High-wear-resistance additive forming titanium-based composite material and preparation method thereof

Abstract

The invention discloses a high-wear-resistance additive forming titanium-based composite material and a preparation method thereof. The high-abrasion-resistance additive forming titanium-based composite material is mainly composed of a base body and an amorphous ceramic film, and the high-abrasion-resistance additive forming titanium-based composite material is prepared from, by mass, 97.0%-99.8% of the base body and 0.2%-3% of the amorphous ceramic film. By accurately controlling the thickness and the quality of the amorphous ceramic film, the number and the size of the reinforced phases can be regulated and controlled, and the fluidity and the oxidation resistance of the additive manufacturing titanium alloy powder can be remarkably improved through introduction of the amorphous ceramic film; the in-situ synthesis ceramic reinforced titanium-based composite material prepared through additive manufacturing is free of cracks, high in hardness, good in wear resistance and suitable for being used under harsh working conditions.

Description

Technical Field

[0001] This invention relates to the field of additive manufacturing of titanium alloy materials, and particularly to a high wear-resistant additively formed titanium-based composite material and its preparation method. Background Technology

[0002] Titanium alloys are widely known as "space metals" and "marine metals" due to their superior specific strength and corrosion resistance. With a density only 60% that of steel, yet strength comparable to high-strength steel, they are ideal for aerospace applications, making them a superior material for manufacturing landing gear, fuselage frames, compressor discs, rocket engines, and fuel tanks, significantly reducing structural weight and improving fuel efficiency and payload. In marine engineering, titanium alloys exhibit excellent resistance to seawater corrosion and are used in deep-sea submarine pressure hulls, ship propulsion systems, and seawater piping systems. Furthermore, they are widely used in chemical, petroleum refining, and seawater desalination industries, manufacturing reactors, heat exchangers, and pipelines, significantly extending equipment life and reducing maintenance costs. Titanium alloys also possess excellent biocompatibility and have been successfully applied to medical implants such as artificial joints and dental implants, thus earning them the title of "biometals."

[0003] However, the inherent low hardness, poor wear resistance, and high coefficient of friction of titanium alloys limit their application in sliding and frictional conditions. Titanium alloys have a low surface hardness (typically only 30-35 HRC), far lower than tool steel or carburized steel, making them prone to plastic deformation and scratches during friction. Simultaneously, titanium alloys have poor thermal conductivity, making it difficult for frictional heat to dissipate quickly, leading to excessively high localized temperatures, causing microstructural changes and exacerbating the material's adhesion tendency. More critically, their high chemical reactivity makes them prone to "cold welding" or adhesive wear with mating materials at high frictional temperatures, resulting in material transfer and surface failure. To overcome these limitations, researchers have developed various surface strengthening techniques, including thermal oxidation, laser cladding, plasma spraying, physical / chemical vapor deposition (PVD / CVD), and ion implantation, to improve wear resistance by constructing high-hardness coatings (such as titanium oxide, titanium nitride, and diamond-like carbon) on the surface. However, these technologies can usually only treat a few millimeters of the component surface. The process is complex and costly, and it is difficult to achieve uniform coating coverage on complex-shaped components, making repair difficult and limiting their engineering applicability.

[0004] To further improve the overall wear resistance and comprehensive performance of titanium alloys, particle-reinforced titanium-based composites have become an important development direction. The current mainstream preparation methods are in-situ self-generated technologies, including casting, powder metallurgy, self-propagating high-temperature synthesis, mechanical alloying, and laser deposition. Based on reaction type, these can be divided into solid-solid, solid-liquid, and gas-solid reaction methods, with solid-solid reaction methods such as spark plasma sintering and reactive hot pressing being the most widely used. However, a single method is usually insufficient to produce products with a comprehensive match in size, shape, and performance in a single step, often requiring subsequent processing to obtain usable components. Furthermore, due to the introduction of high-hardness ceramic reinforcing phases (such as carbides and oxides), these composites exhibit high deformation resistance and poor room-temperature plasticity, significantly increasing the difficulty of hot working, especially in forming complex contour workpieces. During the mixing process of the parent alloy and ceramics, problems such as ceramic particle agglomeration easily occur, affecting component distribution and printing quality. Therefore, future research on titanium-based composite material processing technology needs to be further strengthened to promote its engineering applications and industrialization. Summary of the Invention

