Aluminum net shaped aluminum-diamond composite material with vertical seepage and preparation method thereof

Abstract

The present application belongs to the technical field of metal matrix composite material preparation, and particularly relates to an aluminum-diamond composite material with aluminum net shaping and vertical infiltration and a preparation method thereof. The composite material is composed of an aluminum matrix and diamond particles, and a three-dimensional framework composed of aluminum nets is arranged in the composite material, and the diamond particles are constrained in the net holes of the aluminum net framework. The preparation method comprises the following steps: assembling diamond particles with different particle sizes and aluminum nets with a predetermined thickness into a diamond-aluminum net preform; stacking a solid aluminum supply layer above the preform to form a layered structure; placing the layered structure in a mold, melting the aluminum supply layer to form an aluminum melt at a temperature of 680-750 DEG C and a pressure of 8-10 MPa, and making the aluminum melt vertically infiltrate from top to bottom, and cooling and demolding after infiltrating for 1-5 min, to obtain a dense aluminum-diamond composite material. The present application inhibits the displacement of diamond particles during the forming process, reduces the porosity of the composite material, and obtains an aluminum-diamond composite material with a high volume fraction, high density and high thermal conductivity.

Description

Technical Field

[0001] This invention belongs to the field of metal matrix composite material preparation technology, specifically relating to aluminum-diamond composite materials with aluminum mesh shaping and vertical infiltration, and their preparation methods. Background Technology

[0002] Aluminum-diamond composites possess the advantages of both aluminum's lightweight and easy processing properties and diamond's ultra-high thermal conductivity, making them promising candidates for applications in electronic packaging and thermal management. The key to preparing high-performance aluminum-diamond composites lies in achieving a high volume fraction distribution of diamond particles within the aluminum matrix, good interfacial bonding, and extremely low porosity.

[0003] In existing technologies, using a metal mesh to spatially constrain diamond particles to improve their distribution uniformity is an effective method. For example, prior art document CN110453126A discloses a diamond-metal composite thermally conductive material and its preparation method. This method involves arranging a metal mesh filled with diamond powder between metal foils to form a layered composite, which is then sintered using a vacuum hot-pressing method. In this method, the presence of the metal mesh can indeed stabilize the position of the diamond particles to a certain extent and optimize the particle size distribution.

[0004] However, the vacuum hot pressing method used in the aforementioned existing technology essentially involves applying extremely high static pressure (30-50 MPa) at high temperatures, causing the metal foil and metal mesh to melt, deform, and flow, thereby filling the voids between diamond particles. This process has the following limitations: First, the extremely high global static pressure may force the initially positioned diamond particles to undergo secondary displacement or rolling, affecting the stability of the preform structure; second, during the hot pressing process, the flow direction of the metal is controlled by the pressure field within the mold, lacking directionality, which may lead to the formation of "dead zones" of metal flow within the complex preform, thus leaving pores; furthermore, the hot pressing process usually requires a long holding time to ensure sufficient metal flow, limiting production efficiency. Therefore, this closest existing technical solution is based on static high-pressure compaction logic, and its high-pressure environment inherently contradicts the initial intention of spatial constraints in metal mesh shaping.

[0005] Therefore, the key to improving the performance and preparation efficiency of aluminum-diamond composites lies in how to use a non-high-pressure static compaction molding process that can achieve full directional filling of aluminum melt, based on the spatial shaping of diamond particles using metal mesh, in order to jointly solve the problems of diamond displacement and porosity residue. Summary of the Invention

[0006] The purpose of this invention is to provide an aluminum-diamond composite material with aluminum mesh shaping and vertical permeation, and its preparation method, so as to solve the problems of particle displacement, insufficient metal filling and high porosity caused by high pressure hot pressing in the prior art.

[0007] The technical solution of the present invention is as follows: On the one hand, a method for preparing an aluminum-diamond composite material with aluminum mesh shaping and vertical infiltration is provided, comprising the following steps: S1. Provides diamond particles and aluminum mesh; S2. Fill the aluminum mesh with the diamond particles to form a diamond-aluminum mesh preform; S3. A solid aluminum supply layer is stacked on top of the diamond-aluminum mesh preform to form a layered structure; S4. Place the layered structure in a mold, heat it to 680-750℃, and under a pressure of 8-10MPa, allow the aluminum melt formed by melting the solid aluminum layer to vertically permeate the diamond-aluminum mesh preform from top to bottom for 1-5 minutes. S5. After the infiltration is completed, the material is cooled and demolded to obtain the aluminum-diamond composite material.

