Ceramic embedded metal matrix composite and method of manufacture

Abstract

The application discloses a kind of ceramic embedded metal matrix composites and preparation method, belong to ceramic metal composite material technical field, the composite material includes matrix material and dispersedly embedded complex phase ceramic peg in it, complex phase ceramic peg is made by boron carbide powder, zirconium carbide powder, binder and silicon alloy by reaction melt infiltration process, silicon alloy is hafnium silicon alloy and silicon zirconium alloy composition.Form semi-solid slurry by melt cooling stirring when preparing, after adding complex phase ceramic peg stirring dispersion, temperature casting, after normalizing and tempering treatment, product is obtained.Compared with prior art, ceramic peg is dispersedly embedded in matrix, solves the problem that traditional lining ceramic is easy to fall off, outer layer ceramic is easy to crack;Meanwhile, the density of ceramic peg is improved, synergistic strengthening effect is formed by compounding, and the bending strength and wear resistance of the composite material are significantly improved by optimizing the ratio.

Description

Technical Field

[0001] This invention relates to the field of ceramic-metal composite materials technology, and in particular to a ceramic-embedded metal matrix composite material and its preparation method. Background Technology

[0002] Ceramic particle-reinforced metal matrix composites combine the high toughness of the metal matrix with the high hardness and wear resistance of the ceramic particles, making them promising for applications in harsh working conditions such as metallurgy, mining, and building materials. Uniformly dispersing ceramic particles within the metal matrix is ​​crucial for preparing these materials. However, the wettability between ceramic particles and molten metal is generally poor. Furthermore, if the ceramic particles themselves have low density and numerous internal pores, the mechanical and wear-resistant properties of the composite material will be severely affected. Therefore, achieving uniform dispersion of ceramic particles within the metal matrix while simultaneously increasing their density is a pressing technical challenge that needs to be addressed.

[0003] Patent CN115961172A discloses a nano-ceramic particle-reinforced metal matrix composite material and its preparation method. This method involves introducing a gaseous ceramic precursor into a liquid metal to decompose and generate nano-ceramic particles. However, the ceramic particles generated by this method are very small and not suitable for densifying micron-sized ceramic particles. Patent CN119874377A discloses a silicon carbide fiber-reinforced ceramic matrix composite material and its preparation method, using a reactive melt infiltration process to prepare a silicon-based multiphase ceramic matrix. However, this method is designed for fiber-reinforced systems, is complex, and not applicable to particle-reinforced metal matrix composites. Patent CN117488130A discloses a method for preparing ceramic particle-reinforced metal matrix composites, utilizing the properties of supercritical metal fluids to disperse ceramic particles. However, this method requires extremely sophisticated equipment and is only applicable to low-melting-point metals such as magnesium; it may not be feasible for steel matrices.

[0004] In existing technologies, insufficient density of ceramic particles, limited reinforcing effect of single borides, and improper alloy ratios leading to unoptimized performance are the main problems restricting the improvement of the overall performance of ceramic particle-reinforced metal matrix composites. Therefore, there is an urgent need to develop a ceramic particle-reinforced metal matrix composite material and its preparation method that can improve the density of ceramic particles, achieve synergistic reinforcement through alloy compounding, and is simple to process and suitable for steel matrices. Summary of the Invention

[0005] To address the shortcomings of existing technologies, this invention aims to provide a ceramic-embedded metal matrix composite material and its preparation method.

[0006] To achieve the above-mentioned objectives, the present invention adopts the following technical solution:

[0007] A ceramic-embedded metal matrix composite material, comprising a matrix and multiphase ceramic nails dispersedly embedded in the matrix;

[0008] The substrate is at least one of carbon steel, stainless steel, and copper.

[0009] The multiphase ceramic nail comprises the following raw materials: boron carbide powder, zirconium carbide powder, binder, and silicon-containing alloy.

[0010] The silicon-containing alloy is at least one of the following: silicon hafnium alloy, silicon tantalum alloy, silicon molybdenum alloy, silicon zirconium alloy, silicon titanium alloy, silicon niobium alloy, and silicon chromium alloy.

