WO2022028517A1 - 一种耐磨损梯度界面复相增强钛合金材料及其制备方法 - Google Patents
一种耐磨损梯度界面复相增强钛合金材料及其制备方法 Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 24
- 238000002360 preparation method Methods 0.000 title claims abstract description 9
- 239000000843 powder Substances 0.000 claims abstract description 139
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- 238000002844 melting Methods 0.000 claims abstract description 52
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- 239000010936 titanium Substances 0.000 claims abstract description 50
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Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
- B33Y70/10—Composites of different types of material, e.g. mixtures of ceramics and polymers or mixtures of metals and biomaterials
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0005—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with at least one oxide and at least one of carbides, nitrides, borides or silicides as the main non-metallic constituents
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Definitions
- the invention belongs to the field of ceramic-reinforced titanium-based composite materials, in particular to a wear-resistant gradient interface complex phase-reinforced titanium alloy material and a preparation method thereof.
- Titanium alloys have the characteristics of low density, high specific strength, good corrosion resistance and strong biocompatibility, and are widely used in aerospace, automotive, medical and other fields.
- the hardness of titanium alloys is generally low (generally no more than 350HV 0.2 ), and the wear resistance is poor, which seriously limits its application range and cannot meet the needs of the rapidly developing high-tech fields such as aerospace, electronics and automobile manufacturing.
- it is expected to improve the hardness and wear resistance of the matrix by compounding ceramic reinforcements with high modulus, high strength and high hardness in the titanium alloy matrix.
- Selective rapid melting/solidification accumulation forming is carried out to realize direct rapid forming of complex structural metal components.
- the interaction time between the laser heat source and the pre-laid powder layer is extremely short, so the molten powder has a relatively high cooling rate, which provides favorable conditions for the grain refinement of ceramic-reinforced titanium matrix composites, and the powder particles It is completely melted under the action of high-energy laser beam, so that adjacent scanning tracks or interlayer metallurgical bonding is good, and the forming quality of ceramic reinforced titanium matrix composite parts is improved, thereby improving the mechanical properties of the material.
- the selective laser melting technology breaks through the constraints of the traditional manufacturing process, conforms to the "near net shape" design concept, effectively shortens the development and manufacturing cycle of new products, improves production efficiency, and can form parts with complex geometric shapes, so the selective area is used.
- the preparation of ceramic reinforced titanium matrix composites by laser melting technology has great potential for development.
- the technical problem to be solved by the present invention is to provide a method of adding TiC and TiN composite reinforcing phase to the titanium alloy matrix, and improving the interaction between the reinforcing phase and the matrix through the interaction between the reinforcing phases.
- the interface bonding improves the forming quality of the material, and finally plays a role in improving the mechanical properties of the material.
- a wear-resistant gradient interface multiphase reinforced titanium alloy material comprising a titanium alloy matrix and a TiC ceramic reinforcement phase and a TiN ceramic reinforcement phase dispersed in the titanium alloy matrix;
- the titanium alloy matrix is a titanium-aluminum-molybdenum-vanadium-zirconium alloy, wherein the aluminum content is 5.5-6.5 wt.%, the zirconium content is 1.6-2.0 wt.%, the molybdenum content is 1.0-1.5 wt.%, and the vanadium content is 1.0 ⁇ 1.8wt.%, the balance is Ti.
- TiC ceramic reinforcement phase Through the interaction between the TiC ceramic reinforcement phase and the TiN ceramic reinforcement phase, the interface between the reinforcement phase and the matrix is improved, the forming quality of the material is improved, and finally the mechanical properties of the material are improved.
- the TiC ceramic reinforcing phase accounts for 10-15 wt.% of the total mass of the alloy material.
- the TiN ceramic reinforcing phase accounts for 10-15 wt.% of the total mass of the alloy material.
- the mass fraction of the TiC ceramic reinforcing phase and the TiN ceramic reinforcing phase are equal.
- the present invention also provides a method for preparing the above-mentioned wear-resistant gradient interface complex-phase enhanced titanium alloy material, comprising the following steps:
- step (3) The selective laser melting and forming equipment melts and solidifies the composite powder in step (1) layer by layer according to the file imported in step (2), and finally forms the target part to be created.
- the particle size distribution range of the titanium alloy base powder is 15-53 ⁇ m, the purity is greater than 99.0%, and the powder fluidity is 35-42s/50g.
- the particle size distribution range of the TiC ceramic powder is 2-5 ⁇ m, and the purity is greater than 99%.