[0005] To address the problems existing in the background technology, this invention provides a high-wear-resistant additively formed titanium-based composite material, its preparation method, and its application. The method comprises two stages: the first stage is the composite material preparation stage, and the second stage is a laser selective melting forming stage. This material is produced by depositing an amorphous ceramic thin film on the surface of titanium alloy powder, thereby modifying the surface of the titanium alloy powder and improving its fluidity and oxidation resistance. Then, selective melting technology is used to induce an in-situ reaction between Ti elements in the titanium alloy and elements such as B, C, or N in the amorphous ceramic thin film, generating a nano-reinforcing phase (one or more of TiC, TiB, and TiN), achieving a uniform and dispersed distribution within the bulk titanium-based composite material. By precisely controlling the thickness and quality of the amorphous ceramic thin film, the quantity and size of the reinforcing phase can be controlled.

[0006] The technical solution adopted in this invention is: I. A high wear-resistant additively formed titanium-based composite material The high wear-resistant additively formed titanium-based composite material is mainly composed of a matrix and an amorphous ceramic film. The mass fraction of each component of the high wear-resistant additively formed titanium-based composite material is as follows: Matrix: 97.0-99.8%; Amorphous ceramic thin films: 0.2-3.0%.

[0007] The substrate is a titanium alloy powder, which is one or more of TA1, TA15, TC4, TA18, and TC21; the amorphous ceramic film is one or more of TiB2, B4C, and BN.

[0008] II. Preparation Method of High Wear-Resistant Additive Molding Titanium-Based Composite Materials Composite material preparation stage: S1: The titanium alloy powder is thoroughly dried in a vacuum drying oven to remove the physically adsorbed water on the titanium alloy powder and obtain dry titanium alloy powder. S2: First, the surface of the dry titanium alloy powder is cleaned by in-situ plasma etching. Then, ceramic particles are added in a certain proportion, and a dense amorphous ceramic film is deposited using thin film deposition technology to obtain titanium alloy composite powder with an amorphous ceramic film on the surface. S3: The titanium alloy composite material powder with an amorphous ceramic film on its surface is sieved and dried sequentially to obtain titanium-based composite material powder.

[0009] In step S1, the titanium alloy powder is one or more of TA1, TA15, TC4, TA18, TC21, etc.

[0010] In step S2, the ceramic particles are one or more of B4C, TiB2, BN, etc., and the mass of the ceramic particles is 0.2-3.1% of the mass of the dry titanium alloy powder.

[0011] In step S2, the thickness of the amorphous ceramic thin film is 10nm-300nm, the in-situ plasma etching and cleaning is performed in a chamber filled with argon gas, and the thin film deposition technology is one of physical vapor deposition (PVD) or chemical vapor deposition (CVD).

[0012] The particle size of the titanium-based composite material powder obtained after sieving in step S3 is 15~53µm.

[0013] III. Applications of High Wear-Resistant Additive Molding Titanium-Based Composites Applications of titanium alloy materials in additive manufacturing.

[0014] IV. Additive Manufacturing Method of Titanium Alloy Materials for High Wear-Resistant Additive Molding Titanium-Based Composite Materials Laser selective melting and forming stage: 1) Use 3D software to construct the required part model, and then process the part model into layers according to the requirements of layered analysis; 2): Using laser melting technology, specifically laser powder bed melting, titanium-based composite powder coated with an amorphous ceramic film is additively manufactured. The layered part model is imported into the laser additive manufacturing equipment, and the titanium-based composite powder is printed using laser powder bed melting according to the set process parameters, resulting in an in-situ self-generated titanium-based composite block. 3): The microstructure of the prepared in-situ self-generated titanium-based composite material block was characterized and its performance was verified.