[0008] Preferably, in step S1, the diamond particles have a particle size of 150-500 μm, and the aluminum mesh has a thickness of 200-400 μm.

[0009] Preferably, in step S1, the diamond particles include diamond particles of a first diameter and diamond particles of a second diameter, wherein the diameter of the first diameter diamond particles is 150-250 μm and the diameter of the second diameter diamond particles is 300-500 μm.

[0010] Preferably, in step S4, the temperature of the vertical seepage is 700-730℃.

[0011] Preferably, in step S4, the pressure of the vertical seepage is 9-10 MPa.

[0012] Preferably, in step S1, the surface of the diamond particles is pre-coated with a metal coating or a ceramic coating.

[0013] Preferably, the metal coating is a Ti coating, a Cr coating, or a W coating, and the ceramic coating is a SiC coating.

[0014] Preferably, in step S3, solid aluminum supply layers are stacked above and below the diamond-aluminum mesh preform, and the thickness of the upper solid aluminum supply layer is greater than the thickness of the lower solid aluminum supply layer.

[0015] On the other hand, an aluminum-diamond composite material with aluminum mesh shaping and vertical permeation is provided, which is prepared by any of the above preparation methods.

[0016] Preferably, the composite material contains a three-dimensional skeleton structure made of aluminum mesh, and the diamond particles are distributed in the skeleton structure; the porosity of the composite material is ≤5%, and the thermal conductivity is ≥600 W / (m·K).

[0017] Compared with the prior art, the advantages of the present invention are: (1) Before the infiltration process, the present invention uses aluminum mesh to assemble a preform skeleton with good rigidity to fix the diamond position. Subsequently, a vertical infiltration process with significantly reduced pressure (8-10 MPa) and single direction is adopted. This pressure is mainly used to drive the aluminum liquid to flow and fill along the direction of gravity, rather than to compact the preform in a global multi-directional manner. Therefore, the lateral extrusion pressure on the preform skeleton is reduced, which helps to maintain the initial spatial position of the diamond particles during the densification process and reduces the secondary displacement of the particles in the final forming stage.

[0018] (2) The present invention adopts a top-down directional vertical flow, in which the aluminum melt flows downward sequentially and directionally along the pore channels of the preform under the pressure difference. This flow mode enables the aluminum melt front to gradually and effectively drive the gas in the preform downward and discharge it, reducing the risk of gas being trapped inside and forming pores due to metal turbulence and eddies, thereby promoting more complete filling and reducing the porosity of the composite material.

[0019] (3) During the infiltration process, the high-temperature aluminum melt comes into contact with the aluminum mesh skeleton, causing the skeleton surface to partially melt, thereby achieving metallurgical bonding with the infiltrated aluminum liquid. After solidification, the aluminum mesh skeleton integrates and becomes part of the continuous aluminum matrix network. This not only ensures the continuity of the spatial confinement effect, but also forms a continuous three-dimensional aluminum phase heat conduction path.

[0020] (4) By independently adjusting the aluminum mesh parameters (such as thickness, number of layers, and arrangement), diamond gradation, coating, and percolation temperature, pressure, and time, the densification process, final microstructure, and interface state of the composite material can be controlled more precisely, providing a flexible and controllable process path for obtaining composite materials with low porosity and high thermal conductivity. Attached Figure Description

[0021] The present invention will be further described below with reference to the accompanying drawings and embodiments: Figure 1 This is a schematic diagram of the structure of the diamond-aluminum mesh preform described in this invention; Figure 2 This is a schematic diagram of the final aluminum-diamond composite material product obtained by the preparation method described in this invention. Detailed Implementation

[0022] The present invention will be further described in detail below with reference to specific embodiments: The core of the preparation method of this invention lies in two synergistic steps: the construction of an aluminum mesh spatially shaped preform and the directional vertical infiltration densification of liquid aluminum. The temperature and pressure parameters for vertical infiltration are determined based on the fluidity of the aluminum melt, its wettability to diamond, and the stability of the preform skeleton. Below 680℃, the aluminum melt viscosity is high, making it difficult to fully penetrate the fine pores of the preform; above 750℃, it may exacerbate the adverse reaction at the aluminum-diamond interface. Pressures below 8 MPa may be insufficient to overcome capillary resistance and drive the aluminum melt to completely fill the preform; pressures above 10 MPa may cause plastic deformation of the aluminum mesh skeleton, weakening its spatial constraint ability. Preferably, the process is carried out at 700-730℃ and 9-10 MPa. Within this process parameter range, the aluminum melt has excellent fluidity and wettability, while the pressure is sufficient to achieve dense filling without excessively damaging the preform structure.

