Hexagonal boron nitride nanosheet reinforced titanium-based composite material and preparation method thereof

Abstract

The present invention relates to a hexagonal boron nitride nanosheet reinforced titanium-based composite material and a preparation method thereof, and belongs to the technical field of metal-based composite materials. The material is based on titanium-based metal as a matrix, h-BNNSs are uniformly dispersed on the surface of the matrix, and has a three-dimensional interface structure composed of h-BNNSs and nano TiBw whiskers. A rapid hot pressing sintering process is adopted to reduce the diffusion rate of B atoms and N atoms in hexagonal boron nitride nanosheets under low temperature conditions, inhibit the interface reaction between the Ti matrix and the hexagonal boron nitride nano, and at the same time, high pressure increases the contact between the powders, which is conducive to the welding between the powders to achieve rapid densification. Next, a high-temperature heat treatment is applied to the composite blank with no obvious interface reaction, and the diffusion of surface B atoms in the boron nitride nanosheets is used to generate nano-scale TiBw at the interface of the composite material and insert it into the Ti matrix to achieve the retention of the intrinsic structure of the hexagonal boron nitride nano while improving the interface bonding between it and the matrix.

Description

Technical Field

[0001] The invention relates to a hexagonal boron nitride nanosheet reinforced titanium-based composite material and a preparation method thereof, belonging to the technical field of metal-based composite materials. Background Art

[0002] Hexagonal boron nitride nanosheets have a similar structure to graphene and are called white graphene. They have high elastic modulus (800-850GPa), extremely high thermal conductivity (1700-2000W / mk), high thermal stability (structure stability in air up to 900°C) and good wear resistance and other excellent properties and are considered to be an ideal composite reinforcement phase. It is expected that titanium-based composite materials with excellent mechanical properties will be prepared by combining it with titanium, which has broad application prospects in aviation, aerospace, automobile, biomedicine and other fields.

[0003] However, the preparation of hexagonal boron nitride nanosheets reinforced titanium-based composites usually adopts hot pressing and plasma activated sintering (SPS) processes, and the sintering temperature is generally above 800℃. The following problems need to be solved in the preparation process: how to achieve uniform dispersion of nano-reinforced phase in the titanium matrix, how to control the intact retention of the intrinsic structure of hexagonal boron nitride nanosheets during the sintering process, and how to achieve good interface bonding between hexagonal boron nitride nanosheets and titanium matrix. At present, the research on hexagonal boron nitride nanosheet metal-based composites at home and abroad is mainly based on aluminum and copper. Since it is full of challenges to retain the intrinsic structure of boron nitride nanosheets in titanium-based composites while achieving strong interface bonding between the reinforcement phase and the titanium matrix, the application research of hexagonal boron nitride nanosheets in titanium matrix is ​​relatively weak. Summary of the invention

[0004] In view of the problems existing in the prior art, the present invention provides a hexagonal boron nitride nanosheet reinforced titanium-based composite material and a preparation method thereof. In the composite material, the hexagonal boron nitride nanosheets are evenly dispersed, the intrinsic structure is well preserved, and at the same time, the interface between the boron nitride nanosheets and the titanium matrix generates a controllable one-dimensional nano-titanium boride (TiB w ) whiskers, to achieve a strong interface bonding between the reinforcement phase and the matrix, thereby giving full play to the intrinsic mechanical properties of the hexagonal boron nitride nanosheets. The hexagonal boron nitride nanosheet titanium-based composite material has good strength-plasticity matching and significantly improved mechanical properties.

[0005] The objectives of the present invention are achieved through the following technical solutions.

[0006] A hexagonal boron nitride nanosheet reinforced titanium-based composite material, the material has a titanium-based metal as a matrix, hexagonal boron nitride nanosheets (h-BNNSs) are uniformly dispersed on the surface of the matrix, and has a three-dimensional interface structure composed of two-dimensional hexagonal boron nitride nanosheets (h-BNNSs) and nano-TiBw whiskers.

[0007] Preferably, the thickness of the two-dimensional hexagonal boron nitride nanosheets is less than 100 nm.

[0008] A method for preparing the hexagonal boron nitride nanosheet reinforced titanium-based composite material according to the present invention, the method steps comprising:

[0009] (1) Preparation of hexagonal boron nitride (BN) nanosheet Ti composite powder

[0010] Hexagonal boron nitride nanosheets (h-BNNSs) and titanium-based metal powder are ball-milled in anhydrous ethanol and dried after ball-milling to obtain composite powders in which h-BNNSs are uniformly dispersed in Ti powder.