[0011] A method for preparing a ceramic-embedded metal matrix composite material is as follows:

[0012] Step 1: Heat the base material to melt it. After the base material has completely melted into liquid metal, remove the surface slag to obtain the molten metal. Then cool and stir to form a semi-solid metal slurry.

[0013] Step 2: Under continuous stirring, the multiphase ceramic nails are gradually added to the semi-solid metal slurry obtained in Step 1. After the addition is completed, stirring is continued. Then the slurry is heated to obtain a metal melt containing dispersed multiphase ceramic nails.

[0014] Step 3: Pour the molten metal obtained in Step 2 smoothly into the preheated metal mold, so that the molten metal completely fills the cavity; after casting, let the entire mold cool naturally in the air.

[0015] Step 4: After the casting has cooled, open the mold and remove the cast billet; cut off the sprue and riser on the cast billet, remove the oxide scale on the surface of the casting, and sandblast the surface of the billet to obtain the cast billet of ceramic embedded metal matrix composite material; normalize the cleaned billet; and then temper the billet to obtain ceramic embedded metal matrix composite material.

[0016] The heating and melting mentioned in step 1 refers to heating to 1500-1600℃ for melting.

[0017] The cooling and stirring mentioned in step 1 involves cooling the molten metal to 1450-1480℃ and applying mechanical stirring at a speed of 100-300 rpm.

[0018] The amount of multiphase ceramic nails added in step 2 is 10-20% of the mass of the semi-solid metal slurry.

[0019] The temperature increase mentioned in step 2 is to raise the temperature to 1500-1650℃.

[0020] The metal mold mentioned in step 3 is preheated to 150-300℃.

[0021] The natural cooling mentioned in step 3 refers to cooling to below 300°C.

[0022] The normalizing treatment described in step 4 involves heating to 800-900℃, holding at that temperature for 1-3 hours, and then cooling in still air to perform the normalizing treatment.

[0023] The tempering process described in step 4 involves heating the billet to 500-700℃, holding it at that temperature for 1-3 hours, and then air-cooling it for tempering.

[0024] The preparation method of the multiphase ceramic nail is as follows:

[0025] S1. Ball mill boron carbide powder, zirconium carbide powder and binder to obtain uniform composite powder; put the dried and sieved composite powder into a mold and press it into shape to obtain ceramic nail green body;

[0026] S2. The ceramic nail green body obtained in step S1 is completely embedded with a silicon-containing alloy; the reaction melt infiltration is carried out; after the reaction is completed, the sample is cooled to room temperature in the furnace, and the sample is taken out. It is first acid-washed and then ultrasonically cleaned to obtain the multiphase ceramic nail.

[0027] The mass ratio of boron carbide powder, zirconium carbide powder and binder is 20-30:5-15:0.5-2.

[0028] The adhesive is polyvinyl butyral.

[0029] The ball milling process involves using anhydrous ethanol as the medium and zirconia balls as the grinding media, and mixing at a speed of 100-300 rpm for 10-30 hours.

[0030] The drying and sieving process involves passing the material through a 200-mesh sieve.

[0031] The pressing process involves pressing a cylindrical ceramic nail blank with a diameter of 1-3 mm and a length of 2-5 mm under a molding pressure of 100-300 MPa.

[0032] The silicon-containing alloy is at least one of the following: silicon hafnium alloy, silicon tantalum alloy, silicon molybdenum alloy, silicon zirconium alloy, silicon titanium alloy, silicon niobium alloy, and silicon chromium alloy.

[0033] Preferably, the silicon-containing alloy is composed of a silicon-hafnium alloy and a silicon-zirconium alloy in a mass ratio of 1-5:1.

[0034] More preferably, the silicon-containing alloy is composed of a silicon-hafnium alloy and a silicon-zirconium alloy in a mass ratio of 3:1.

[0035] The amount of silicon alloy used in the embedding is 3-5 times the mass of the ceramic nail green body.

[0036] The reaction melt infiltration is achieved by heating to 1400-1500℃ at a rate of 5-10℃ / min and holding at this temperature for 60-180 minutes.