[0015] In step 2), the laser power used for laser powder bed melting is set between 150 and 200W, the scanning speed is maintained between 1200 and 1800 mm / s, and the layer thickness is set between 20 and 40 µm; the oxygen content of the laser powder bed melting is controlled below 0.200%; and the substrate preheating temperature of the laser powder bed melting is set to 120-180℃.

[0016] By modifying the particle surface with an amorphous layer, the moisture resistance, flowability, compaction, dispersibility, and cohesion of the printed powder can be greatly improved, the reflectivity can be reduced, oxidation can be reduced, smaller and more uniform grain boundaries can be formed, and inclusions can be reduced.

[0017] During the laser powder bed melting process, the titanium-based composite powder undergoes chemical reactions with elements such as B, C, and N in the amorphous ceramics: Ti + TiB₂ → TiB, or Ti + B₄C → TiB + TiC, or Ti + BN → TiB + TiN. This introduces TiB, TiN whiskers, or TiC reinforcing phases into the titanium alloy matrix. The reinforcing phases are uniformly dispersed in the titanium solid solution matrix and can form low-interfacial-energy coherent interfaces with the matrix.

[0018] A ceramic reinforcing phase is introduced into the titanium-based composite powder system. Ceramic phase particles typically possess characteristics such as high hardness, high elastic modulus, and high melting point. Uniformly distributed ceramic particles can significantly alter the solidification path of the matrix and compound, and as a heterogeneous nucleating agent, they can refine grains. Simultaneously, they can significantly improve the thermal stress distribution during rapid solidification, inhibit the generation of hot cracks, and thus improve the alloy's formability and heat resistance.

[0019] By adding ceramic reinforcing phases to titanium alloy powder through in-situ reaction, the strength, hardness, and wear resistance of printed titanium alloys can be improved simultaneously.

[0020] In this invention, different precursors are selected, and a dense amorphous ceramic film is deposited on the surface of titanium alloy powder using thin film deposition technology. Selective melting technology is used to induce an in-situ reaction between Ti elements in the titanium alloy and elements such as B, C, or N in the amorphous ceramic film, generating a nanocrystalline whisker-reinforcing phase (one or more of TiC, TiB, and TiN), which is uniformly dispersed within the bulk titanium-based composite material. By precisely controlling the thickness and quality of the amorphous ceramic film, the quantity and size of the reinforcing phase can be controlled. The introduction of the amorphous ceramic film significantly improves the flowability and oxidation resistance of additively manufactured titanium alloy powder. The in-situ self-generated ceramic-reinforced titanium-based composite material prepared by additive manufacturing is crack-free, has high hardness, good wear resistance, and is suitable for use under harsh conditions.

[0021] The beneficial effects of this invention are: This invention provides a high-wear-resistant additively formed titanium-based composite material and its preparation method. This invention combines thin-film deposition technology and additive manufacturing technology to achieve the preparation of nanofiber-reinforced titanium-based composite materials through in-situ reaction. The bulk titanium-based composite material prepared using this method possesses excellent comprehensive mechanical properties and has broad application prospects in aerospace, transportation, and other fields.

[0022] The titanium alloy powder prepared in this invention has good flowability and strong oxidation resistance. The in-situ self-generated nanocrystal-reinforced titanium-based composite material prepared by additive manufacturing has high strength / hardness, good wear resistance, and high molding quality, making it suitable for use in extremely harsh working conditions. Attached Figure Description

