Preparation method of ceramic / metal-based composite material with net-shaped structure

Abstract

The invention relates to a preparation method of a ceramic / metal composite material, in particular to a preparation method of a reticular structure ceramic / metal matrix composite material. The invention aims to solve the problems of easy damage and weak interface of a reticular structure reinforcement body of a reticular structure reinforcement body / metal matrix composite material. The preparation method comprises the following steps: forming a matrix by using prefabricated metal powder, wetting and filling pores of the matrix with a liquid ceramic precursor to form a net-shaped structure, and performing in-situ ceramization to obtain a net-shaped structure ceramic reinforcement; the prepared reticular structure ceramic reinforcement is generated in situ by a precursor infiltrating into pores, and the formation and sintering processes of the reticular structure ceramic reinforcement are synchronously performed, so that the problems that wetting cannot be performed at low pressure and a skeleton is damaged at high pressure in the existing preparation process are avoided. The reticular structure ceramic / metal-based composite material has good interface bonding, reinforcing phase distribution uniformity and structure precision designability, the comprehensive performance of the material is improved, and the reticular structure ceramic / metal-based composite material has good expandability and engineering prospects.

Description

TECHNICAL FIELD

[0001] The present application relates to a kind of ceramic / metal composite material preparation method. BACKGROUND

[0002] The reticular structure reinforced metal matrix composite is a kind of structure-function integrated material with important application prospect. Among them, the three-dimensional continuous network (such as ceramic network, intermetallic compound network, carbon material network, etc.) with high strength and high modulus is used as the reinforcing phase, and is combined with metal or alloy matrix to form the composite. This configuration aims to combine the excellent performance (such as high strength, high hardness, high temperature resistance) of the reinforcing phase with the good plasticity, thermal and electrical conductivity of the metal matrix, so as to obtain an advanced material with comprehensive performance far superior to traditional particle or short fiber reinforced metal matrix composite.

[0003] However, in the preparation and performance of the reticular structure reinforced metal matrix composite, there are the following bottlenecks, which seriously restrict its practical application. First, there is a contradiction between the preparation process and the structural integrity. In order to obtain a dense composite material, the metal liquid must be completely infiltrated and filled into the micro-pores of the three-dimensional network. If low pressure or pressureless infiltration is used, due to the poor wettability of the metal liquid to the reinforcing phase, it is difficult to spontaneously infiltrate into the micro-pores, resulting in low density of the composite material. If high pressure, high temperature or long time holding is used to promote infiltration, it is easy to cause thermal damage or mechanical damage to the brittle reinforcing network, resulting in the breakage of the network skeleton. The interface between the reinforcing phase and the metal matrix is the key channel for load transfer. At present, the metal melt has poor wettability with most high-performance reinforcing materials, and the interface is mainly combined directly, with weak bonding force. In the high temperature environment of preparation, harmful interfacial reaction between metal and reinforcing phase is easy to occur, resulting in interfacial debonding and early failure of the material before reaching the theoretical strength.

[0004] In summary, the existing reticular structure reinforced metal matrix composite, due to the damage of the preparation process to the reinforcing network structure and the interface bonding problem, etc., the theoretical high performance advantage is difficult to be fully realized in practice. Therefore, it is urgent to find a new type of composite material and its preparation method which can realize the complete reinforcing network structure and strong interface bonding at the same time. SUMMARY

[0005] The present application is to solve the problem of easy damage of the reticular structure reinforcing phase and weak interface between the reinforcing phase and the metal matrix in the preparation process of the reticular structure reinforced metal matrix composite, and a reticular structure ceramic / metal matrix composite material preparation method is proposed.

[0006] The preparation method of the reticular structure reinforced metal matrix composite of the present application is carried out according to the following steps:

[0007] I. Raw material preparation

[0008] weighing the metal matrix powder and the liquid ceramic precursor;

[0009] the liquid ceramic precursor is one or a combination of polycarbosilane, polysilazane, polyborosilazane;

[0010] II. Preparation of porous metal preform

[0011] The metal matrix powder is loaded into a mold for cold pressing to obtain a porous metal preform with a porosity of 5-40%. After cold pressing of the metal matrix powder, the porosity of the preform is designed by pre-determined displacement of the lower press, and the porosity value can be determined by the mass and height of the preform to prepare a preform with a certain porosity. The preform obtained by cold pressing forms a uniform and interconnected pore network, which lays a structural foundation for subsequent uniform infiltration of the precursor;