- the particle size distribution range of the TiN ceramic powder is 3-10 ⁇ m, and the purity is greater than 99%.
- the ball mill adopts QM series planetary ball mill, adopts stainless steel tank, and the ball milling medium is stainless steel balls with diameters of 6mm, 8mm and 10mm; 400rpm, ball milling time is 4-6h.
- the operation mode of the equipment during ball milling is the interval type, and the air cooling is suspended for 5 minutes after every 15 minutes of operation.
- the ball-milling process requires the protection of inert gas to prevent the titanium-based powder from being oxidized or contaminated during the ball-milling process.
- step (3) use SLM-150 type selective laser melting equipment, which mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling cycle system.
- SLM-150 type selective laser melting equipment which mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling cycle system.
- the sandblasted titanium alloy substrate is fixed on the workbench of the selective laser melting forming equipment and leveled, and then the forming cavity is sealed by a sealing device, evacuated and introduced into an inert gas protective atmosphere.
- the typical selective laser melting forming process is as follows: (a) The powder spreading device evenly spreads the powder to be processed on the forming substrate, and the laser beam scans the slicing area line by line according to the pre-designed scanning path, so that the powder layer rapidly melts/ solidification, thereby obtaining the first two-dimensional plane of the part to be formed; (b) the computer control system lowers the forming substrate by one powder layer thickness, while the piston of the powder supply cylinder rises by one powder layer thickness, and the powder spreading device re-lays a layer to be processed powder, the high-energy laser beam scans the second layer of powder according to the slicing information to obtain the second two-dimensional plane of the part to be formed; (c) repeat step (b), the powder to be processed is formed layer by layer until the part to be formed is processed.
- the laser power of the selected area laser melting and forming is 225-275 W
- the laser scanning speed is 800-1200 mm/s
- the scanning distance is 50 ⁇ m
- the powder thickness is 50 ⁇ m.
- the parameters are determined after process optimization.
- the reinforcing phase of titanium-based composites can be reasonably selected and appropriately added, and the preparation method combined with the cutting-edge selective laser melting technology can effectively adjust the morphology, size and shape of the ceramic reinforcing phase. distribution state, and successfully prepared a titanium matrix composite material with good forming quality and excellent comprehensive properties.
- the titanium-aluminum-molybdenum-vanadium-zirconium alloy material reinforced by TiC and TiN ceramic particles is melted by laser irradiation to form a molten pool, the larger TiC and TiN reinforced phases are partially melted, and the edges and corners are passivated, The fine ceramic particles are completely melted.
- the titanium nitride precipitation phase preferentially selects the incompletely melted titanium carbide ceramic particles as the nucleation point and grows epitaxially, forming burr-like dendrites and wrapping the titanium carbide particles.
- a gradient interface structure of TiC-Ti(C,N)-TiN is formed, which improves the interface bonding between the ceramic reinforcing phase and the titanium matrix and reduces the composite
- the tendency of the material to crack due to stress concentration during the rapid condensation of the melt reduces the cracks in the titanium matrix composite after forming and improves its forming quality and mechanical properties.
- the invention forms a multi-phase enhanced gradient interface between the reinforcing phase and the matrix, improves the interface bonding force, reduces the interface cracking of the titanium-based composite material after selective laser melting and forming, and improves the titanium-based composite material. Forming quality and performance of composites.
- titanium-aluminum-molybdenum-vanadium-zirconium alloy powder and micron-scale TiC and TiN powder are used as raw materials, and the powders are mixed and placed in a QM series planetary ball mill for ball milling and powder mixing, and the ceramic reinforcement is finally obtained through the ball milling process.
- the composite powder with uniform phase distribution and good flow performance is suitable for selective laser melting and forming, and the process is simple and cost-saving.
- the preparation of ceramic-reinforced titanium matrix composites by selective laser melting technology not only shortens the production cycle, improves product production efficiency, but also forms parts with complex geometries almost without subsequent machining.
- the cooling rate of the molten pool during selective laser melting and forming is extremely high, reaching 10 3 to 10 8 K/s, which effectively avoids the formation of coarse dendrites in the traditional processing technology and improves the mechanical properties of the parts.
- the present invention can adjust the laser energy density by changing the laser power and the laser scanning speed. With the change of the laser energy input of the powder bed, the thermodynamic and dynamic characteristics of the molten pool formed by the action of the laser and the powder bed also change. Process parameters, adjust the laser energy input, reduce the generation of metallurgical defects such as spheroidization and porosity, and obtain a gradient interface complex TiC+TiN reinforced titanium-aluminum-molybdenum-vanadium-zirconium composite material with forming quality and wear resistance.