[0011] (2) Rapid hot pressing sintering

[0012] The h-BNNSs / Ti-based composite powder is placed in a rapid hot pressing sintering furnace, and is rapidly heated to 200°C to 700°C at a heating rate of 50°C / min or more under a sintering pressure of 100MPa to 1000MPa, and is kept at this temperature for 1min to 30min, and then cooled to obtain a dense h-BNNSs / Ti-based sintered green body.

[0013] (3) Heat treatment

[0014] The h-BNNSs / Ti-based sintered green body is placed in a vacuum heat treatment furnace at a temperature of 750° C. to 1000° C., kept at the temperature for 0.1 h to 8 h, and then cooled to obtain an h-BNNSs / Ti composite material.

[0015] Preferably, in step (1), the mass fraction of h-BNNSs in the composite powder is 0.05% to 2%.

[0016] Preferably, in step (1), the thickness of the h-BNNSs is less than or equal to 100 nm.

[0017] Preferably, in step (1), the titanium-based metal powder is pure titanium powder, Ti6Al4V alloy powder, Ti-6Al-2Sn-4Zr-2Mo memory titanium alloy powder or Ti-50Nb superconducting titanium alloy powder.

[0018] Preferably, the particle size of the titanium-based metal powder is 5 μm to 120 μm.

[0019] Preferably, in step (1), the ball milling speed is 200 rpm to 800 rpm, and the ball milling time is 2 h to 20 h.

[0020] Preferably, in step (1), the drying temperature is 50°C to 80°C, and the drying time is 12h to 24h.

[0021] Preferably, in step (2), the sintering pressure is 500MPa-800MPa, the sintering temperature is 400°C-600°C, the heating rate is 100°C / min-300°C / min, and the heat preservation and pressure holding time is 5min-15min.

[0022] Preferably, in step (3), the heat treatment temperature is 800° C. to 900° C., and the insulation time is 0.5 h to 3 h.

[0023] Beneficial effects:

[0024] (1) The hexagonal boron nitride nanosheets in the hexagonal boron nitride nanosheet reinforced titanium-based composite material of the present invention are uniformly dispersed, the intrinsic structure is intact, and the interface is tightly bonded. The composite material has excellent mechanical properties and good matching of strength and plasticity. After heat treatment, the strength of the composite material reaches 876MPa, and the elongation after fracture is 22% to 25%. Compared with pure titanium, the strength is increased by more than 60%, and the plasticity is less reduced relative to the matrix. It is a low-cost discontinuously reinforced titanium-based composite material with excellent mechanical properties.

[0025] (2) The present invention adopts a rapid hot pressing sintering process to reduce the diffusion rate of B atoms and N atoms in hexagonal boron nitride nanosheets under low temperature conditions, inhibit the interface reaction between the Ti matrix and the hexagonal boron nitride nanosheets, and at the same time, high pressure increases the contact between the powders, which is conducive to the welding between the powders to achieve rapid densification. Next, the composite material blank that is dense and has no obvious interface reaction is subjected to high-temperature heat treatment, and the diffusion of the surface B atoms in the boron nitride nanosheets is used to generate nano-scale TiBw at the interface of the composite material and insert it into the Ti matrix to achieve the retention of the intrinsic structure of the hexagonal boron nitride nanosheets while improving the interface bonding between it and the matrix. A three-dimensional interface structure of nano-TiBw whiskers with a three-dimensional spatial orientation distribution generated using two-dimensional hexagonal boron nitride nanosheets as a template is obtained.

[0026] (3) The method of the present invention is simple to operate, has a short preparation process, high preparation efficiency, low production cost, strong universality, is applicable to a variety of titanium substrates, and has good application prospects. BRIEF DESCRIPTION OF THE DRAWINGS

[0027] Figure 1 This is the SEM (scanning electron microscope) image of the h-BNNSs / Ti composite powder in step (1) of Example 1.

[0028] Figure 2 The SEM image and local enlarged image of the h-BNNSs / Ti body in step (2) of Example 1.

[0029] Figure 3 This is the SEM image of the h-BNNSs / Ti composite material after heat treatment in step (3) of Example 1.