[0012] III. Network preform of ceramic precursor

[0013] The liquid ceramic precursor is injected from the upper opening of the mold containing the porous metal preform, and then the pressure head is used to apply pressure to the liquid ceramic precursor for infiltration, so that the liquid ceramic precursor infiltrates the porous metal preform to obtain a ceramic precursor / metal powder composite. Since the pores in the porous metal preform are through holes, and the liquid ceramic precursor has good wettability to the metal powder, the liquid ceramic precursor can fully fill the pores of the preform through capillary action and pressure. The structure of the ceramic precursor in the ceramic precursor / metal powder composite is the same as the pore structure of the preform, which is a three-dimensional network structure;

[0014] The infiltration process is as follows: the liquid ceramic precursor is pressurized to 10-100 MPa at a pressurization speed of 0.1-10 mm / min and is kept at pressure for 10-30 min;

[0015] IV. In-situ reaction of ceramic precursor

[0016] The ceramic precursor / metal powder composite is placed in a heating furnace for low-temperature solidification and high-temperature ceramicization to obtain a ceramic / metal powder composite. During the low-temperature solidification stage, the liquid ceramic precursor undergoes crosslinking and solidification, changes from a liquid state to a solid polymer network, and forms a three-dimensional network structure to prevent deformation under subsequent high temperature. During the subsequent high-temperature ceramicization process, the liquid ceramic precursor undergoes ceramicization and in-situ conversion into a three-dimensional continuous ceramic network composed of SiC, Si3N4, BN or their composite ceramic phases. At high temperature, the metal elements in the metal matrix and the adjacent ceramic precursor decomposition products undergo a controlled diffusion reaction, and a transition interface layer containing compounds such as Al4C3 and AlN is generated in-situ at the interface between the metal particles and the newly formed ceramic network.

[0017] The low-temperature curing process used is: under a protective atmosphere, heating at a rate of 1-5°C / min to 100-300°C, and holding for 1-3 hours;

[0018] The high-temperature ceramicization process used is: under a protective atmosphere, heating at a rate of 1-5°C / min to 800-1300°C, and holding for 1-3 hours;

[0019] V. Densification of the composite material

[0020] The ceramic / metal powder composite is subjected to densification treatment by hot pressing or rolling to obtain a reticular structure ceramic / metal matrix composite material; during the densification of the composite material, the metal matrix undergoes thermal plastic flow to fill the residual micropores, and finally a metal matrix composite material with high density, strong interface bonding and uniform distribution of three-dimensional ceramic network is obtained.

[0021] Principles and beneficial effects of the application:

[0022] 1. The application innovates a new reticular structure ceramic / metal matrix composite material preparation method. The prior art uses a reticular structure ceramic reinforcement body to be prepared first, and then the pores of the reticular structure ceramic reinforcement body are filled by infiltration. In the process of infiltrating the aluminum liquid, the reinforcement body framework is easily washed away, causing damage to the reticular structure ceramic reinforcement body, and there is a contradiction between the preparation process and the structural integrity. The application first uses a pre-prepared metal powder to form a matrix, then a liquid ceramic precursor is used to wet and fill the pores of the matrix to form a reticular structure, and then in-situ ceramicization is performed to obtain a reticular structure ceramic reinforcement body. The reticular structure ceramic reinforcement body prepared by the application is generated in-situ by infiltrating the pores, and the formation of the reticular structure ceramic reinforcement body is synchronized with the sintering process, avoiding the problem of low pressure wetting and high pressure damage to the framework in the existing preparation process. The reticular structure ceramic reinforcement body prepared by the application is not a complete rigid body, and the continuous network framework is composed of separated small particles. In the process of densification thermal deformation, the separated small particles can flow together with the matrix, so that the composite material formed by the application can be further densified by thermal deformation, without causing damage to the reticular structure ceramic reinforcement body.

[0023] 2. The reticular structure ceramic / metal matrix composite material prepared by the application has good interface bonding. The ceramic formed by the ceramic precursor can react with the metal matrix to a certain extent, thereby forming a good interface bonding. The structure generated by the in-situ reaction is a gradient interface layer of metal-intermetallic compound-ceramic layer (such as Al-AlN-Si3N4), which establishes a strong chemical bond between the ceramic reinforcement phase and the metal matrix. The interface bonding strength is much higher than that of traditional mechanical bonding or weak reaction bonding, and the strong chemical bonding interface ensures the load transfer effect.

