CN112030037B - Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof - Google Patents
Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof Download PDFInfo
- Publication number
- CN112030037B CN112030037B CN202010787663.8A CN202010787663A CN112030037B CN 112030037 B CN112030037 B CN 112030037B CN 202010787663 A CN202010787663 A CN 202010787663A CN 112030037 B CN112030037 B CN 112030037B
- Authority
- CN
- China
- Prior art keywords
- titanium
- powder
- titanium alloy
- tic
- tin
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
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
- C22C1/05—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
Abstract
The invention discloses a wear-resistant gradient interface complex phase reinforced titanium alloy material and a preparation method thereof, wherein the wear-resistant gradient interface complex phase reinforced titanium alloy material comprises a titanium alloy matrix, and a TiC ceramic reinforcing phase and a TiN ceramic reinforcing phase which are 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.%, the vanadium content is 1.0-1.8 wt.%, and the balance is Ti; 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 method is characterized in that titanium-aluminum-molybdenum-vanadium-zirconium alloy powder and micron-sized TiC and TiN powder are used as raw materials, after ball milling and powder mixing, a ceramic reinforced titanium-based composite material is prepared through a selective laser melting technology, a TiC-Ti (C, N) -TiN gradient interface structure is formed, interface combination between a ceramic reinforced phase and a titanium matrix is improved, the tendency of cracking caused by stress concentration of the composite material in a melt rapid condensation process is reduced, cracks in the formed titanium-based composite material are reduced, and forming quality and mechanical properties of the formed titanium-based composite material are improved.
Description
Technical Field
The invention belongs to the field of ceramic reinforced titanium-based composite materials, and particularly relates to a wear-resistant gradient interface complex-phase reinforced titanium alloy material and a preparation method thereof.
Background
The titanium alloy has the characteristics of low density, high specific strength, good corrosion resistance, strong biocompatibility and the like, and is widely applied to the fields of aerospace, automobiles, medical treatment and the like. However, titanium alloys generally have a low hardness (generally no more than 350HV)0.2) The wear resistance is poor, the application range of the wear-resistant rubber is severely limited, and the wear-resistant rubber cannot meet the requirements of high and new technical fields such as aerospace, electronics and automobile manufacturing which are developed rapidly. In order to overcome the defects, the hardness and the wear resistance of the matrix are hopefully improved by compounding the high-modulus, high-strength and high-hardness ceramic reinforcement in the titanium alloy matrix. Among the ceramic reinforcements, TiC and TiN have the advantages of high hardness, high elastic modulus, high tensile strength, good chemical stability and the like, and the density of the TiC and the TiN is close to that of titanium alloy (rho)Titanium alloy＝4.5g/cm3，ρTiC＝4.99g/cm3，ρTiN＝5.43g/cm3) The difference between the thermal expansion coefficient and the titanium alloy is small (alpha)Titanium alloy＝8.8×10-6/K，αTiC＝7.4×10-6/K，αTiN＝9.35×10-6K), therefore, TiC and TiN are desirable reinforcing phases for the preparation of titanium-based composites. However, when the content of the reinforcing phase is high, the viscosity of a liquid phase is increased, the fluidity is poor, ceramic particles cannot be uniformly distributed in the forming process, a relatively thick dendritic crystal structure is formed, the problems of poor interface bonding, cracking and the like are caused, and the forming quality of parts is poor.
From the viewpoint of processing technology, there are many methods for preparing ceramic reinforced titanium-based composite materials at present, such as fusion casting method, powder metallurgy, self-propagating high-temperature synthesis, mechanical alloying method, etc., but the defects of non-uniform distribution of ceramic reinforcement, difficult control of size and shape, poor interface bonding between ceramic reinforcement and matrix, etc. easily occur between ceramic phase and metal matrix due to the difference of components, crystal structure and physicochemical properties, resulting in poor comprehensive performance of the composite materials. The selective laser melting technology is used as a novel laser additive manufacturing technology, based on the local forming principle of layered manufacturing and cumulative superposition, and based on a three-dimensional part model designed by a computer auxiliary, the high-energy laser heat source is utilized to selectively and rapidly melt/solidify, stack and form a metal powder layer in a channel-by-channel layer-by-layer mode, so that the direct and rapid forming of a metal component with a complex structure is realized. In the selective laser melting forming process, the action time of a laser heat source and a pre-laid powder layer is extremely short, so that the molten powder has a quite high cooling speed, favorable conditions are provided for grain refinement of the ceramic reinforced titanium-based composite material, powder particles are completely melted under the action of a high-energy laser beam, adjacent scanning tracks or interlaminar metallurgy are well combined, the forming quality of ceramic reinforced titanium-based composite material parts is improved, and the mechanical property of the material is improved. The selective laser melting technology breaks through the constraint of the traditional manufacturing process, accords with the design concept of near-net-shape forming, effectively shortens the research and development and manufacturing period of new products, improves the production efficiency, and can form parts with complex geometric shapes, so that the selective laser melting technology for preparing the ceramic reinforced titanium-based composite material has great development potential.
Disclosure of Invention
The purpose of the invention is as follows: the technical problem to be solved by the invention is to provide a method for adding TiC and TiN composite reinforced phase into a titanium alloy matrix, and through the interaction between the reinforced phases, the interface combination between the reinforced phase and the matrix is improved, the forming quality of the material is improved, and the mechanical property of the material is finally improved.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
a wear-resistant gradient interface complex phase reinforced titanium alloy material comprises a titanium alloy matrix, and a TiC ceramic reinforcing phase and a TiN ceramic reinforcing phase which are 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.%, the vanadium content is 1.0-1.8 wt.%, and the balance is Ti.