[0023] Example 1

[0024] In this embodiment, an aluminum-diamond composite material is prepared, with a target diamond volume fraction of approximately 60 vol.

[0025] S1. Raw material preparation Two types of synthetic single-crystal diamond particles are provided: a first-size particle with a diameter range of 150-250 μm (average approximately 200 μm); and a second-size particle with a diameter range of 300-500 μm (average approximately 400 μm). The two types of particles are mixed at a mass ratio of 1:1.

[0026] A 300μm thick pure aluminum mesh (1060 pure aluminum) is provided, with mesh size matching the size of the mixed diamond particles to ensure that most particles can be effectively constrained by the mesh.

[0027] In this embodiment, no surface coating treatment is applied to the diamond particles.

[0028] S2, Preform Preparation On a flat substrate, a layer of the aforementioned aluminum mesh is laid. The mixed diamond particles are evenly distributed onto this layer of aluminum mesh and gently smoothed with a scraper, ensuring the diamond particles fill the mesh openings and are slightly higher than the mesh surface. Then, a second layer of aluminum mesh is applied, and diamond particles are similarly distributed and smoothed. This process is repeated, stacking five layers of aluminum mesh and diamond particles to form a diamond-aluminum mesh preform of a certain thickness. In this preform, the aluminum mesh forms a continuous framework, and the diamond particles are confined within the mesh openings and interlayer gaps, as shown in the diagram. Figure 1As shown, this assembly method interconnects the aluminum meshes in three-dimensional space, forming a self-supporting open framework. Diamond particles are mechanically confined within the mesh units formed by the woven aluminum mesh and in the gaps between adjacent mesh layers. This prefabricated structure not only prevents large-scale movement of diamond particles during subsequent seepage, but its own porosity also provides pre-defined, continuous channels for the flow of molten aluminum.

[0029] S3, Layered Structure Assembly On top of the prepared diamond-aluminum mesh preform, a solid aluminum supply layer composed of multiple layers of 0.1mm thick 1060 pure aluminum foil is stacked. The total thickness of the aluminum supply layer is calculated to ensure that the volume of molten aluminum it provides after melting is sufficient to completely wet and fill all voids in the preform, achieving the target aluminum matrix content. In this embodiment, the thickness of the aluminum supply layer is approximately 1.5 times the height of the preform.

[0030] S4, Vertical permeation molding The assembled layered structure is placed into a steel mold and heated to 600°C at a rate of 10°C / min in a pit furnace. The mold is then transferred into a pressure mold, and molten aluminum at 720°C is poured on top. Driven by both pressure and gravity, the molten aluminum penetrates directionally from top to bottom into the diamond-aluminum mesh preform below.

[0031] Maintaining a temperature of 720℃ and a pressure of 9MPa, infiltration was carried out for 1 minute. During this process, the molten aluminum gradually filled all the pores within the aluminum mesh skeleton and between the diamond particles. The aluminum mesh itself also partially melted at the high temperature, combining with the infiltrated molten aluminum.

[0032] When pressure is applied, the molten aluminum first spreads on the surface of the top preform, and then, driven by pressure, preferentially seeps downward along the gaps between the aluminum mesh wires and the larger pore channels formed by the diamond particles and the aluminum mesh. This process is front-propelled; the leading edge of the molten aluminum pushes the gas in the preform downward and eventually towards the mold venting system, rather than trapping it inside. As seepage proceeds, the high-temperature molten aluminum undergoes heat conduction and limited intermelting with the aluminum mesh skeleton, causing the surface of the skeleton wires to gradually melt, thereby achieving metallurgical bonding with the flowing molten aluminum. Finally, after solidification, a composite structure is formed where the aluminum matrix and the original aluminum mesh skeleton are integrated, and the diamond particles are firmly embedded, as shown in the image. Figure 2 As shown.

[0033] S5, Cooling and Demolding After infiltration is complete, heating is stopped, and the furnace is cooled to below 200°C while maintaining pressure. Then, the pressure is released, and cooling continues to room temperature. After demolding, a blocky aluminum-diamond composite preform is obtained. Further machining can be performed as needed.