[0037] The pickling is a mixed acid pickling prepared by mixing 65%-68% nitric acid and 35%-42% hydrofluoric acid in a volume ratio of 6-10:1.

[0038] The ultrasonic cleaning process involves immersing the sample in water using an ultrasonic frequency of 20-60 kHz and a power density of 0.5-1 W / cm². 2 Wash for 5-10 minutes at room temperature.

[0039] In the preparation of metal matrix composites, the insufficient density of ceramic nails when added to the metal melt severely weakens their reinforcing effect. This invention pre-prepares multiphase ceramic nails using a reactive melt infiltration process. A silicon-containing alloy is melted and infiltrated into the green body at high temperature, reacting in situ with boron carbide to generate silicon carbide and metal borides, filling the pores within the particles and obtaining a highly dense ceramic reinforcement. The densified ceramic nails are then added to the metal matrix via a semi-solid stirring method to achieve uniform dispersion, thus solving the problems of low density and poor reinforcing effect of the ceramic nails.

[0040] The types of metal borides generated by using a single silicon-containing alloy are limited, resulting in limited improvement on the performance of ceramic nails. This invention proposes to use a combination of silicon-hafnium alloy and silicon-zirconium alloy. The hafnium boride and zirconium boride generated during the melting and infiltration process belong to the hexagonal crystal system and have well-matched lattice parameters, which can form a continuous solid solution. Through the solid solution strengthening effect, the hardness and density of ceramic nails are significantly improved, thereby solving the problem of the low upper limit of the strengthening effect of a single boride.

[0041] Based on the established synergistic effect of silicon-hafnium and silicon-zirconium alloys, the ratio of these two alloys directly affects the lattice distortion, phase stability, and the balance between hardness and toughness of the solid solution. This invention optimizes the mass ratio of silicon-hafnium alloy to silicon-zirconium alloy to a specific proportion, achieving an optimal balance between lattice distortion and phase stability in the solid solution. While maintaining high hardness, it enhances grain boundary bonding and refines grains, achieving a synergistic improvement in hardness and toughness. This solves the problem of inadequate performance maximization caused by improper ratios in composite formulations.

[0042] Compared with the prior art, the present invention has the following beneficial technical effects:

[0043] 1) This invention uses a reactive melt infiltration process to pre-prepare multiphase ceramic nails. It utilizes silicon-containing alloy melt infiltration to fill the internal pores of the green body and generate silicon carbide and metal boride in situ, which significantly improves the density of the ceramic nails and solves the problems of internal porosity and poor reinforcement effect of traditional ceramic nails.

[0044] 2) This invention uses a combination of silicon hafnium alloy and silicon zirconium alloy as a silicon-containing alloy. The two alloys generate borides belonging to the same hexagonal crystal system and form a continuous solid solution. Through the solid solution strengthening effect, the hardness and density of the ceramic nails are significantly higher than those of the scheme using a single silicon-containing alloy.

[0045] 3) This invention optimizes the ratio of silicon hafnium alloy to silicon zirconium alloy to the optimal range, so that the degree of lattice distortion and phase stability of the solid solution are balanced. While maintaining high hardness, it enhances the grain boundary bonding force and refines the grains, thus achieving a synergistic improvement in the hardness and toughness of ceramic nails. Detailed Implementation

[0046] Some material sources or parameters:

[0047] Carbon steel matrix material: carbon content 0.42%-0.50%, silicon content 0.17%-0.37%, manganese content 0.50%-0.80%, density 7.85 g / cm³ 3 The solidus is about 1425℃ and the liquidus is about 1500℃.

[0048] Boron carbide powder: molecular formula B4C, average particle size 3μm, melting point 2450℃.

[0049] Zirconium carbide powder: molecular formula ZrC, average particle size 8μm, melting point 3540℃.

[0050] Polyvinyl butyral adhesive: Brand: Butvar ® B-79, Manufacturer: Eastman Chemical Company, USA.