[0024] 3. This invention ensures the uniformity of the reinforcing phase distribution and the precise designability of the structure. The excellent flowability of the liquid precursor ensures uniform distribution within the submicron-level pores of the porous metal preform, resulting in a ceramic network that is non-agglomerated, continuously interconnected, and uniformly distributed. Furthermore, by controlling the particle size and pressing pressure of the initial metal powder, the size and volume fraction of the ceramic network in the final composite material can be precisely designed, achieving accurate design of material properties.

[0025] 4. The overall performance of the materials in this invention is significantly improved. The improved overall performance of the network-reinforced / metal matrix composite material of this invention is due to the intact ceramic precursor network, strong interfacial bonding, and uniform phase distribution. The prepared composite material exhibits comprehensive performance that is difficult to achieve with traditional processes. Under the same ceramic content, the tensile strength, elastic modulus, and fracture toughness of the network-reinforced / metal matrix composite material of this invention can be significantly improved simultaneously. At the same time, due to the presence of the three-dimensional interconnected ceramic network, the dimensional stability, wear resistance, and creep resistance of the material at high temperatures are also greatly enhanced.

[0026] This invention achieves active control of material properties at multiple scales by constructing a synergistic system of a three-dimensional continuous ceramic network, a gradient interface structure, and a uniform phase distribution. The improvement in elastic modulus stems from the efficient load transfer of the network structure; the improvement in fracture toughness is due to the reduction of damage and the increase in density; and the enhancement of dimensional stability, wear resistance, and creep resistance are respectively attributed to the network constraint, hard phase bearing capacity, and microstructure stabilization.

[0027] 5. This invention significantly expands the material selection space and simplifies the preparation process, bringing convenience to actual production. The method of this invention breaks through the strict requirements of traditional processes on the interconnected pore structure of the pre-fabricated ceramic skeleton, while relaxing the restrictions on the morphology and particle size of metal powder, making the selection of raw materials more flexible and diverse.

[0028] 6. This invention has good scalability and engineering prospects. This invention integrates the two traditionally independent complex processes of skeleton manufacturing and melt infiltration composite into three naturally connected continuous steps: preform forming, precursor infiltration and curing, and integrated sintering process. This forms a simple and efficient integrated production process, which not only reduces equipment investment and energy consumption costs, but is also particularly suitable for manufacturing near-net-shape components with complex shapes. Attached Figure Description

[0029] Figure 1 The image shows the TEM characterization of the mesh-structured ceramic / metal composite material obtained in Example 1. Detailed Implementation

[0030] The technical solution of the present invention is not limited to the specific embodiments listed below, but also includes any reasonable combination of the specific embodiments.

[0031] Specific Implementation Method 1: The preparation method of the mesh structure reinforced / metal matrix composite material in this implementation method is carried out according to the following steps:

[0032] I. Raw Material Preparation

[0033] Weigh out the metal matrix powder and the liquid ceramic precursor;

[0034] The liquid ceramic precursor is one or a combination of polycarbosilane, polysilazane, and polyboronsilazane.

[0035] II. Preparation of Porous Metal Preforms

[0036] Metal matrix powder is loaded into a mold and cold-pressed to obtain a porous metal preform with a porosity of 5-40%. After cold pressing, the porosity of the preform is designed by pressing down a predetermined displacement. The porosity value can be determined by the mass and height of the preform, thus preparing a preform with a certain porosity. A uniform and interconnected pore network is formed in the cold-pressed preform, which lays the structural foundation for the uniform infiltration of the precursor in the subsequent process.

[0037] III. Prefabrication of Ceramic Precursor Network

[0038] Liquid ceramic precursor is injected into a mold containing a porous metal preform through the top opening of the mold. Then, pressure is applied to the liquid ceramic precursor through a pressure head to impregnate it, allowing the liquid ceramic precursor to penetrate into the porous metal preform and obtain a ceramic precursor / metal powder composite. Since the pores in the porous metal preform are through-holes and the liquid ceramic precursor has good wettability to the metal powder, the liquid ceramic precursor can fully fill the pores of the preform through capillary action and pressure. The structure of the ceramic precursor in the ceramic precursor / metal powder composite is the same as the pore structure of the preform, which is a three-dimensional network structure.