[0034] The properties of the obtained composite material were tested: the density was determined using the Archimedes displacement method, and the porosity was calculated to be approximately 3.8%. The thermal diffusivity was measured using the laser scintillation method, and the thermal conductivity was calculated by combining the specific heat capacity and density, with a result of approximately 620 W / m·K. The diamond volume fraction was quantitatively estimated using image analysis, and was approximately 58 vol%.

[0035] Example 2

[0036] Based on Example 1, this embodiment applies a surface coating to the diamond particles and optimizes the percolation process parameters, aiming to further improve interfacial bonding and increase densification efficiency.

[0037] S1. Raw material preparation The particle size distribution of the diamond particles was the same as in Example 1. A Ti coating with a thickness of approximately 100 nm was prepared on the surface of the diamond particles using magnetron sputtering. The purpose of this coating is that, during the subsequent high-temperature infiltration process, the Ti element can react with the carbon on the diamond surface to form a TiC transition layer, thereby improving the wettability between the aluminum melt and the diamond, reducing the interfacial thermal resistance, and simultaneously inhibiting the formation of the harmful Al4C3 phase.

[0038] The aluminum mesh parameters are the same as in Example 1 (1060 pure aluminum mesh with a thickness of 300μm).

[0039] S2, Preform Preparation The preparation method is the same as in Example 1, where diamond particles coated with Ti are assembled with an aluminum mesh to form a 5-layer diamond-aluminum mesh preform (e.g., Figure 1 (As shown).

[0040] S3, Layered Structure Assembly Similar to Example 1, a sufficient amount of solid aluminum supply layer (1060 pure aluminum foil) is stacked on top of the preform.

[0041] S4, Vertical permeation molding To promote effective reaction between the Ti coating and diamond, and better wetting of the coated diamond by the molten aluminum, this embodiment increases the infiltration temperature to 740°C and slightly increases the infiltration pressure to 9.5 MPa to compensate for the viscosity change of the molten aluminum due to the increased temperature, ensuring filling power. The specific process is as follows: the preform is heated to 600°C, then transferred to a press mold, molten aluminum at 740°C is poured in, a pressure of 9.5 MPa is applied, and infiltration is maintained at this temperature for 3 minutes. The higher temperature helps accelerate the formation of the TiC reaction layer, while the combination of moderate pressure and shortened infiltration time aims to achieve rapid densification while reducing potential thermal damage to the diamond.

[0042] S5, Cooling and Demolding After the infiltration process is completed, the pressure is maintained and cooled to below 200°C. After depressurization, the material is cooled to room temperature and demolded to obtain a composite material preform.

[0043] Performance testing: The resulting composite material has a porosity of approximately 2.5%, an increased thermal conductivity of approximately 670 W / (m·K), and a diamond volume fraction of approximately 59 vol%. Compared to Example 1, the further reduction in porosity and the increase in thermal conductivity confirm the positive effect of the Ti coating on improving interfacial bonding and promoting the spread and filling of aluminum melt.

[0044] Example 3

[0045] This embodiment focuses on the impact of differentiated aluminum supply layer design on the filling quality of the bottom region of the composite material, aiming to optimize the filling uniformity of the aluminum melt in the thickness direction of the preform.

[0046] S1. Raw material preparation Same as in Example 1, using uncoated two-graded diamond particles and a 300μm thick 1060 pure aluminum mesh.

[0047] S2, Preform Preparation Similar to Example 1, a 5-layer diamond-aluminum mesh preform was prepared (e.g., Figure 1 (As shown).

[0048] S3, Layered Structure Assembly A differentiated aluminum supply layer design is employed. Specifically, a thicker aluminum supply layer (composed of 20 layers of 0.1mm aluminum foil, with a total thickness of approximately 2.0mm) is placed on top of the diamond-aluminum mesh preform. Simultaneously, a thinner aluminum supply layer (composed of 5 layers of 0.1mm aluminum foil, with a total thickness of approximately 0.5mm) is pre-laid at the bottom of the mold before the preform is placed on top of this thin aluminum supply layer. The mechanism of this design is that the thicker aluminum supply layer at the top provides the primary source of molten aluminum, implementing a top-down main flow; the thinner aluminum supply layer at the bottom, after melting upon heating, can form a small amount of bottom-up reverse micro-flow. The two portions of molten aluminum meet in the middle region of the preform, which helps to expel residual gas in this area and may improve the relative porosity problem caused by the aluminum liquid arriving last and solidifying and shrinking at the bottom.