[0023] Figure 1 This is the basic technical path for the high wear-resistant additively formed titanium-based composite material and its preparation method in this invention; Figure 2 The image shows the microstructure of TC4 deposited via thin film in Example 1. Figure 3 This is a topographic image of the additively manufactured titanium alloy block in Example 1; Figure 4 The transmission electron microscopy (TEM) images of the titanium alloy after additive manufacturing in Example 1 are shown below. (a) is the high-angle annular dark field image (HAADF) of the TiB whiskers formed in situ after additive manufacturing, (b) is the bright field image (BF) of the TiB whiskers formed in situ after additive manufacturing, (c) is the dark field image (DF) of the TiB whiskers formed in situ after additive manufacturing, and (d) is the energy dispersive spectroscopy (EDS) corresponding to the regions (a)-(c). Figure 5 The following are the tribological properties of the printed titanium-based composite material in Example 1: (a) is the scratch profile morphology image of the printed titanium-based composite material after friction test with 1% mass fraction TiB2 added (the thickness of the amorphous TiB2 ceramic film is 200 nm); (b) is the variation of the scratch profile along the X direction of the printed titanium-based composite material after friction test with 1% mass fraction TiB2 added. Figure 6 The images show the tribological properties of TC4 powder without TiB2 amorphous ceramic film coating after printing. (a) is the morphological image of the friction scratch outline of TC4 powder without TiB2 amorphous ceramic film coating in the printed state; (b) is the height variation of the friction scratch outline of TC4 powder without TiB2 amorphous ceramic film coating along the X direction. Figure 7 The image shows the morphology of the TiB2 / TC4 composite material printed in Comparative Example 2. Detailed Implementation

[0024] The present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments.

[0025] The embodiments of the present invention are as follows: Example 1:

[0026] like Figure 1 As shown, the preparation process of high wear-resistant additively formed titanium-based composite materials is as follows: Step 1: Select spherical TC4 powder with a particle size distribution of 15-53μm, place the spherical TC4 powder in a vacuum drying oven, and dry at 120°C for at least 12 hours to completely remove physically adsorbed water.

[0027] Step 2: Reactor loading The processed dry powder is loaded into the deposition chamber of a dedicated fluidized bed sputtering coating equipment.

[0028] Step 3: High vacuum and preheating The deposition chamber was evacuated to a high vacuum (background vacuum ≤ 5.0 × 10⁻). 4 Pa). Turn on the heater to preheat the powder to the predetermined deposition temperature (120°C), and at the same time introduce a small amount of high-purity Ar gas (Ar gas is 99.999% high-purity argon gas, pressure 10Pa). Start the fluidization system to begin initial fluidization, so that the powder is heated evenly during the preheating process.

[0029] Step 4: In-situ plasma etching and cleaning Ar gas is introduced into the deposition chamber, and the pressure is adjusted to the working pressure required for fluidization (10 Pa). The fluidizing gas is turned on to bring the powder bed into a stable fluidized state. The radio frequency (RF) plasma power supply (or the power supply of the sputtering target) is turned on to generate Ar plasma, which bombards and cleans the surface of the fluidized powder for 10-20 minutes. This step can effectively remove trace oxides and adsorbates from the powder surface, significantly improving film adhesion.

[0030] Step 5: Thin Film Deposition Select a TiB2 ceramic target (sintered target) with a stoichiometric ratio of 1:2 and initiate sputtering. First, maintain a stable Ar gas flow rate and operating pressure to ensure continuous and stable powder fluidization. Then, turn on the magnetron sputtering power supply using an radio frequency (RF) power source. Gradually and slowly increase the power to the preset value to generate a stable and uniform plasma. Set the power to 200W, precisely control the deposition temperature at 120℃, and the chamber pressure to 0.8 × 10⁻⁶. -7 Torr, deposition time 5h. Atoms and atomic groups in the TiB2 target are sputtered and deposited on the surface of the continuously tumbling titanium powder.

[0031] Step 6: Cooling and Sampling The magnetron sputtering power supply and heater were turned off in sequence, while Ar gas was continuously introduced and fluidized. The powder was allowed to cool to near room temperature under the protection of an inert atmosphere to prevent oxidation from contact with oxygen in the air. The average thickness of the amorphous TiB2 ceramic film deposited on the surface of the TC4 particles was 200 nm, with a mass fraction of 1%. Then the chamber was opened, the coated powder was removed, and stored in a desiccator.