[0039] The impregnation process is as follows: pressurize the liquid ceramic precursor to 10-100 MPa at a pressurization rate of 0.1-10 mm / min and hold the pressure for 10-30 min;

[0040] IV. In-situ reaction of ceramic precursors

[0041] The ceramic precursor / metal powder composite is placed in a heating furnace and subjected to low-temperature curing and high-temperature ceramicizing sequentially to obtain the ceramic / metal powder composite. During the low-temperature curing stage, the liquid ceramic precursor undergoes cross-linking and solidification, transforming from a liquid state into a solid polymer network, forming a three-dimensional network structure to prevent flow and deformation at subsequent high temperatures. Subsequently, during the high-temperature ceramicizing process, the liquid ceramic precursor undergoes a ceramicizing transformation, transforming in situ into a three-dimensional continuous ceramic network composed of SiC, Si3N4, BN, or composite ceramic phases thereof. At high temperatures, the metal elements in the metal matrix undergo a controlled diffusion reaction with the decomposition products of the adjacent ceramic precursor, generating a transition interface layer containing compounds such as Al4C3 and AlN in situ at the interface between the metal particles and the newly formed ceramic network.

[0042] The low-temperature curing process used is as follows: under a protective atmosphere, the temperature is raised to 100-300°C at a rate of 1-5°C / min, and held for 1-3 hours;

[0043] The high-temperature ceramicization process used is as follows: under a protective atmosphere, the temperature is raised to 800~1300°C at a rate of 1~5°C / min, and held for 1~3 hours;

[0044] V. Densification of Composite Materials

[0045] The ceramic / metal powder composite is densified by hot pressing or rolling to obtain a network-structured ceramic / metal matrix composite. During the densification process, the metal matrix undergoes thermoplastic flow, filling the residual micropores, and finally obtaining a metal matrix composite with high density, strong interfacial bonding, and uniform distribution of three-dimensional ceramic network.

[0046] This embodiment has the following beneficial effects:

[0047] 1. This embodiment innovates a novel method for preparing network-structured ceramic / metal matrix composites. Existing technologies involve first preparing a network-structured ceramic reinforcement and then impregnating and filling its pores. During the impregnation process with molten aluminum, the reinforcement framework is easily dispersed, causing damage to the network-structured ceramic reinforcement, resulting in a contradiction between the preparation process and structural integrity. In contrast, this embodiment first uses pre-formed metal powder to form a matrix, then uses a liquid ceramic precursor to wet and fill the matrix pores to form a network structure, followed by in-situ ceramization to obtain the network-structured ceramic reinforcement. The network-structured ceramic reinforcement prepared in this embodiment is generated in-situ from the precursor that penetrates the pores; the formation and sintering of the network-structured ceramic reinforcement occur simultaneously, avoiding the problems of insufficient wetting under low pressure and damage to the framework under high pressure in existing preparation processes. The mesh-structured ceramic reinforcement prepared in this embodiment is not a completely rigid body. The continuous network skeleton is composed of separated small particles. During the densification heat deformation process, the separated small particles can flow with the matrix. Therefore, in this embodiment, the composite material can be further densified by heat deformation without causing damage to the mesh-structured ceramic reinforcement.

[0048] 2. The network-structured ceramic / metal matrix composite material prepared in this embodiment exhibits excellent interfacial bonding. The ceramic precursor formed can undergo a certain degree of in-situ reaction with the metal matrix, thereby forming a good interfacial bond. The structure generated by the in-situ reaction is a gradient interfacial layer of metal-intermetallic compound-ceramic layer (such as Al-AlN-Si3N4), establishing a strong chemical bond between the ceramic reinforcing phase and the metal matrix. This interfacial bonding strength is much higher than that of traditional mechanical bonding or weak reactive bonding, and the strong chemical bonding interface ensures the load transfer effect.

[0049] 3. This implementation method ensures the uniformity of the reinforcing phase distribution and the precise designability of the structure. The excellent flowability of the liquid precursor ensures uniform distribution within the submicron-level pores of the porous metal preform, resulting in a ceramic network that is non-agglomerated, continuously interconnected, and uniformly distributed. Furthermore, by controlling the particle size and pressing pressure of the initial metal powder, the size and volume fraction of the ceramic network in the final composite material can be precisely designed, achieving accurate design of material properties.