[0030] Figure 4 The mechanical property curves of the h-BNNSs / Ti composite material and the matrix after stretching after heat treatment in step (3) of Example 1.

[0031] Figure 5 The SEM image and local enlarged image of the h-BNNSs / Ti body in step (2) of Example 2.

[0032] Figure 6 This is the SEM image of the h-BNNSs / Ti composite material after heat treatment in step (3) of Example 2.

[0033] Figure 7 This is the SEM image of the h-BNNSs / Ti body in step (2) of Example 3.

[0034] Figure 8 This is the SEM image of the h-BNNSs / Ti composite material after heat treatment in step (3) of Example 3.

[0035] Fig. 9 h-BNNSs / Ti in step (1) of Example 4 6 Al 4 SEM image of V composite powder.

[0036] Fig.10 h-BNNSs / Ti in step (2) of Example 4 6 Al 4 SEM image of the V blank and its local enlarged image.

[0037] Fig.11 h-BNNSs / Ti after heat treatment in step (3) of Example 4 6 Al 4 SEM image of V composite material.

[0038] Fig.12 This is the SEM image of the h-BNNSs / Ti body in step (2) of comparative example 1.

[0039] Fig.13 This is the SEM image of the h-BNNSs / Ti composite material after heat treatment in step (3) of comparative example 1.

[0040] Fig.14 This is the tensile mechanical property curve of the h-BNNSs / Ti composite material and the matrix after heat treatment in step (3) of comparative example 1. DETAILED DESCRIPTION

[0041] The present invention will be further described below in conjunction with the accompanying drawings and specific embodiments.

[0042] In the following embodiments:

[0043] h-BNNSs: purity 99%, thickness about 50nm, length × width 1μm × 2μm, manufacturer is Jiangsu Xianfeng Nanotechnology Co., Ltd.

[0044] Ti powder: purity 99.95%, average particle size 30μm, sold by Aladdin Chemical Reagent Platform.

[0045] Scanning electron microscope: FSEM, HITACHI S-4800N, HITACHI, Japan.

[0046] Transmission electron microscope: HRTEM, Talos, FEI, USA.

[0047] Mechanical properties of the h-BNNSs / Ti composites prepared in the examples were characterized by using a universal testing machine (AUTO-STC8800) to carry out tensile tests at room temperature, where the strain rate was 5.0×10 -4 s -1 .

[0048] Example 1

[0049] (1) Preparation of h-BNNSs / Ti composite powders

[0050] h-BNNSs powder and spherical Ti powder with an average particle size of 25 μm were added to a vacuum ball mill filled with anhydrous ethanol, wherein the ratio of zirconia ball milling beads to powder in the ball mill was 10:1, the ball milling speed was 200 rpm / min, and the ball milling time was 8 h. After the ball milling, the mixed solution was filtered and the composite powder was dried in a vacuum drying oven at 50° C. for 12 h to obtain h-BNNSs / Ti composite powder, wherein the mass fraction of h-BNNSs in the composite powder was 0.1%.

[0051] (2) Rapid hot pressing sintering

[0052] The h-BNNSs / Ti composite powder was loaded into a φ20×10 mold and heated to 500°C at a heating rate of 100°C / min using a rapid hot pressing device. At the same time, a pressure of 500 MPa was applied. The temperature was maintained at 500°C and 500 MPa for 10 minutes, and then the mold was cooled in the furnace to obtain an h-BNNSs / Ti green body.

[0053] (4) Heat treatment

[0054] The h-BNNSs / Ti blank was placed in a vacuum heat treatment furnace at a temperature of 850°C, kept at this temperature for 0.5 h, and then air-cooled to obtain the h-BNNSs / Ti composite material.