- Example 1 is an optical image of the TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in Example 1.
- FIG. 2 is a schematic diagram of a complex TiC+TiN gradient interface in the TiC+TiN/Titanium-Aluminum-Molybdenum-Vanadium-Zirconium composite material sample prepared in Example 1 and its SEM/EDS image.
- FIG. 3 is an SEM image of the TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in Example 4.
- FIG. 3 is an SEM image of the TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in Example 4.
- FIG. 4 is the SEM image of the TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite sample prepared in Comparative Example 1.
- FIG. 5 is the SEM image of the TiC/titanium-aluminum-molybdenum-vanadium-zirconium composite sample prepared in Comparative Example 2.
- FIG. 6 is a SEM image of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in Comparative Example 3.
- FIG. 6 is a SEM image of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in Comparative Example 3.
- the titanium-aluminum-molybdenum-vanadium-zirconium alloy powder used has an aluminum content of 6.23wt.%, a zirconium content of 1.84wt.%, a molybdenum content of 1.25wt.%, and a vanadium content of 1.53wt.%,
- the balance is Ti, the particle size distribution range is 15-53 ⁇ m, the purity is more than 99.0%, and the powder flowability is 41s/50g.
- the used TiC ceramic powder has a particle size distribution range of 2-5 ⁇ m and a purity greater than 99%.
- the used TiN ceramic powder has a particle size distribution range of 3-10 ⁇ m, and a purity greater than 99%.
- the QM series planetary ball mill is used for ball milling and powder mixing operation.
- the process uses a stainless steel tank, and the ball milling medium is stainless steel grinding balls with diameters of 6mm, 8mm and 10mm.
- the ball milling process parameters are set as: the ratio of ball to material is 2:1, the ball milling speed is 250rpm, and the ball milling time is 4h.
- the operation mode of the equipment during ball milling is the interval type, that is, the air cooling is suspended for 5 minutes after every 15 minutes of operation of the equipment.
- the ball milling process requires argon protection to prevent the titanium-based powder from being oxidized or contaminated during the ball milling process.
- the laser process parameters are set as follows: the laser power is 250W, the laser scanning speed is 1000mm/s, the scanning spacing is 50 ⁇ m, the powder thickness is 50 ⁇ m, the partitioned island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layers is 37 ⁇ m. °.
- the multiphase ceramic reinforced titanium-based composite powder obtained in step (1) is used for selective laser melting forming.
- SLM-150 type selective laser melting equipment is used, the system mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling circulation system.
- the sandblasted titanium alloy substrate was fixed on the table of the selective laser melting forming equipment and leveled, and then the forming cavity was sealed by a sealing device, evacuated and passed into an argon protective atmosphere (the purity of Ar is 99.999 %, the outlet pressure is 30mbar), to ensure that the O2 content in the forming chamber is less than 10ppm.
- the typical selective laser melting forming process is as follows: (a) The powder spreading device evenly spreads the powder to be processed on the forming substrate, and the laser beam scans the slicing area line by line according to the pre-designed scanning path, so that the powder layer rapidly melts- Solidification, thereby obtaining the first two-dimensional plane of the part; (b) the computer control system lowers the forming substrate by one powder layer thickness, on the contrary, makes the piston of the powder supply cylinder rise one powder layer thickness, and the powder spreading device re-lays a layer to be prepared. To process the powder, the laser beam scans the second powder layer according to the slicing information to obtain the second two-dimensional plane of the part; (c) Step (b) is repeated, and the powder to be processed is formed layer by layer until the part is processed.
- the formed substrate was taken out from the equipment, and the parts were separated from the substrate by wire cutting to obtain a TiC+TiN composite ceramic reinforced titanium matrix composite sample.
- the multiphase reinforced titanium matrix composite bulk samples were ground, polished and etched.
- the high-density TiC+TiN/Ti-Aluminum-Molybdenum-Vanadium-Zirconium composite sample prepared by this selective laser melting process has no cracks, and the ceramic reinforcing particles are uniformly distributed in the matrix.
- the optical image of its microstructure is shown in Figure 1. shown.
- the samples prepared in Example 1 were analyzed by SEM and EDS, as shown in FIG. 2 .
- the reinforcing phase in the titanium alloy matrix is that the fine burr-like TiN dendrites wrap the larger TiC particles, and the interdiffusion of C and N atoms occurs at the interface between TiC and TiN to form carbon.