[0050] 4. This embodiment achieves a breakthrough improvement in the overall performance of the material. The improved overall performance of the network-reinforced / metal matrix composite material in this embodiment is due to the intact ceramic precursor network, strong interfacial bonding, and uniform phase distribution. The prepared composite material exhibits comprehensive performance that is difficult to achieve with traditional processes. Under the same ceramic content, the tensile strength, elastic modulus, and fracture toughness of the network-reinforced / metal matrix composite material in this embodiment can be significantly improved simultaneously. At the same time, due to the presence of the three-dimensional interconnected ceramic network, the dimensional stability, wear resistance, and creep resistance of the material at high temperatures are also greatly enhanced.

[0051] This implementation achieves active control of material properties at multiple scales by constructing a synergistic system of a three-dimensional continuous ceramic network, a gradient interface structure, and a uniform phase distribution. The increase in elastic modulus stems from the efficient load transfer of the network structure; the improvement in fracture toughness benefits from the reduction of damage and the increase in density; and the enhancement of dimensional stability, wear resistance, and creep resistance comes from the network constraint, hard phase bearing capacity, and microstructure stabilization effects, respectively.

[0052] 5. This embodiment significantly expands the material selection space and simplifies the preparation process, bringing convenience to actual production. The method of this embodiment breaks through the stringent requirements of traditional processes on the interconnected pore structure of the pre-fabricated ceramic framework, while relaxing the restrictions on the morphology and particle size of metal powders, making the selection of raw materials more flexible and diverse.

[0053] 6. This implementation method has good scalability and engineering prospects. This implementation method integrates the two traditionally independent complex processes of skeleton manufacturing and melt infiltration composite into three naturally connected continuous steps: preform forming, precursor infiltration and curing, and integrated sintering process. This forms a simple and efficient integrated production process, which not only reduces equipment investment and energy consumption costs, but is also particularly suitable for manufacturing near-net-shape parts with complex shapes.

[0054] Specific Implementation Method Two: This implementation method differs from Specific Implementation Method One in that the average particle size of the metal matrix powder in step one is 1~100 μm.

[0055] Specific Implementation Method 3: This implementation method differs from Specific Implementation Method 1 or 2 in that the metal matrix powder mentioned in step 1 is aluminum, aluminum alloy, copper, copper alloy, magnesium, or magnesium alloy.

[0056] Specific Implementation Method Four: This implementation method differs from Specific Implementation Method Three in that: the aluminum alloy is one or a combination of several of the following: Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Si-Cu alloy, Al-Si-Mg alloy, Al-Cu-Mg alloy, Al-Zn-Cu alloy, Al-Zn-Mg-Cu alloy, Al-Be alloy, Al-Li alloy, and Al-Si-Cu-Mg alloy; the copper alloy is Cu-Zn alloy, Cu-Sn alloy, Cu-Al alloy, Cu-Be alloy, or Cu-N alloy. The alloy is one or a combination of several of the following: i alloy, Cu-Ni-Zn alloy, Cu-Cr alloy, Cu-Zr alloy, Cu-Cr-Zr alloy, Cu-Fe alloy, Cu-Ag alloy, Cu-Mg alloy, or Cu-Si alloy; the magnesium alloy is one or a combination of several of the following: Mg-Al alloy, Mg-Zn alloy, Mg-Mn alloy, Mg-RE alloy, Mg-Li alloy, Mg-Ag alloy, Mg-Th alloy, Mg-Ca alloy, Mg-Sr alloy, Mg-Si alloy, Mg-Sn alloy, or Mg-Y alloy.

[0057] Specific Implementation Method 5: This implementation method differs from one of the specific implementation methods 1 to 4 in that the degree of polymerization of the liquid ceramic precursor described in step 1 is 300~10000.

[0058] Specific Implementation Method Six: This implementation method differs from Specific Implementation Methods One to Five in that: the side chain functional groups of the liquid ceramic precursor in step one are one or a combination of several of the following: hydrogen-based, alkyl-based, alkenyl-based, oxygen-containing, sulfur-containing, phosphorus-containing, and halogen-containing functional groups.

[0059] Specific Implementation Method Seven: This implementation method differs from one of the specific implementation methods one to six in that the protective atmosphere described in step four is a nitrogen atmosphere, an argon atmosphere, or a vacuum atmosphere.