[0055] The characterization and results of the h-BNNSs / Ti composite material obtained in this embodiment are as follows:

[0056] Figure 1 is the SEM photograph of h-BNNSs / Ti composite powder, from which it can be observed that h-BNNSs are uniformly dispersed on the surface of Ti powder. Figure 2 This is a SEM photo of the h-BNNSs / Ti body obtained after rapid hot pressing and sintering. High-resolution observation shows that the composite material has high density, there is no obvious interface reaction between h-BNNSs and the Ti matrix, and the intrinsic structure of h-BNNSs is well preserved, laying the foundation for the performance of the intrinsic performance of the reinforcement phase. Figure 3 As shown. After heat treatment, nano-scale TiBw whiskers are generated at the h-BNNSs / Ti interface and inserted into the Ti matrix, which significantly improves the interface bonding between h-BNNSs and the Ti matrix. At the same time, the intrinsic structure of h-BNNSs is well preserved. The mechanical properties of the h-BNNSs / Ti composite material after heat treatment are shown in the figure. Figure 4 As shown in the figure, the tensile strength and yield strength of the composite material are 876MPa and 792MPa, which are 61% and 84% higher than those of the matrix, respectively, and the strengthening effect is very significant. At the same time, the elongation of the composite material after fracture is maintained at 23%, achieving a good matching of strength and toughness.

[0057] Example 2

[0058] (1) Preparation of h-BNNSs / Ti composite powders

[0059] h-BNNSs powder and spherical Ti powder with an average particle size of 45 μm were added to a vacuum ball mill filled with anhydrous ethanol, wherein the ratio of zirconia ball milling beads to powder in the ball mill was 8:1, the ball milling speed was 300 rpm / min, and the ball milling time was 8 h. After the ball milling, the mixed solution was filtered and the composite powder was dried in a vacuum drying oven at 50° C. for 12 h to obtain h-BNNSs / Ti composite powder, wherein the mass fraction of h-BNNSs in the composite powder was 0.05%.

[0060] (2) Rapid hot pressing sintering

[0061] The h-BNNSs / Ti composite powder was loaded into a φ20×10 mold and heated to 550°C at a heating rate of 100°C / min using a rapid hot pressing device. At the same time, a pressure of 300 MPa was applied. The temperature was maintained at 550°C and 300 MPa for 10 minutes, and then the mold was cooled in the furnace to obtain an h-BNNSs / Ti green body.

[0062] (4) Heat treatment

[0063] The h-BNNSs / Ti blank was placed in a vacuum heat treatment furnace at a temperature of 800°C, kept warm for 1 hour, and then air-cooled to obtain the h-BNNSs / Ti composite material.

[0064] The characterization and results of the h-BNNSs / Ti composite material obtained in this embodiment are as follows:

[0065] Figure 5 This is the SEM image of the h-BNNSs / Ti body obtained after rapid hot pressing sintering. The composite material obtained a dense body after sintering, and the interface reaction between h-BNNSs and Ti matrix was weak. Figure 6 As shown. After heat treatment, nano-TiBw whiskers are generated at the interface between h-BNNSs and Ti matrix and grow into the Ti matrix while the intrinsic structure of h-BNNSs is well preserved. The tensile strength of the composite material tested on a universal mechanical testing machine is 803MPa, which is 51% higher than that of pure titanium matrix under the same process while the elongation after fracture of the composite material remains at 21%.

[0066] Example 3

[0067] (1) Preparation of h-BNNSs / Ti composite powders

[0068] h-BNNSs powder and spherical Ti powder with an average particle size of 25 μm were added to a vacuum ball mill filled with anhydrous ethanol, wherein the ratio of zirconia ball milling beads to powder in the ball mill was 10:1, the ball milling speed was 200 rpm / min, and the ball milling time was 8 h. After the ball milling, the mixed solution was filtered and the composite powder was dried in a vacuum drying oven at 50° C. for 12 h to obtain h-BNNSs / Ti composite powder, wherein the mass fraction of h-BNNSs in the composite powder was 0.1%.

[0069] (2) Rapid hot pressing sintering

[0070] The h-BNNSs / Ti composite powder was loaded into a φ15×10 mold and heated to 400°C at a heating rate of 100°C / min using a rapid hot pressing device. At the same time, a pressure of 1000 MPa was applied. The temperature was maintained at 400°C and 1000 MPa for 10 minutes, and then the mold was cooled in the furnace to obtain an h-BNNSs / Ti green body.

[0071] (4) Heat treatment

[0072] The h-BNNSs / Ti blank was placed in a vacuum heat treatment furnace at a temperature of 850°C, kept at this temperature for 0.5 h, and then air-cooled to obtain the h-BNNSs / Ti composite material.