[0032] Step 7: Additive manufacturing of the coated titanium-based composite powder First, powder is spread using a laser powder bed fusion device, followed by printing. A unidirectional scanning strategy is employed, with the powder layer thickness set to 30µm, laser power set to 180W, scanning speed set to 1250mm / s, scanning spacing set to 90µm, angle increment set to 67°, and area overlap set to 0.13mm. The printing process is protected by argon gas with an oxygen content ≤0.200%, and the substrate preheating temperature is 180℃. After printing, the substrate is removed after cooling to room temperature.

[0033] Step 8: Perform microstructure characterization and performance verification on the printed TiB2 / TC4 titanium-based composite material block.

[0034] like Figure 2 As shown in the microstructure morphology diagram of TC4 after thin film deposition, it can be seen that the titanium-based composite powder prepared by this invention has good sphericity; as Figure 3 As shown, the additively manufactured titanium alloy block exhibits good morphology, meaning the printed titanium alloy block shows no visible cracks and good formability; for example... Figure 4 As shown in (a), (b), (c), and (d), the TiB generated in situ exists in the form of nanorod whiskers; as Figure 5 As shown in (a) and (b), the tribological properties of the printed titanium-based composite material show that the scratches on the printed sample after adding ceramic particles are shallower, indicating stronger wear resistance. Example 2:

[0035] Step 1: Select industrial pure titanium (TA1) powder with a particle size distribution of 15-53μm, place the industrial pure titanium (TA1) powder in a vacuum drying oven, and dry it at 110°C for at least 15 hours to completely remove physically adsorbed water.

[0036] Step 2: Reactor loading The processed dried powder is loaded into the deposition chamber of a dedicated fluidized bed PVD equipment.

[0037] Step 3: High vacuum and preheating The deposition chamber was evacuated to a high vacuum (background vacuum ≤ 5.0 × 10⁻). 4Turn on the heater and heat the powder to the predetermined deposition temperature (150°C). At the same time, introduce a small amount of high-purity Ar gas (Ar gas is 99.999% high-purity argon gas, pressure 10 Pa) and start the fluidization system to begin initial fluidization, so that the powder is heated uniformly during the preheating process.

[0038] Step 4: In-situ plasma etching and cleaning Ar gas is introduced into the deposition chamber, and the Ar gas pressure is adjusted to the working pressure required for fluidization (15 Pa). The fluidizing gas is turned on to bring the powder bed into a stable fluidized state. Then, the radio frequency (RF) plasma power supply is turned on to generate Ar plasma. The fluidized powder is bombarded and cleaned for 15-25 minutes. This step effectively removes the extremely thin oxide layer formed on the powder surface during transport and preheating, significantly improving the adhesion between the film and the substrate.

[0039] Step 5: BN thin film deposition Using a BN ceramic target (sintered target) with a stoichiometric ratio close to 1:1, sputtering was initiated. First, a stable Ar gas flow rate and operating pressure were maintained to ensure continuous and stable powder fluidization. Then, the radio frequency (RF) power supply connected to the BN target was turned on, and the power was gradually and slowly increased to the preset value to generate a stable and uniform plasma. The power was set to 250W, the deposition temperature was precisely controlled at 150℃, and the chamber pressure was 0.65 × 10⁻⁶. -7 Torr, deposition time 2h. Atoms and atomic groups in the BN target are sputtered and deposited on the surface of continuously tumbling titanium powder. Precise control of deposition temperature, sputtering power, working pressure and deposition time is crucial, with low temperature (<150℃) being key to suppressing atomic diffusion and forming amorphous BN.