- the titanium nitride diffusion zone no other new phases are formed, which indicates that TiC and TiN form a stable gradient interface structure in the titanium alloy matrix, which reduces the interface stress concentration and avoids the formation of cracks during the rapid solidification process.
- the obtained TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium bulk sample was tested for microhardness at room temperature, and its microhardness could reach 813HV 0.2 , which was 2.32 times that of titanium alloys (the apparent hardness of titanium alloys was 2.32 times). Microhardness is 350HV), with good wear resistance.
- the QM series planetary ball mill is used for ball milling and powder mixing operation.
- the process uses a stainless steel tank, and the ball milling medium is stainless steel grinding balls with diameters of 6mm, 8mm and 10mm.
- the ball milling process parameters are set as: the ratio of ball to material is 2:1, the ball milling speed is 300rpm, and the ball milling time is 5h.
- the operation mode of the equipment during ball milling is the interval type, that is, the air cooling is suspended for 5 minutes after every 15 minutes of operation of the equipment.
- the ball milling process requires argon protection to prevent the titanium-based powder from being oxidized or contaminated during the ball milling process.
- the laser process parameters are set as follows: the laser power is 275W, the laser scanning speed is 1200mm/s, the scanning spacing is 50 ⁇ m, the powder thickness is 50 ⁇ m, the partitioned island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layers is 37 ⁇ m. °.
- the titanium-based composite powder obtained in step (1) is used for selective laser melting and forming.
- SLM-150 type selective laser melting equipment is used, the system mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling circulation system.
- the sandblasted titanium alloy substrate was fixed on the table of the selective laser melting forming equipment and leveled, and then the forming cavity was sealed by a sealing device, evacuated and passed into an argon protective atmosphere (the purity of Ar is 99.999 %, the outlet pressure is 30mbar), to ensure that the O2 content in the forming chamber is less than 10ppm.
- the typical selective laser melting forming process is as follows: (a) The powder spreading device evenly spreads the powder to be processed on the forming substrate, and the laser beam scans the slicing area line by line according to the pre-designed scanning path, so that the powder layer rapidly melts- Solidification, thereby obtaining the first two-dimensional plane of the part; (b) the computer control system lowers the forming substrate by one powder layer thickness, on the contrary, makes the piston of the powder supply cylinder rise one powder layer thickness, and the powder spreading device re-lays a layer to be prepared. To process the powder, the laser beam scans the second powder layer according to the slicing information to obtain the second two-dimensional plane of the part; (c) Step (b) is repeated, and the powder to be processed is formed layer by layer until the part is processed.
- the formed substrate was taken out from the equipment, and the parts were separated from the substrate by wire cutting to obtain a TiC+TiN composite reinforced titanium matrix composite sample.
- the multiphase reinforced titanium matrix composite bulk samples were ground, polished and etched.
- the high-density TiC+TiN/Ti-Aluminum-Molybdenum-Vanadium-Zirconium composite samples prepared by this selective laser melting process have no cracks, and the ceramic reinforcing particles are uniformly distributed in the matrix, and the content of the reinforcing phase is slightly reduced.
- TiC and TiN ceramics The particles form a stable gradient interface structure in the titanium alloy matrix.
- the obtained TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium bulk sample was tested for microhardness at room temperature, and its microhardness was 786HV 0.2 , which was 2.25 times that of titanium alloys (the microhardness of titanium alloys was 786HV 0.2 ).
- the hardness is 350HV) and has good wear resistance.
- the QM series planetary ball mill is used for ball milling and powder mixing operation.
- the process uses a stainless steel tank, and the ball milling medium is stainless steel grinding balls with diameters of 6mm, 8mm and 10mm.
- the ball milling process parameters are set as: the ratio of ball to material is 2:1, the ball milling speed is 400rpm, and the ball milling time is 6h.
- the operation mode of the equipment during ball milling is the interval type, that is, the air cooling is suspended for 5 minutes after every 15 minutes of operation of the equipment.
- the ball milling process requires argon protection to prevent the titanium-based powder from being oxidized or contaminated during the ball milling process.
- the laser process parameters are set as: the laser power is 225W, the laser scanning speed is 800mm/s, the scanning interval is 50 ⁇ m, the powder thickness is 50 ⁇ m, the partitioned island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layers is 37 ⁇ m. °.
- the titanium-based composite powder obtained in step (1) is used for selective laser melting and forming.
- SLM-150 type selective laser melting equipment is used, the system mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling circulation system.