[0073] The characterization and results of the h-BNNSs / Ti composite material obtained in this embodiment are as follows:

[0074] Figure 7This is the SEM image of h-BNNSs / Ti composite material after sintering. There is no interface reaction between h-BNNSs and Ti matrix, and the intrinsic structure of the reinforcement phase is intact. Figure 8 This is a SEM image of the h-BNNSs / Ti composite material after heat treatment. The intrinsic structure of h-BNNSs is well preserved, and nano-TiBx whiskers grow from the interface between h-BNNSs and Ti matrix into the Ti matrix to obtain a composite material with strong interface bonding. The tensile strength of the composite material tested on a universal mechanical testing machine is 852MPa, which is 59% higher than that of pure titanium matrix under the same process, while the elongation after fracture of the composite material remains at 23%.

[0075] Example 4

[0076] (1) h-BNNSs / Ti 6 Al 4 Preparation of V(TC4) composite powder

[0077] h-BNNSs powder and spherical TC4 powder with an average particle size of 45 μm were added to a vacuum ball mill filled with anhydrous ethanol, wherein the ratio of zirconium oxide ball milling beads to powder in the ball mill was 10:1, the ball milling speed was 300 rpm / min, and the ball milling time was 8 h. After the ball milling, the mixed solution was filtered and then the composite powder was dried in a vacuum drying oven at 50°C for 12 h to obtain h-BNNSs / TC4 composite powder, wherein the mass fraction of h-BNNSs in the composite powder was 0.1%.

[0078] (2) Rapid hot pressing sintering

[0079] The h-BNNSs / TC4 composite powder was loaded into a φ20×10 mold and heated to 600°C at a heating rate of 100°C / min using a rapid device. At the same time, a pressure of 500 MPa was applied. The temperature was maintained at 600°C and 500 MPa for 10 minutes, and then the mold was cooled in the furnace to obtain the h-BNNSs / TC4 green body.

[0080] (4) Heat treatment

[0081] h-BNNSs / TC 4 The green body was placed in a vacuum heat treatment furnace at 900°C, kept at this temperature for 0.5h and then cooled with the furnace to obtain the h-BNNSs / TC4 composite material.

[0082] The characterization and results of the h-BNNSs / TC4 composite material obtained in this embodiment are as follows:

[0083] Fig. 9 This is the SEM photo of h-BNNSs / TC4 composite powder, from which it can be observed that h-BNNSs are uniformly dispersed on the surface of TC4 spherical powder. Fig.10This is the SEM photo of the h-BNNSs / TC4 green body obtained after rapid hot pressing sintering. It is observed that the composite material has high density, there is no obvious interface reaction between h-BNNSs and Ti matrix, and the intrinsic structure of h-BNNSs is well preserved. Fig.11 As shown. After heat treatment, nano-scale TiBw whiskers are generated at the h-BNNSs / TC4 interface and inserted into the TC4 matrix, which significantly improves the interface bonding between h-BNNSs and TC4 matrix, while the intrinsic structure of h-BNNSs is well preserved. After being stretched by a universal mechanical testing machine, the tensile strength of the composite material is 1098MPa, which is 26% higher than that of the TC4 matrix under the same process. At the same time, the elongation of the composite material after fracture is maintained at 15%, achieving a good matching of strength and toughness.

[0084] Comparative Example 1

[0085] (1) Preparation of h-BNNSs / Ti composite powders

[0086] h-BNNSs powder and spherical Ti powder with an average particle size of 45 μm were added to a vacuum ball mill filled with anhydrous ethanol, wherein the ratio of zirconia ball milling beads to powder in the ball mill was 8:1, the ball milling speed was 300 rpm / min, and the ball milling time was 8 h. After the ball milling, the mixed solution was filtered and the composite powder was dried in a vacuum drying oven at 50° C. for 12 h to obtain h-BNNSs / Ti composite powder, wherein the mass fraction of h-BNNSs in the composite powder was 0.1%.

[0087] (2) Rapid hot pressing sintering

[0088] The h-BNNSs / Ti composite powder was loaded into a φ20×10 mold and heated to 850°C at a heating rate of 100°C / min using a rapid hot pressing device. At the same time, a pressure of 50 MPa was applied. The temperature was maintained at 850°C and 50 MPa for 10 minutes, and then the h-BNNSs / Ti green body was obtained by cooling with the furnace.

[0089] (4) Heat treatment

[0090] The h-BNNSs / Ti blank was placed in a vacuum heat treatment furnace at a temperature of 850°C, kept at this temperature for 0.5 h, and then air-cooled to obtain the h-BNNSs / Ti composite material.