[0051] Silicon-hafnium alloy: The main component is silicon, containing hafnium. The mass ratio of silicon to hafnium is 90:10, and the average particle size of the powder is 1-3μm.

[0052] Silicon-tantalum alloy: The main component is silicon, containing tantalum element, with a silicon to tantalum mass ratio of 90:10, and the average particle size of the powder is 1-3μm.

[0053] Silicon-molybdenum alloy: The main component is silicon, containing molybdenum. The mass ratio of silicon to molybdenum is 90:10, and the average particle size of the powder is 1-3μm.

[0054] Silicon-zirconium alloy: The main component is silicon, containing zirconium, with a silicon to zirconium mass ratio of 90:10, and the average particle size of the powder is 1-3μm.

[0055] Silicon-titanium alloy: The main component is silicon, containing titanium. The mass ratio of silicon to titanium is 90:10, and the average particle size of the powder is 1-3μm.

[0056] Silicon-niobium alloy: The main component is silicon, containing niobium. The mass ratio of silicon to niobium is 90:10, and the average particle size of the powder is 1-3μm.

[0057] Silicon-chromium alloy: The main component is silicon, containing chromium. The mass ratio of silicon to chromium is 90:10, and the average particle size of the powder is 1-3μm.

[0058] In the embodiments and comparative examples of this invention, the raw materials are all commercially available products or products prepared by conventional methods.

[0059] Example 1

[0060] A method for preparing a ceramic-embedded metal matrix composite material is as follows:

[0061] Step 1: Load the carbon steel matrix material into a medium-frequency induction melting furnace and heat it to 1550℃ for melting. After the matrix material is completely melted into liquid metal, remove the surface slag to obtain a clean metal melt. Then, cool the metal melt to 1480℃ and apply mechanical stirring at a stirring speed of 200 rpm to make the metal melt enter a semi-solid state, forming a semi-solid metal slurry with high viscosity and high shear force.

[0062] Step 2: Under continuous stirring, gradually add the multiphase ceramic nails to the semi-solid metal slurry obtained in Step 1. The amount of multiphase ceramic nails added is 15% of the mass of the semi-solid metal slurry. After the addition is completed, continue stirring for 20 minutes to fully disperse and evenly distribute the multiphase ceramic nails in the semi-solid metal slurry. Then, rapidly heat the slurry to 1600℃ to obtain a metal melt containing dispersed multiphase ceramic nails.

[0063] Step 3: Pour the molten metal obtained in Step 2 smoothly into a metal mold that has been preheated to 200°C, so that the molten metal completely fills the cavity; after casting, allow the entire mold to cool naturally in the air to below 300°C.

[0064] Step 4: After the casting cools to below 300℃, open the mold and remove the cast billet; cut off the sprue and riser on the cast billet, remove the oxide scale and coating layer on the surface of the casting, and sandblast the surface of the billet to obtain the cast billet of ceramic embedded metal matrix composite material; heat the cleaned billet to 860℃, hold it for 2 hours, and then cool it in still air for normalizing treatment; then heat the billet to 600℃, hold it for 1.5 hours, and then air cool it for tempering treatment to obtain ceramic embedded metal matrix composite material.

[0065] The preparation method of the multiphase ceramic nail is as follows:

[0066] S1. Weigh boron carbide powder, zirconium carbide powder, and polyvinyl butyral binder at a mass ratio of 25:10:1. Place the weighed powder and binder together in a ball mill and use anhydrous ethanol as the medium and zirconium oxide balls as the grinding media. Ball mill the mixture at 200 rpm for 16 hours to obtain a uniform composite powder. After drying and passing through a 200-mesh sieve, load the composite powder into a mold and press it into a cylindrical ceramic nail green body with a diameter of 2 mm and a length of 3 mm under a molding pressure of 200 MPa.