- the sandblasted titanium alloy substrate was fixed on the table of the selective laser melting forming equipment and leveled, and then the forming cavity was sealed by a sealing device, evacuated and passed into an argon protective atmosphere (the purity of Ar is 99.999 %, the outlet pressure is 30mbar), to ensure that the O2 content in the forming chamber is less than 10ppm.
- the typical selective laser melting forming process is as follows: (a) The powder spreading device evenly spreads the powder to be processed on the forming substrate, and the laser beam scans the slicing area line by line according to the pre-designed scanning path, so that the powder layer rapidly melts- Solidification, thereby obtaining the first two-dimensional plane of the part; (b) the computer control system lowers the forming substrate by one powder layer thickness, on the contrary, makes the piston of the powder supply cylinder rise one powder layer thickness, and the powder spreading device re-lays a layer to be prepared. To process the powder, the laser beam scans the second powder layer according to the slicing information to obtain the second two-dimensional plane of the part; (c) Step (b) is repeated, and the powder to be processed is formed layer by layer until the part is processed.
- the formed substrate was taken out from the equipment, and the parts were separated from the substrate by wire cutting to obtain a TiC+TiN composite reinforced titanium matrix composite sample.
- the multiphase reinforced titanium matrix composite bulk samples were ground, polished and etched.
- the high-density TiC+TiN/Titanium-Aluminum-Molybdenum-Vanadium-Zirconium composite sample prepared by this selective laser melting process has no cracks, and the ceramic reinforcing particles are uniformly distributed in the matrix and the content is reduced.
- the obtained TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium bulk sample was tested for microhardness at room temperature, and its microhardness was 769HV 0.2 , which was 2.2 times that of titanium alloys (the microhardness of titanium alloys was 769HV 0.2 ).
- the hardness is 350HV) and has good wear resistance.
- the TiC and TiN ceramic powders were mixed with the titanium-aluminum-molybdenum-vanadium-zirconium alloy powder prepared by the gas atomization method according to the proportion of 10wt.%, and the powder was mixed by ball milling to prepare 20wt.%TiC+TiN/titanium-aluminum- Molybdenum-vanadium-zirconium composite powder.
- the QM series planetary ball mill is used for ball milling and powder mixing operation.
- the process uses a stainless steel tank, and the ball milling medium is stainless steel grinding balls with diameters of 6mm, 8mm and 10mm.
- the ball milling process parameters are set as: the ratio of ball to material is 2:1, the ball milling speed is 250rpm, and the ball milling time is 4h.
- the operation mode of the equipment during ball milling is the interval type, that is, the air cooling is suspended for 5 minutes after every 15 minutes of operation of the equipment.
- the ball milling process requires argon protection to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
- the laser process parameters are set as follows: the laser power is 250W, the laser scanning speed is 1200mm/s, the scanning spacing is 50 ⁇ m, the powder thickness is 50 ⁇ m, the partitioned island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layers is 37 ⁇ m. °.
- the multiphase reinforced titanium-based composite powder obtained in step (1) is used for selective laser melting forming.
- SLM-150 type selective laser melting equipment is used, the system mainly includes YLR-500 type fiber laser, laser forming chamber, automatic powder spreading system, protective atmosphere device, computer control circuit system and cooling circulation system.
- the sandblasted titanium alloy substrate was fixed on the table of the selective laser melting forming equipment and leveled, and then the forming cavity was sealed by a sealing device, evacuated and passed into an argon protective atmosphere (the purity of Ar is 99.999 %, the outlet pressure is 30mbar), to ensure that the O2 content in the forming chamber is less than 10ppm.
- the typical selective laser melting forming process is as follows: (a) The powder spreading device evenly spreads the powder to be processed on the forming substrate, and the laser beam scans the slicing area line by line according to the pre-designed scanning path, so that the powder layer rapidly melts- Solidification, thereby obtaining the first two-dimensional plane of the part; (b) the computer control system lowers the forming substrate by one powder layer thickness, on the contrary, makes the piston of the powder supply cylinder rise one powder layer thickness, and the powder spreading device re-lays a layer to be prepared. To process the powder, the laser beam scans the second powder layer according to the slicing information to obtain the second two-dimensional plane of the part; (c) Step (b) is repeated, and the powder to be processed is formed layer by layer until the part is processed.
- the formed substrate was taken out of the equipment, and the parts were separated from the substrate by wire cutting process to obtain TiC+TiN/Titanium-Aluminum-Molybdenum-Vanadium-Zirconium composite ceramic reinforced titanium matrix composite samples.
- the multiphase reinforced titanium matrix composite bulk samples were ground, polished and etched.