[0060] Specific Implementation Method Eight: This implementation method differs from one of the specific implementation methods one to seven in that the cold pressing process described in step two is as follows: at room temperature, the pressurization rate is 0.1~10mm / min, 0~300MPa pressure is applied to the metal powder, and the pressure is maintained for 10~30min.

[0061] Specific Implementation Method Nine: This implementation method differs from Specific Implementation Methods One through Eight in that the hot pressing process described in step five is performed at a pressure of 50~200MPa and a temperature of 0.6T. m ~1.2T m Under heat and pressure, maintain the temperature for 10-60 minutes; the T m It is the melting point of the metal matrix.

[0062] Specific Implementation Method Ten: This implementation method differs from Specific Implementation Methods One to Nine in that the rolling process described in step five is as follows: at a temperature of 0.6T... m ~1.2T m The deformation per rolling pass is 10-30%, and the total deformation is 10-80%.

[0063] Example 1

[0064] The preparation method of the mesh structure reinforced / metal matrix composite material in this embodiment is carried out according to the following steps:

[0065] I. Raw Material Preparation

[0066] Weigh out the metal matrix powder and the liquid ceramic precursor;

[0067] The average particle size of the metal matrix powder is 10 μm;

[0068] The metal matrix powder is aluminum;

[0069] The liquid ceramic precursor is polysilazane; the degree of polymerization is 300, and the side chain functional group of the liquid ceramic precursor is methyl.

[0070] II. Preparation of Porous Metal Preforms

[0071] Metal matrix powder is loaded into a mold and cold-pressed to obtain a porous metal preform with a porosity of 20%.

[0072] The cold pressing process is as follows: at room temperature, the pressurization rate is 5 mm / min, a pressure of 60 MPa is applied to the metal powder, and the pressure is held for 15 min;

[0073] III. Prefabrication of Ceramic Precursor Network

[0074] Liquid ceramic precursor is injected into the mold from the top opening of the mold containing porous metal preform, and then pressure is applied to the liquid ceramic precursor through the pressure head to impregnate it, so that the liquid ceramic precursor penetrates into the porous metal preform to obtain a ceramic precursor / metal powder composite.

[0075] The impregnation process is as follows: pressurize the liquid ceramic precursor to 50MPa at a pressurization rate of 2mm / min and hold the pressure for 30min;

[0076] IV. In-situ reaction of ceramic precursors

[0077] The ceramic precursor / metal powder composite is placed in a heating furnace and subjected to low-temperature curing and high-temperature ceramization in sequence to obtain the ceramic / metal powder composite.

[0078] The low-temperature curing process used is as follows: under a protective atmosphere, the temperature is increased to 200°C at a rate of 5°C / min and held for 1 hour;

[0079] The high-temperature ceramicization process used is as follows: under a protective atmosphere, the temperature is raised to 800°C at a rate of 5°C / min and held for 2 hours;

[0080] The protective atmosphere is a nitrogen atmosphere;

[0081] V. Densification of Composite Materials

[0082] A network-structured ceramic / metal matrix composite material was obtained by densifying the ceramic / metal powder composite material through hot pressing.

[0083] The hot pressing process is as follows: holding the temperature and pressure at 50 MPa and 500°C for 20 minutes.

[0084] Figure 1 The image shows the TEM characterization of the network-structured ceramic / metal composite material obtained in Example 1; from Figure 1 As can be seen, the composite material is relatively dense without obvious pores, and the nitrogen element ceramic transformed from polysilazane is dispersed in the matrix in a three-dimensional network. This embodiment successfully constructed a complete, continuous, and uniformly distributed ceramic reinforcement network within an aluminum alloy matrix. Microstructural characterization confirmed that the ceramic phase exists in a three-dimensional, interconnected morphology within the matrix, without obvious agglomeration or segregation defects, and forms a uniformly thick and tightly bonded interfacial transition layer with the matrix. Material performance testing results show that the prepared composite material exhibits significant improvements in several key indicators: at a ceramic content of 15 vol%, the room temperature tensile strength reaches 523 MPa; high-temperature performance testing shows that its tensile strength remains above 320 MPa at 300℃, nearly twice that of the matrix alloy. These results fully demonstrate the effectiveness of this invention in solving long-standing technical challenges such as the uniformity of reinforcement phase dispersion, interfacial bonding strength, and high-temperature stability through the in-situ transformation of the ceramic skeleton from the ceramic precursor.