[0040] Step 6: Cooling and Sampling The sputtering power supply and heater were turned off sequentially. Ar gas was continued to be introduced and fluidized, allowing the powder to cool to below 60°C under the protection of an inert atmosphere to prevent the high-temperature powder from being oxidized by contact with oxygen in the air. Then the chamber was opened, the coated powder was removed, and stored in a desiccator.

[0041] Step 7: An amorphous BN ceramic film with a thickness of 90 nm and a mass fraction of 0.3% is deposited on the surface of TA1 particles; Step 8: Powder Bed Molding Printing First, powder is spread using a laser powder bed fusion device, followed by printing. A unidirectional scanning strategy is employed, with the powder layer thickness set to 40µm, laser power set to 160W, scanning speed set to 1200mm / s, scanning spacing to 60µm, angle increment to 67°, and area overlap set to 0.13mm. The printing process is protected by argon gas with an oxygen content ≤0.200%, and the substrate is preheated to 200℃ during printing. After printing, the substrate is removed after cooling to room temperature.

[0042] In this Example 2, the in-situ reaction Ti + BN → TiB + TiN occurs during the additive manufacturing process, thus allowing the in-situ introduction of two reinforcing phases: TiB and TiN into the titanium matrix. The synergistic effect of whisker-like TiB and TiN avoids the limitations of using only one type of whisker, further enhancing wear resistance.

[0043] Comparative Example 1: For TC4 powder without TiB2 ceramic coating, TC4 was sieved and dried before printing. The printing parameters were the same as in Example 1: a unidirectional scanning strategy, a powder layer thickness of 30µm, a laser power of 180W, a scanning speed of 1250mm / s, a scanning spacing of 90µm, an angle increment of 67°, and a region overlap of 0.13mm. The forming process was protected by argon gas with an oxygen content ≤0.200%, and the substrate preheating temperature was 180℃. After printing, the powder was cooled and removed.

[0044] The tribological properties of TC4 powder printed without TiB2 amorphous ceramic film coating are as follows: Figure 6 As shown in (a) and (b), the titanium alloy without TiB2 addition exhibits poor wear resistance and deeper scratches. This comparison with Example 1 demonstrates that TiB2 plays a crucial role in improving the wear resistance of titanium alloys.

[0045] Comparative Example 2: The deposition process was modified to increase the thickness of the amorphous ceramic film on the surface of TC4 titanium alloy particles to 500 nm. A TiB2 ceramic target (sintered target) with a stoichiometric ratio of 1:2 was selected. Sputtering was initiated, and the deposition process was controlled to deposit an amorphous TiB2 ceramic film on the TC4 particle surface. First, a stable Ar gas flow rate and operating pressure were maintained to ensure continuous and stable powder fluidization. Then, the magnetron sputtering power supply was turned on using an radio frequency (RF) power supply. The power was gradually and slowly increased to a preset value to generate a stable and uniform plasma. The power was set to 200 W, the deposition temperature was precisely controlled at 120 °C, and the chamber pressure was 0.8 × 10⁻⁶. -7 Torr, deposition time 12h. The mass fraction of the amorphous ceramic film after deposition was 5%.

[0046] TC4 powder modified with a relatively thick (high mass fraction) amorphous ceramic film was printed. The printing parameters were the same as in Example 1, namely, a unidirectional scanning strategy, a powder layer thickness of 30µm, a laser power of 180W, a scanning speed of 1250mm / s, a scanning spacing of 90µm, an angle increment of 67°, and a region overlap of 0.13mm. Argon gas was used for protection during the forming process, with an oxygen content ≤0.200%. The substrate preheating temperature during forming was 180°C. After printing, the substrate was cooled and removed.

[0047] Figure 7 The morphology of the TiB2 / TC4 composite material printed in this comparative example is shown. As can be seen from the figure, the TiB2 / TC4 titanium-based composite material printed in this comparative example has visible cracks. This indicates that if the concentration of hard and brittle TiB particles generated in situ is too high, it will lead to excessive micro-stress, making the sample brittle, which in turn leads to the appearance of macro-cracks and affects the printability.