[0049] S4, Vertical permeation molding The process parameters are the same as in Example 1: 720℃, 9MPa, seepage for 1 min.

[0050] S5, Cooling and Demolding The process is the same as in Example 1, and the composite material is obtained after cooling and demolding.

[0051] Performance testing: The overall porosity of the resulting composite material was comparable to that of Example 1 (approximately 3.9%). However, metallographic microscopy revealed a more uniform pore distribution from top to bottom, particularly near the bottom, where the number of macroscopic pores larger than 10 μm was significantly less than in Example 1. The overall thermal conductivity of the material was approximately 625 W / (m·K). This indicates that the differentiated aluminum-supply layer design has a positive effect on improving the uniformity of filling in the thickness direction.

[0052] Example 4

[0053] This embodiment explores the influence of a composite skeleton composed of alternating layers of aluminum mesh with different thicknesses on the flow path of molten aluminum, the diamond confinement effect, and the final properties of the composite material.

[0054] S1. Raw material preparation The diamond particles are the same as in Example 1 (uncoated, two-grade).

[0055] Two thicknesses of aluminum mesh are available: one is 200μm thick and the other is 400μm thick (both are made of 1060 pure aluminum).

[0056] S2, Preform Preparation The preform was constructed using an alternating layering method: a 200μm thick aluminum mesh was first laid on the substrate, filled with diamond particles, and leveled; then a 400μm thick aluminum mesh was laid, also filled with diamond particles; this process was repeated for a total of 6 layers (in the order: 200μm, 400μm, 200μm, 400μm, 200μm, 400μm). This alternating thickness structure aims to create channels with periodically varying pore sizes, which theoretically could affect the morphology and flow velocity of the aluminum melt's infiltration front, thereby influencing the gas expulsion process and the final densification effect.

[0057] S3, Layered Structure Assembly Similar to Example 1, a sufficient amount of solid aluminum supply layer is stacked on top of the preform.

[0058] S4, Vertical permeation molding The process parameters are the same as in Example 1: 720℃, 9MPa, seepage for 1 min.

[0059] S5, Cooling and Demolding The process is the same as in Example 1, and the composite material is obtained after cooling and demolding.

[0060] Performance testing: The resulting composite material had a porosity of approximately 4.2% and a thermal conductivity of approximately 610 W / (m·K). Its performance was slightly lower than that of Example 1. Analysis suggests that the thinner aluminum mesh (200 μm) may have a slightly weaker ability to confine the diamond and was more prone to softening and deformation at high temperatures, potentially slightly affecting the overall stability of the preform skeleton. However, the overall performance remained at a high level, indicating that within a certain range, variations in the aluminum mesh thickness were not the most critical factor affecting performance.

[0061] Comparative Example This comparative example aims to compare the effects of the method of the present invention with the closest prior art (hot pressing method).

[0062] The comparative example used the same diamond particles and aluminum mesh as in Example 1 to prepare a diamond-aluminum mesh preform with a similar structure. However, instead of the vertical infiltration process, the typical hot pressing process of Example 1 in CN110453126A was used: the preform and aluminum foil were stacked and placed in a graphite mold, placed in a vacuum hot press furnace, vacuumed, heated to 700°C, pressure of 35 MPa was applied, pressure was held for 60 min, and then pressure was held and cooled.

[0063] The obtained material underwent the same tests: the porosity was approximately 7.5%, and the thermal conductivity was approximately 520 W / m·K. Observations showed that there was obvious pore aggregation in some areas, and some diamond particles tended to align along the pressure direction, indicating that the particles moved relatively during the high-pressure hot pressing process, and the metal filling was not as sufficient as vertical seepage.

[0064] The comparative results show that, although the same aluminum mesh preform was used, the high-pressure hot pressing process (35 MPa) applied static pressure, which more easily caused the aluminum mesh and diamond to undergo coordinated deformation or displacement in the plane. In contrast, the vertical seepage process of this invention, whose main driving force is the pressure gradient along the seepage direction, exerts far less lateral pressure on the preform than the hot pressing method. Therefore, it better maintains the initial structure of the preform, achieving lower porosity and higher thermal conductivity.