[0067] S2. Place the ceramic nail green body obtained in step S1 into a graphite crucible, and completely embed the green body with a silicon-containing alloy. The amount of silicon-containing alloy is four times the mass of the ceramic nail green body. Then, place the graphite crucible into a vacuum melting furnace and heat it to 1450°C at a rate of 8°C / min. Hold it at this temperature for 120 minutes to allow the reaction melt to penetrate. After the holding time, cool the sample to room temperature with the furnace, remove the sample, and first acid-wash it, then ultrasonically clean the surface to remove residual alloy. The acid washing is done with a mixed acid solution of 66% nitric acid and 40% hydrofluoric acid at a volume ratio of 8:1. The ultrasonic cleaning is done by immersing the sample in water using an ultrasonic frequency of 40kHz and a power density of 0.8W / cm³. 2 After cleaning at room temperature for 8 minutes, the multiphase ceramic nails are obtained.

[0068] The silicon-containing alloy is a silicon-hafnium alloy.

[0069] Example 2

[0070] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon alloy in the preparation method of the multiphase ceramic nail is a silicon-tantalum alloy.

[0071] Example 3

[0072] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is a silicon-molybdenum alloy.

[0073] Example 4

[0074] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is a silicon-zirconium alloy.

[0075] Example 5

[0076] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is a silicon-titanium alloy.

[0077] Example 6

[0078] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is a silicon-niobium alloy.

[0079] Example 7

[0080] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is a silicon-chromium alloy.

[0081] Example 8

[0082] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is composed of silicon hafnium alloy and silicon zirconium alloy in a mass ratio of 1:1.

[0083] Example 9

[0084] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is composed of silicon hafnium alloy and silicon molybdenum alloy in a mass ratio of 1:1.

[0085] Example 10

[0086] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is composed of silicon hafnium alloy and silicon zirconium alloy in a mass ratio of 3:1.

[0087] Example 11

[0088] The preparation method of a ceramic embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy in the preparation method of the multiphase ceramic nail is composed of silicon hafnium alloy and silicon zirconium alloy in a mass ratio of 5:1.

[0089] Comparative Example 1

[0090] The preparation method of a ceramic-embedded metal matrix composite material is basically the same as that in Example 1, except that the silicon-containing alloy is not added in the preparation method of the multiphase ceramic nail.

[0091] Test Example 1

[0092] Bending strength test:

[0093] Following the preparation methods of the various embodiments and comparative examples, ceramic-embedded metal matrix composite specimens with dimensions of 80mm × 10mm × 8mm were prepared, with three specimens per group. The specimens were placed on a universal testing machine, and any 80mm × 10mm original surface of the specimen was used as the tension surface. The three-point bending method was employed for testing, with two rollers of 10mm diameter and a fixed span of 80mm. The loading roller, with a diameter of 10mm, was positioned directly above the midpoint of the span, and the loading rate was 0.5mm / min. The maximum load F (N) at the moment of specimen fracture was recorded. The flexural strength was calculated using the following formula:

[0094] σ=(3×F×L) / (2×b×h 2 )

[0095] In the formula:

[0096] σ: Bending strength, in MPa;

[0097] F: The maximum load at which the specimen breaks, in N;

[0098] L: Span, which is the distance between the centers of the two rollers, and is 80mm;

[0099] b: Sample width, 10mm;

[0100] h: Sample thickness, i.e., the original thickness of the casting, is 8 mm;

[0101] The arithmetic mean of the bending strength of the three specimens is taken as the bending strength value of the group.

[0102] The test results are shown in Table 1.

[0103] Table 1

[0104]

[0105] Test Example 2

[0106] Abrasion resistance test:

[0107] Following the preparation methods of each embodiment and comparative example, ceramic-embedded metal matrix composite material samples with dimensions of 10mm×10mm×8mm were prepared, with 3 samples per group, serving as wear samples. A room temperature dry friction test was conducted using a pin-disc friction and wear testing machine, with SiC ceramic balls of 6mm diameter as the wear material, a normal load of 50N applied, a spindle speed of 200rpm, and a wear time of 30min. Before and after the test, the mass of the samples was weighed using an analytical balance with an accuracy of 0.1mg, and the mass wear amount was calculated. The arithmetic mean of the 3 samples was taken as the wear amount of the group.

[0108] The relevant test data are summarized in Table 2.