- the TiC+TiN/Titanium-Aluminum-Molybdenum-Vanadium-Zirconium composite sample prepared by this selective laser melting process has no cracks, and the ceramic reinforcing particles are uniformly distributed in the matrix and the content is reduced.
- the SEM image of its microstructure is shown in the figure 3 shown.
- TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium bulk sample was tested for microhardness at room temperature, and its microhardness could reach 758HV 0.2 , which was 2.17 times that of titanium alloys (the apparent hardness of titanium alloys was 758HV 0.2 ). Microhardness is 350HV), with good wear resistance.
- This comparative example is the same as that of Example 1, except that in step (1), the composite powder is prepared by ball-milling process using TiC and TiN composite ceramic powder as reinforcing phase raw materials, but a certain proportion of graphene (15wt.% ), TiN (15wt.%) and titanium-aluminum-molybdenum-vanadium-zirconium powder as raw materials to ensure that the TiC+TiN composite ceramic reinforcement phase content is 30wt.% after in-situ reaction, and the composite powder is prepared by ball milling, And the selective laser melting forming is carried out, and its microstructure is shown in Figure 4.
- the microhardness of the TiC+TiN/Titanium-Aluminum-Molybdenum-Vanadium-Zirconium composite sample prepared in situ in Comparative Example 1 is 724HV 0.2 .
- the titanium-based composite material the hardness decreased significantly.
- This comparative example is the same as that of Example 1, except that in step (1), the composite powder is prepared by ball milling process without using TiC and TiN composite ceramic powder as raw materials, but a single TiC ceramic powder (15wt.%) is used as the raw material
- the composite powder was prepared by ball milling, and then subjected to selective laser melting and forming.
- the microstructure is shown in Figure 5. Comparing Fig. 1 and Fig. 5, it can be found that compared with TiC+TiN/Ti-Al-Mo-V-Zr composites, TiC/Ti-Al-Mo-V-Zr composites form larger sized particles in the microstructure. Cracks were found throughout the entire formed specimen. Larger-sized TiC ceramic particles are not completely melted during the laser forming process.
- the microhardness of the TiC/titanium-aluminum-molybdenum-vanadium-zirconium composite sample prepared in Comparative Example 2 is 681HV 0.2 , which is significantly lower than that of the TiC+TiN composite reinforced titanium-based composite in Example 1. Due to the cracking of the formed sample, the measured value of microhardness fluctuates greatly, which affects the accuracy of the measured value to a certain extent.
- This comparative example is the same as that of Example 1, except that in step (1), the composite powder was prepared by ball milling process without using TiC and TiN composite ceramic powder as raw materials, but a single TiN ceramic powder (15wt.%) was selected as the raw material
- the composite powder was prepared by ball milling, and then subjected to selective laser melting and forming, and its microstructure is shown in Figure 6. Comparing Figure 1 and Figure 6, it can be found that compared with TiC+TiN/Ti-Al-Mo-V-Zr composite, large cracks are formed in the microstructure of TiN/Ti-Al-Mo-V-Zr composite. Larger-sized TiN ceramic particles are also not completely melted during the laser forming process.
- the microhardness of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite sample prepared in Comparative Example 3 is 729HV 0.2 , which is significantly lower than that of the TiC+TiN composite reinforced titanium-based composite in Example 1. Due to the cracking of the formed sample, the measured value of microhardness fluctuates greatly, which affects the accuracy of the measured value to a certain extent.
- step (1) of this comparative example TiC and TiN ceramic powders are mixed with titanium-aluminum-molybdenum-vanadium-zirconium in proportions of 25 wt.% each.
- the metal powders are mixed, and ball-milled and mixed to prepare 50wt% TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder.
- step (1) of this comparative example TiC and TiN ceramic powders are mixed with titanium-aluminum-molybdenum-vanadium-zirconium in proportions of 25 wt.% each.
- the metal powders are mixed, and ball-milled and mixed to prepare 50wt% TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder.
- step (1) of this comparative example due to the excessively high addition of TiC and TiN ceramics, during the subsequent rapid solidification process, it is easy
- the specific steps of this comparative example are basically the same as those of Example 1, except that in steps (2) and (3) of this comparative example, the prepared TiC+TiN/Titanium-Aluminum-Molybdenum -The vanadium-zirconium composite powder is shaped.
- the distribution of ceramic particles in the formed TiC+TiN/titanium-aluminum-molybdenum-vanadium-zirconium sample is uneven, there is no reaction between the ceramic particles and the matrix, and the interface between the two is not well bonded, resulting in this The mechanical properties of the specimens are seriously degraded.