Claims

1. A method for preparing a mesh-structured reinforced / metal matrix composite material, characterized in that: The preparation method of the network structure reinforced / metal matrix composite material is carried out according to the following steps: I. Raw Material Preparation Weigh out the metal matrix powder and the liquid ceramic precursor; The liquid ceramic precursor is one or a combination of polycarbosilane, polysilazane, and polyboronsilazane. II. Preparation of Porous Metal Preforms Metal matrix powder is loaded into a mold and cold-pressed to obtain a porous metal preform with a porosity of 5-40%. III. Prefabrication of Ceramic Precursor Network Liquid ceramic precursor is injected into the mold from the top opening of the mold containing porous metal preform, and then pressure is applied to the liquid ceramic precursor through the pressure head to impregnate it, so that the liquid ceramic precursor penetrates into the porous metal preform to obtain a ceramic precursor / metal powder composite. The impregnation process is as follows: pressurize the liquid ceramic precursor to 10-100 MPa at a pressurization rate of 0.1-10 mm / min and hold the pressure for 10-30 min; IV. In-situ reaction of ceramic precursors The ceramic precursor / metal powder composite is placed in a heating furnace and subjected to low-temperature curing and high-temperature ceramization in sequence to obtain the ceramic / metal powder composite. The low-temperature curing process used is as follows: under a protective atmosphere, the temperature is raised to 100-300°C at a rate of 1-5°C / min, and held for 1-3 hours; The high-temperature ceramicization process used is as follows: under a protective atmosphere, the temperature is raised to 800~1300°C at a rate of 1~5°C / min, and held for 1~3 hours; V. Densification of Composite Materials Densification of ceramic / metal powder composites is achieved by hot pressing or rolling to obtain a network-structured ceramic / metal matrix composite material.

2. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The average particle size of the metal matrix powder in step one is 1~100 μm.

3. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The metal matrix powder mentioned in step one is aluminum, aluminum alloy, copper, copper alloy, magnesium, or magnesium alloy.

4. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 3, characterized in that: The aluminum alloy is one or a combination of several of the following: Al-Si alloy, Al-Cu alloy, Al-Mg alloy, Al-Si-Cu alloy, Al-Si-Mg alloy, Al-Cu-Mg alloy, Al-Zn-Cu alloy, Al-Zn-Mg-Cu alloy, Al-Be alloy, Al-Li alloy, and Al-Si-Cu-Mg alloy; the copper alloy is one or a combination of several of the following: Cu-Zn alloy, Cu-Sn alloy, Cu-Al alloy, Cu-Be alloy, Cu-Ni alloy, Cu-Ni-Zn alloy, Cu-Cr alloy, Cu-Zr alloy, Cu-Cr-Zr alloy, Cu-Fe alloy, Cu-Ag alloy, Cu-Mg alloy, or Cu-Si alloy; and the magnesium alloy is one or a combination of several of the following: Mg-Al alloy, Mg-Zn alloy, Mg-Mn alloy, Mg-RE alloy, Mg-Li alloy, Mg-Ag alloy, Mg-Th alloy, Mg-Ca alloy, Mg-Sr alloy, Mg-Si alloy, Mg-Sn alloy, or Mg-Y alloy.

5. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The degree of polymerization of the liquid ceramic precursor mentioned in step one is 300~10000.

6. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The side chain functional groups of the liquid ceramic precursor in step one are one or a combination of several of the following: hydrogen-based, alkyl-based, alkenyl-based, oxygen-containing, sulfur-containing, phosphorus-containing, and halogen-containing functional groups.

7. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The protective atmosphere described in step four is a nitrogen atmosphere, an argon atmosphere, or a vacuum atmosphere.

8. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The cold pressing process described in step two is as follows: at room temperature, the pressurization rate is 0.1~10mm / min, 0~300MPa pressure is applied to the metal powder, and the pressure is maintained for 10~30min.

9. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The hot pressing process described in step five is as follows: The pressure is 50~200MPa, and the temperature is 0.6T. m ~1.2T m Under heat and pressure, maintain the temperature for 10-60 minutes; the T m It is the melting point of the metal matrix.

10. The method for preparing the mesh-structured reinforced / metal matrix composite material according to claim 1, characterized in that: The rolling process described in step five is as follows: at a temperature of 0.6T... m ~1.2T m The deformation per rolling pass is 10-30%, and the total deformation is 10-80%.

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