[0091] The characterization and results of the h-BNNSs / Ti composite material obtained in this embodiment are as follows:

[0092] Fig.12This is a SEM image of the h-BNNSs / Ti body obtained after high-temperature sintering. The interface reaction between the h-BNNSs and the Ti matrix in the composite material is intense, and basically only the existence of the interface reaction product TiBw can be observed. The intrinsic structure of h-BNNSs no longer exists. Fig.13 As shown. After heat treatment, only TiBw whiskers were observed to grow and coarsen further in the composite material. The mechanical properties of the composite material were tested on a universal mechanical testing machine. Fig.14 As shown, the tensile strength of the composite material is 835 MPa, but its elongation is reduced to 0.8%, and the strong-plastic matching effect cannot be obtained.

[0093] In summary, the above are only preferred embodiments of the present invention and are not intended to limit the protection scope of the present invention. Any modifications, equivalent substitutions, improvements, etc. made within the spirit and principles of the present invention should be included in the protection scope of the present invention.

Claims

1. A hexagonal boron nitride nanosheet reinforced titanium-based composite material, characterized in that: The material has a titanium-based metal as a matrix, h-BNNSs are uniformly dispersed on the surface of the matrix, and has a three-dimensional interface structure composed of h-BNNSs and nano-TiBw whiskers; The material is prepared by the following method, which comprises the following steps: (1) ball milling h-BNNSs and titanium-based metal powder in anhydrous ethanol and drying after ball milling to obtain composite powders in which h-BNNSs are uniformly dispersed in Ti powder; (2) placing the h-BNNSs / Ti-based composite powder into a rapid hot pressing sintering furnace, rapidly heating the temperature to 200°C~700°C at a heating rate of 50°C / min or more under a sintering pressure of 100MPa~1000MPa, maintaining the temperature and pressure for 1min~30min, and cooling to obtain a dense h-BNNSs / Ti-based sintered green body; (3) placing the h-BNNSs / Ti-based sintered body into a vacuum heat treatment furnace at a temperature of 750°C to 1000°C, keeping the temperature for 0.1h to 8h, and then cooling to obtain an h-BNNSs / Ti composite material.

2. The hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 1, characterized in that: The thickness of the h-BNNSs is less than 100 nm.

3. A method for preparing the hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 1 or 2, characterized in that: The method steps include: (1) ball milling h-BNNSs and titanium-based metal powder in anhydrous ethanol and drying after ball milling to obtain composite powders in which h-BNNSs are uniformly dispersed in Ti powder; (2) placing the h-BNNSs / Ti-based composite powder into a rapid hot pressing sintering furnace, rapidly heating the temperature to 200°C~700°C at a heating rate of 50°C / min or more under a sintering pressure of 100MPa~1000MPa, maintaining the temperature and pressure for 1min~30min, and cooling to obtain a dense h-BNNSs / Ti-based sintered green body; (3) placing the h-BNNSs / Ti-based sintered body into a vacuum heat treatment furnace at a temperature of 750°C to 1000°C, keeping the temperature for 0.1h to 8h, and then cooling to obtain an h-BNNSs / Ti composite material.

4. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (1), the mass fraction of h-BNNSs in the composite powder is 0.05% to 2%.

5. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (1), the thickness of the h-BNNSs is less than or equal to 100 nm.

6. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (1), the titanium-based metal powder is pure titanium powder, Ti6Al4V alloy powder, Ti-6Al-2Sn-4Zr-2Mo memory titanium alloy powder or Ti-50Nb superconducting titanium alloy powder.

7. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: The particle size of the titanium-based metal powder is 5 μm to 120 μm.

8. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (1), the ball milling speed is 200 rpm to 800 rpm, and the ball milling time is 2 h to 20 h; the drying temperature is 50° C. to 80° C., and the drying time is 12 h to 24 h.

9. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (2), the sintering pressure is 500MPa~800MPa, the sintering temperature is 400℃~600℃, the heating rate is 100℃ / min~300℃ / min, and the heat preservation and pressure holding time is 5min~15min.

10. The method for preparing a hexagonal boron nitride nanosheet reinforced titanium-based composite material according to claim 3, characterized in that: In step (3), the heat treatment temperature is 800°C to 900°C, and the insulation time is 0.5h to 3h.

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