[0109] Table 2

[0110]

[0111] In Comparative Example 1, without the addition of silicon-containing alloys, the ceramic nail green body underwent only high-temperature sintering at 1450℃. The boron carbide and zirconium carbide powders achieved limited bonding primarily through solid-phase diffusion, leaving numerous pores within the particles and resulting in low density. Consequently, these pores acted as crack initiation points under bending loads, leading to low bending strength. During wear, the porous structure exacerbated abrasive grain spalling, resulting in poor wear resistance. Examples 1 to 7 employed different silicon-containing alloys for reactive melt infiltration. Molten silicon and alloying elements infiltrated into the green body pores under capillary force. Silicon and boron carbide underwent an in-situ reaction to generate silicon carbide and metallic boride, filling the pores within the particles and achieving densification, significantly improving the load-bearing capacity and wear resistance of the ceramic nails. Example 1 used a silicon-hafnium alloy. The resulting hafnium boride had a higher melting point, higher hardness, and better high-temperature chemical stability, exhibiting the strongest interfacial bonding with the silicon carbide phase. Therefore, it demonstrated higher bending strength and better wear resistance among the seven single alloy schemes.

[0112] In Example 8, a silicon-hafnium alloy and a silicon-zirconium alloy were compounded at a mass ratio of 1:1. During the reaction and infiltration process, hafnium boride and zirconium boride were simultaneously generated. Both belong to the hexagonal crystal system and have similar lattice parameters, forming a continuous solid solution of hafnium-zirconium boride at high temperature. Hafnium atoms and zirconium atoms achieve uniform atomic-scale substitution in the boride lattice, producing a significant lattice distortion strengthening effect, making the hardness and elastic modulus of the solid solution higher than that of hafnium boride or zirconium boride alone. At the same time, the difference in diffusion rate between the two alloying elements optimizes the liquid phase flow and reaction front advancement during the infiltration process, making the internal microstructure of the ceramic nail more uniform and dense. Therefore, the bending strength of Example 8 is higher than that of Examples 1 and 4. Example 9 involves blending a silicon-hafnium alloy with a silicon-molybdenum alloy. Although the resulting hafnium boride and molybdenum boride both belong to the hexagonal crystal system, the atomic radii of molybdenum and hafnium differ significantly, resulting in severe lattice parameter mismatch. Furthermore, their electronic structures differ greatly, preventing the formation of a solid solution at the melting point, and causing them to form independent phases. Residual stress arises at the interface due to lattice mismatch, hindering synergistic strengthening. Therefore, the overall performance of Example 9 falls only between that of Example 1 and Example 3, exhibiting no synergistic effect.

[0113] Example 10 optimized the mass ratio of silicon-hafnium alloy to silicon-zirconium alloy to 3:1. Under this ratio, the hafnium content in the hafnium-zirconium boride solid solution generated during the melting process is within a suitable range. This provides sufficient solid solution strengthening to ensure high hardness while retaining an appropriate amount of zirconium to adjust the lattice parameters and electronic structure of the solid solution, thereby enhancing grain boundary bonding and significantly refining the grains. This increases the resistance to crack propagation along grain boundaries when the ceramic nail is subjected to bending loads and reduces the tendency to spalling during wear. In Example 8, the 1:1 ratio has a high zirconium content, resulting in a large degree of lattice distortion in the solid solution but relatively large grain size and a relatively reduced grain boundary area. In Example 11, the 5:1 ratio has an excessively high hafnium content, leading to excessively high solid solution hardness but insufficient toughness reserve. During wear, microcrack initiation increases due to micro-stress concentration in micro-regions. Therefore, the ratio in Example 10 achieves the optimal match between hardness and toughness, resulting in better bending strength and wear resistance.

Claims

1. A ceramic-embedded metal matrix composite material, characterized in that, It includes a matrix and multiphase ceramic nails dispersedly embedded in the matrix; The substrate is at least one of carbon steel, stainless steel, and copper; The multiphase ceramic nail comprises the following raw materials: boron carbide powder, zirconium carbide powder, binder, and silicon-containing alloy; The silicon-containing alloy is composed of silicon hafnium alloy and silicon zirconium alloy in a mass ratio of 1-5:

1.

