 14 B.R 2 Fe 17 ,RCo 3 、RFe 12 , R 3 Fe 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 an intermetallic compound formed by partial substitution of the Fe position, Co position or Mn position in the above chemical formula by 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, It is characterized in that The inorganic non-metallic material is selected from SiC, Si 3 N 4 , AlN, graphite, carbon fiber, graphene, and diamond.

4. The material according to claim 1, It is 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 adjustable thermal expansion coefficient, It is characterized in that The method is used to prepare the material according to any one of claims 1 to 4, and the method comprises the following steps: Step S1, according to the volume fraction of the aluminum-based composite material to be prepared, converted into weight, the negative expansion reinforcement powder, the high thermal conductivity reinforcement powder and the aluminum matrix powder are weighed accordingly; Step S2, mixing the three powders weighed in step S1 uniformly to obtain a composite powder; Step S3, loading the composite powder of step S2 into a sintering mold and moving it into a furnace, adjusting the furnace environment, keeping the temperature or keeping the temperature under pressure for solid phase sintering, cooling with the furnace, and taking it out at room temperature to obtain an aluminum-based composite material.

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

7. The method according to claim 5, It is characterized in that In the step S3, the solid phase sintering is performed in any one of a vacuum sintering furnace, an atmosphere sintering furnace, a hot pressing sintering furnace, a hot isostatic pressing furnace or a spark plasma sintering furnace.

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

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

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

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