- the microhardness of the formed sample is 554HV 0.2 , which is greatly reduced compared to the titanium-based composite material with the TiC+TiN complex reinforced phase in Example 1.
- Example 1 and Comparative Examples 1 to 5 it can be seen that the cracks of the TiC+TiN composite reinforced composite samples formed by selective laser melting are significantly reduced, the forming quality is significantly improved, the microhardness is maintained at a high level, and it has excellent wear resistance.
- the mechanical properties are optimized, which is 2.1 to 2.3 times that of the titanium alloy microhardness, which is mainly due to the partial melting and interaction of the larger TiC and TiN particles in the titanium alloy matrix during the selective laser melting forming process.
- the fine TiN dendrites are wrapped around the incompletely melted TiC ceramic particles, which improves the interface bonding between the reinforcing particles and the matrix and reduces the titanium matrix composite. Cracks in the material, forming quality and microhardness are significantly improved.
- the present invention provides an idea and method for a wear-resistant gradient interface multiphase reinforced titanium alloy material and a preparation method thereof.
- the above are only the preferred embodiments of the present invention, and should be It is pointed out that for those skilled in the art, without departing from the principle of the present invention, several improvements and modifications can also be made, and these improvements and modifications should also be regarded as the protection scope of the present invention. All components not specified in this embodiment can be implemented by existing technologies.
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Abstract
Description
Claims (10)
- 一种耐磨损梯度界面复相增强钛合金材料,其特征在于,包括钛合金基体以及分散在钛合金基体内的TiC陶瓷增强相和TiN陶瓷增强相;所述钛合金基体为钛-铝-钼-钒-锆合金,其中,铝含量为5.5~6.5wt.%,锆含量1.6~2.0wt.%,钼含量1.0~1.5wt.%,钒含量为1.0~1.8wt.%,余量为Ti。
- 根据权利要求1所述的耐磨损梯度界面复相增强钛合金材料,其特征在于,所述TiC陶瓷增强相占合金材料总质量的10~15wt.%。
- 根据权利要求1所述的耐磨损梯度界面复相增强钛合金材料,其特征在于,所述TiN陶瓷增强相占合金材料总质量的10~15wt.%。
- 根据权利要求1所述的耐磨损梯度界面复相增强钛合金材料,其特征在于,所述TiC陶瓷增强相与TiN陶瓷增强相的质量分数相等。
- 权利要求1所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,包括如下步骤:(1)取钛合金基体粉末、TiC陶瓷粉末、TiN陶瓷粉末通过球磨机在惰性气体保护下进行球磨混合均匀,得到复合粉体;(2)使用Soildworks软件建立目标零件的三维实体几何模型,然后利用Magics软件对该模型进行分层切片并规划激光扫描路径,将三维实体离散成一系列二维数据,保存并导入选区激光熔化成形设备中;(3)选区激光熔化成形设备根据步骤(2)所导入的文件,将步骤(1)中的复合粉体逐层熔化并凝固,最终成形为所要建立的目标零件。
- 根据权利要求5所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,步骤(1)中,所述钛合金基体粉末粒径分布范围在15~53μm,纯度大于99.0%,粉末流动性35~42s/50g。
- 根据权利要求5所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,步骤(1)中,所述TiC陶瓷粉末粒径分布范围在2~5μm,纯度大于99%。
- 根据权利要求5所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,步骤(1)中,所述TiN陶瓷粉末粒径分布范围在3~10μm,纯度大于99%。
- 根据权利要求5所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,步骤(1)中,所述球磨机采用QM系列行星式球磨机,球料比为2:1,球磨转 速为250~400rpm,球磨时间为4~6h。
- 根据权利要求5所述耐磨损梯度界面复相增强钛合金材料的制备方法,其特征在于,步骤(3)中,选区激光熔化成形设备采用的激光功率为225~275W,激光扫描速度为800~1200mm/s。
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Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09176759A (ja) * | 1997-02-07 | 1997-07-08 | Toshiba Corp | 耐浸食合金の製造方法 |