2. A method for preparing the ceramic-embedded metal matrix composite material as described in claim 1, characterized in that, The method is as follows: Step 1: Heat the base material to melt it. After the base material has completely melted into liquid metal, remove the surface slag to obtain the molten metal. Then cool and stir to form a semi-solid metal slurry. Step 2: Under continuous stirring, the multiphase ceramic nails are gradually added to the semi-solid metal slurry obtained in Step 1. After the addition is completed, stirring is continued. Then the slurry is heated to obtain a metal melt containing dispersed multiphase ceramic nails. Step 3: Pour the molten metal obtained in Step 2 smoothly into the preheated metal mold, so that the molten metal completely fills the cavity; after casting, let the entire mold cool naturally in the air. Step 4: After the casting has cooled, open the mold and remove the cast billet; cut off the sprue and riser on the cast billet, remove the oxide scale on the surface of the casting, and sandblast the surface of the billet to obtain the cast billet of ceramic embedded metal matrix composite material; normalize the cleaned billet; and then temper the billet to obtain ceramic embedded metal matrix composite material.

3. The method as described in claim 2, characterized in that, The heating and melting mentioned in step 1 refers to heating to 1500-1600℃ for melting; the cooling and stirring refers to cooling the molten metal to 1450-1480℃ and applying mechanical stirring at a speed of 100-300 rpm.

4. The method as described in claim 2, characterized in that, The amount of multiphase ceramic nails added in step 2 is 10-20% of the mass of the semi-solid metal slurry; the heating is to raise the temperature to 1500-1650℃.

5. The method as described in claim 2, characterized in that, The preheating of the metal mold in step 3 refers to preheating to 150-300℃; the natural cooling refers to cooling to below 300℃.

6. The method as described in claim 2, characterized in that, The normalizing treatment in step 4 involves heating to 800-900℃, holding at that temperature for 1-3 hours, and then cooling in still air. The tempering treatment involves heating the billet to 500-700℃, holding at that temperature for 1-3 hours, and then air cooling.

7. The method as described in claim 2, characterized in that, The preparation method of the multiphase ceramic nail is as follows: S1. Ball mill boron carbide powder, zirconium carbide powder and binder to obtain uniform composite powder; put the dried and sieved composite powder into a mold and press it into shape to obtain ceramic nail green body; S2. The ceramic nail green body obtained in step S1 is completely embedded with a silicon-containing alloy; the reaction melt infiltration is carried out; after the reaction is completed, the sample is cooled to room temperature in the furnace, and the sample is taken out. It is first acid-washed and then ultrasonically cleaned to obtain the multiphase ceramic nail.

8. The method as described in claim 7, characterized in that, The mass ratio of boron carbide powder, zirconium carbide powder, and binder is 20-30:5-15:0.5-2; the binder is polyvinyl butyral; the ball milling is performed using anhydrous ethanol as the medium and zirconium oxide balls as the grinding media, at a speed of 100-300 rpm for 10-30 hours; the drying and sieving is performed through a 200-mesh sieve; the pressing and molding is performed by pressing into cylindrical ceramic nail green bodies with a diameter of 1-3 mm and a length of 2-5 mm under a molding pressure of 100-300 MPa.

9. The method as described in claim 7, characterized in that, The amount of silicon alloy used in the embedding is 3-5 times the mass of the ceramic nail green body; the reaction melt infiltration is carried out by heating to 1400-1500℃ at a rate of 5-10℃ / min and holding at this temperature for 60-180 minutes.

10. The method as described in claim 7, characterized in that, The acid pickling is performed using a mixed acid solution prepared with 65%-68% nitric acid and 35%-42% hydrofluoric acid at a volume ratio of 6-10:1; the ultrasonic cleaning involves immersing the sample in water and using ultrasonic waves at a frequency of 20-60 kHz and a power density of 0.5-1 W / cm². 2 Wash for 5-10 minutes at room temperature.

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