[0065] Table 1: Comparison of Process and Performance in Examples and Comparative Examples

[0066] The analysis results based on Table 1 are as follows: Examples 1-4 demonstrate the impact of adjusting variables such as diamond surface condition (Example 2), aluminum supply method (Example 3), and aluminum mesh skeleton structure (Example 4) on the final properties of the composite material under the concept of "aluminum mesh shaping combined with vertical infiltration" of this invention. All examples were subjected to directional infiltration within a medium pressure range of 8-10 MPa, and their porosity (2.5%-4.2%) and thermal conductivity (610-670 W / (m·K)) were significantly better than the comparative example using 35 MPa high-pressure static hot pressing (porosity 7.5%, thermal conductivity 520 W / (m·K)). This indicates the effectiveness of the synergistic process of "aluminum mesh spatial constraint" and "medium-pressure directional infiltration" in solving the two related problems of particle displacement and pore residue; that is, moderate directional pressure is sufficient to drive dense filling while avoiding excessive compression and damage to the preform skeleton.

[0067] As can be seen from the above embodiments and comparative examples, the aluminum mesh shaping and vertical infiltration preparation method provided by the present invention, compared with the traditional hot pressing method, can more effectively maintain the predetermined spatial distribution of diamond particles during the molding process and achieve more complete and denser filling of the aluminum melt, thereby significantly reducing the porosity of the composite material and improving its thermal conductivity. By adjusting the diamond particle size, coating, aluminum mesh parameters, and infiltration process parameters, the material properties can be further optimized.

[0068] The above embodiments are merely illustrative of the technical concept and features of the present invention, intended to enable those skilled in the art to understand the content of the present invention and implement it accordingly, and should not be construed as limiting the scope of protection of the present invention. It will be apparent to those skilled in the art that the present invention is not limited to the details of the above exemplary embodiments, and that the present invention can be implemented in other specific forms without departing from the spirit or essential characteristics of the present invention. Therefore, the embodiments should be considered exemplary and non-limiting in all respects. The scope of the present invention is defined by the appended claims rather than the foregoing description, and thus all changes falling within the meaning and scope of the equivalents of the claims are intended to be included within the present invention.

Claims

1. A method for preparing an aluminum-diamond composite material with aluminum mesh shaping and vertical diffusion, comprising the following steps: S1. Provides diamond particles and aluminum mesh; S2. Fill the aluminum mesh with the diamond particles to form a diamond-aluminum mesh preform; S3. A solid aluminum supply layer is stacked on top of the diamond-aluminum mesh preform to form a layered structure; S4. Place the layered structure in a mold, heat it to 680-750℃, and under a pressure of 8-10MPa, allow the aluminum melt formed by melting the solid aluminum layer to vertically permeate the diamond-aluminum mesh preform from top to bottom for 1-5 minutes. S5. After the infiltration is completed, the material is cooled and demolded to obtain the aluminum-diamond composite material.

2. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical infiltration according to claim 1, characterized in that, In step S1, the diamond particles have a particle size of 150-500 μm; the aluminum mesh has a thickness of 200-400 μm.

3. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 2, characterized in that, In step S1, the diamond particles include diamond particles of a first diameter and diamond particles of a second diameter. The first diameter diamond particles have a diameter of 150-250 μm, and the second diameter diamond particles have a diameter of 300-500 μm.

4. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 1, characterized in that, In step S4, the temperature of the vertical seepage is 700-730℃.

5. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 1, characterized in that, In step S4, the pressure of the vertical seepage is 9-10 MPa.

6. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical infiltration according to claim 1, characterized in that, In step S1, the surface of the diamond particles is pre-coated with a metal coating or a ceramic coating.

7. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 6, characterized in that, The metal coating is a Ti coating, a Cr coating, or a W coating, and the ceramic coating is a SiC coating.

8. The method for preparing aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 1, characterized in that, In step S3, a solid aluminum supply layer is also stacked below the diamond-aluminum mesh preform, and the thickness of the upper solid aluminum supply layer is greater than the thickness of the lower solid aluminum supply layer.

9. An aluminum-diamond composite material for aluminum mesh shaping and vertical permeation, characterized in that, It is prepared by any one of claims 1 to 8.

10. The aluminum-diamond composite material with aluminum mesh shaping and vertical permeation according to claim 9, characterized in that, The composite material contains a three-dimensional skeleton structure made of aluminum mesh, and the diamond particles are distributed in this skeleton structure; the porosity of the composite material is ≤5%, and the thermal conductivity is ≥600 W / (m·K).

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