CN104073750A (zh) * | 2014-04-11 | 2014-10-01 | 上海交通大学 | TiC短纤维增强钛基复合材料及其制备方法 |
CN107737932A (zh) * | 2017-10-26 | 2018-02-27 | 西北工业大学 | 一种钛或钛合金选区强化的一体化激光增材制造方法 |
CN107916380A (zh) * | 2017-11-27 | 2018-04-17 | 上海万泽精密铸造有限公司 | 碳纤维增强钛基复合材料及其制备方法 |
CN108213438A (zh) * | 2018-03-29 | 2018-06-29 | 山东建筑大学 | 一种钛合金高强度直齿条加工方法 |
CN108754491A (zh) * | 2018-05-31 | 2018-11-06 | 株洲辉锐增材制造技术有限公司 | 一种钛合金表面改性方法及其表面改性钛合金 |
CN112030037A (zh) * | 2020-08-07 | 2020-12-04 | 南京航空航天大学 | 一种耐磨损梯度界面复相增强钛合金材料及其制备方法 |
Family Cites Families (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4915908A (en) * | 1984-10-19 | 1990-04-10 | Martin Marietta Corporation | Metal-second phase composites by direct addition |
US6221513B1 (en) * | 1998-05-12 | 2001-04-24 | Pacific Coast Technologies, Inc. | Methods for hermetically sealing ceramic to metallic surfaces and assemblies incorporating such seals |
KR101255386B1 (ko) * | 2005-01-31 | 2013-04-17 | 머티리얼즈 앤드 일렉트로케미칼 리써치 코포레이션 | 정밀 정형 티타늄 보디의 저비용 제조 방법 |
CN101775518A (zh) * | 2010-04-02 | 2010-07-14 | 哈尔滨工业大学 | 利用超声波制备颗粒增强梯度复合材料的装置及方法 |
CN103045914A (zh) * | 2012-12-06 | 2013-04-17 | 南京航空航天大学 | 一种纳米碳化硅增强铝基复合材料的制备方法 |
JP6099457B2 (ja) * | 2013-03-28 | 2017-03-22 | 株式会社Pfu | 画像処理装置、領域決定方法及びコンピュータプログラム |
JP5807850B2 (ja) * | 2013-06-10 | 2015-11-10 | 住友電気工業株式会社 | サーメット、サーメットの製造方法、および切削工具 |
FR3008014B1 (fr) * | 2013-07-04 | 2023-06-09 | Association Pour La Rech Et Le Developpement De Methodes Et Processus Industriels Armines | Procede de fabrication additve de pieces par fusion ou frittage de particules de poudre(s) au moyen d un faisceau de haute energie avec des poudres adaptees au couple procede/materiau vise |
US9849532B2 (en) * | 2014-06-12 | 2017-12-26 | Kennametal Inc. | Composite wear pad and methods of making the same |
US10808297B2 (en) * | 2016-11-16 | 2020-10-20 | Hrl Laboratories, Llc | Functionally graded metal matrix nanocomposites, and methods for producing the same |
CN107058901A (zh) * | 2017-02-09 | 2017-08-18 | 江苏汇诚机械制造有限公司 | 一种高强韧耐热TiC/TiN钢结硬质合金的制备方法 |
CN107130138B (zh) * | 2017-05-19 | 2018-09-04 | 淮阴工学院 | 医用高耐磨钛合金复合材料及3d打印梯度原位纳米复相减磨医用钛合金的方法 |
CN108411300A (zh) * | 2018-04-18 | 2018-08-17 | 上海工程技术大学 | 一种钛合金表面激光熔覆镍基自润滑涂层及其制备方法 |
CN110408817A (zh) * | 2019-05-10 | 2019-11-05 | 东北大学 | 一种TiC/TiN/B4C颗粒增强镍基复合材料及其制备方法 |
CN110241419B (zh) * | 2019-07-24 | 2021-04-02 | 青岛滨海学院 | 一种表面具有抗高温氧化和耐磨涂层的钛合金材料及应用 |
-
2020
- 2020-08-07 CN CN202010787663.8A patent/CN112030037B/zh active Active
-
2021
- 2021-08-05 GB GB2218372.7A patent/GB2624471A/en active Pending
- 2021-08-05 WO PCT/CN2021/110799 patent/WO2022028517A1/zh active Application Filing
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09176759A (ja) * | 1997-02-07 | 1997-07-08 | Toshiba Corp | 耐浸食合金の製造方法 |
CN104073750A (zh) * | 2014-04-11 | 2014-10-01 | 上海交通大学 | TiC短纤维增强钛基复合材料及其制备方法 |
CN107737932A (zh) * | 2017-10-26 | 2018-02-27 | 西北工业大学 | 一种钛或钛合金选区强化的一体化激光增材制造方法 |
CN107916380A (zh) * | 2017-11-27 | 2018-04-17 | 上海万泽精密铸造有限公司 | 碳纤维增强钛基复合材料及其制备方法 |
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CN112030037A (zh) | 2020-12-04 |
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