[0048] The above embodiments are used to explain and illustrate the present invention, but not to limit the present invention. Any modifications and changes made to the present invention within the spirit and scope of the claims shall fall within the protection scope of the present invention.

Claims

1. A high wear resistance additive manufacturing titanium-based composite material, characterized in that: the high wear resistance additive manufacturing titanium-based composite material is mainly composed of a matrix and an amorphous ceramic film, and the mass fraction of each component of the high wear resistance additive manufacturing titanium-based composite material is: the matrix: 97.0-99.8%; the amorphous ceramic film: 0.2-3.0%. The matrix is a titanium alloy system powder, and the titanium alloy system powder is a combination of one or more of TA1, TA15, TC4, TA18, and TC21; the amorphous ceramic film is a combination of one or more of TiB2, B4C, and BN. The method comprises: S1: drying the titanium alloy powder in a vacuum drying box to remove the physical adsorbed water on the titanium alloy powder and obtain dried titanium alloy powder; 2. A high wear resistant additive formed titanium matrix composite according to claim 1, characterized in that: S2: first, the surface of the dried titanium alloy powder is cleaned by in-situ plasma etching, then ceramic particles are put in, and a layer of amorphous ceramic film is deposited by thin film deposition technology to obtain titanium alloy composite material powder covered with amorphous ceramic film; 3. A method of producing the high wear resistant additively formed titanium matrix composite of any of claims 1-2, characterized by: S3: the titanium alloy composite material powder covered with amorphous ceramic film is sequentially sieved and dried to obtain titanium-based composite material powder. In step S1, the titanium alloy powder is a combination of one or more of TA1, TA15, TC4, TA18, and TC21. In step S2, the ceramic particles are a combination of one or more of B4C, TiB2, and BN, and the mass of the ceramic particles is 0.2-3.1% of the mass of the dried titanium alloy powder. In step S2, the thickness of the amorphous ceramic film is 10-300 nm, the in-situ plasma etching is carried out in an argon gas chamber, and the thin film deposition technology is one of physical vapor deposition and chemical vapor deposition.

4. A method of producing a high wear resistant additive formed titanium matrix composite material as claimed in claim 3, wherein: The particle size of the titanium-based composite material powder obtained after sieving in step S3 is 15-53 µm.

5. A method of producing a high wear resistant additive formed titanium matrix composite as claimed in claim 3, wherein: In the application of additive manufacturing of titanium alloy materials.

6. A method of making a high wear resistant additive formed titanium matrix composite according to claim 3, characterized in that:

9. A titanium alloy material additive manufacturing method applied to the high wear resistance additive manufacturing titanium-based composite material of any one of claims 1-2 or the high wear resistance additive manufacturing titanium-based composite material prepared by the preparation method of any one of claims 3-7, characterized in that:

7. A method of making a high wear resistant additive formed titanium matrix composite according to claim 3, characterized in that: 1): a three-dimensional software is used to construct a required part model, and the part model is layered according to the layering analysis requirements; 8. Use of the high wear resistant additive manufactured titanium matrix composite material according to any one of claims 1 to 2 or the high wear resistant additive manufactured titanium matrix composite material produced according to the method of any one of claims 3 to 7, characterized in that: 2): the layered part model is imported into a laser additive manufacturing device, and the titanium-based composite material powder is printed by laser powder bed fusion according to the set process parameters to obtain an in-situ self-grown titanium-based composite material block; 3): the prepared in-situ self-grown titanium-based composite material block is subjected to microstructure characterization and performance verification.

10. The titanium alloy material additive manufacturing method of claim 9, characterized in that: In step 2), the laser power used in the laser powder bed fusion is set to be between 150-200 W, the scanning speed is kept between 1200-1800 mm / s, and the layer thickness is set to be 20-40 µm; the oxygen content of the laser powder bed fusion is controlled to be below 0.200%. ​ ​ ​

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