By the interaction between the TiC ceramic reinforcing phase and the TiN ceramic reinforcing phase, the interface combination between the reinforcing phase and the matrix is improved, the forming quality of the material is improved, and the effect of improving the mechanical property of the material is finally achieved. Both TiC and TiN have a face centered cubic crystal structure with a carbon atom radius (R)C0.0077nm) close to the radius of the nitrogen atom (R)N0.0074nm) so that the C atoms in the TiC lattice can be substituted by N atoms in any proportion, and vice versa. Because the atoms are diffused to generate mutual solubility, the two ceramic reinforced phases can form continuous titanium carbonitride Ti (C, N) solid solution under the action of high temperature, so that TiC and TiN become an ideal complex phase reinforcement in the titanium-based composite material.
Preferably, the TiC ceramic reinforcing phase accounts for 10-15 wt% of the total mass of the alloy material.
Preferably, the TiN ceramic reinforcing phase accounts for 10-15 wt% of the total mass of the alloy material.
Most preferably, the mass fraction of the TiC ceramic reinforcing phase and the TiN ceramic reinforcing phase is equal.
Further, the invention also provides a preparation method of the wear-resistant gradient interface complex phase reinforced titanium alloy material, which comprises the following steps:
(1) taking titanium alloy matrix powder, TiC ceramic powder and TiN ceramic powder, and carrying out ball milling and mixing uniformly under the protection of inert gas by a ball mill to obtain composite powder;
(2) establishing a three-dimensional entity geometric model of a target part by using Soildworks software, then carrying out layered slicing on the model by using Magics software, planning a laser scanning path, dispersing a three-dimensional entity into a series of two-dimensional data, storing and guiding the two-dimensional data into selective laser melting forming equipment;
(3) and (3) melting and solidifying the composite powder in the step (1) layer by the selective laser melting and forming equipment according to the file imported in the step (2), and finally forming the target part to be established.
Specifically, in the step (1), the particle size distribution range of the titanium alloy matrix powder is 15-53 mu m, the purity is more than 99.0%, and the powder flowability is 35-42 s/50 g.
Preferably, the grain size distribution range of the TiC ceramic powder is 2-5 mu m, and the purity is more than 99%.
Preferably, the TiN ceramic powder has a particle size distribution range of 3-10 μm and a purity of more than 99%.
Preferably, in the step (1), the ball mill adopts a QM series planetary ball mill, a stainless steel tank is adopted, and the ball milling media are stainless steel milling balls with the diameters of 6mm, 8mm and 10 mm; the ball-material ratio is 2:1, the ball milling rotation speed is 250-400 rpm, and the ball milling time is 4-6 h. In order to prevent the temperature in the ball milling tank from being overhigh, the operation mode of the equipment adopts a spaced mode during ball milling, and air cooling is suspended for 5min after each operation for 15 min. The ball milling process requires that it be conducted under inert gas shielding to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
Preferably, in the step (3), SLM-150 type selective laser melting equipment is used, and the equipment mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, the titanium alloy substrate subjected to sand blasting treatment is fixed on a selective laser melting forming equipment workbench and leveled, and then a forming cavity is sealed through a sealing device, vacuumized and introduced with inert gas protective atmosphere. A typical selective laser fusion forming process is as follows: (a) the powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt/solidify the powder layer, so that a first two-dimensional plane of the part to be formed is obtained; (b) the computer control system enables the forming substrate to descend by one powder layer thickness, the piston of the powder supply cylinder ascends by one powder layer thickness, the powder laying device lays a layer of powder to be processed again, and the high-energy laser beam finishes scanning of the second layer of powder according to the slice information to obtain a second two-dimensional plane of the part to be formed; (c) and (c) repeating the step (b), and forming the powder to be processed layer by layer until the part to be formed is processed.
Preferably, the laser power of the selected area laser melting forming in the step (3) is 225-275W, the laser scanning speed is 800-1200 mm/s, the scanning distance is 50 μm, the powder spreading thickness is 50 μm, a subarea island scanning strategy is adopted, and the laser parameters are determined after process optimization.
The titanium-based composite material reinforcing phase can be reasonably selected and properly added according to the tissue and performance characteristics of the titanium-based composite material, and the preparation method which is combined with the front-edge selective laser melting technology is adopted, so that the appearance, the size and the distribution state of the ceramic reinforcing phase can be effectively adjusted, and the titanium-based composite material with good forming quality and excellent comprehensive performance can be successfully prepared.
Has the advantages that:
1. when the TiC and TiN ceramic particle reinforced titanium-aluminum-molybdenum-vanadium-zirconium alloy material is subjected to laser irradiation to be melted to form a molten pool, the larger TiC and TiN reinforced phase are partially melted, edges and corners are passivated, and fine ceramic particles are completely melted. In the subsequent rapid solidification process, titanium carbide ceramic particles which are not completely melted are preferentially selected as nucleation points by the titanium nitride precipitated phase and epitaxially grow to form burr-shaped dendrites to wrap the titanium carbide particles. Because C and N atoms at the interface of titanium carbide and titanium nitride are mutually diffused, a TiC-Ti (C, N) -TiN gradient interface structure is formed, the interface combination between a ceramic reinforcing phase and a titanium matrix is improved, the tendency of cracking of the composite material due to stress concentration in the melt rapid condensation process is reduced, cracks in the formed titanium-based composite material are reduced, and the forming quality and the mechanical property of the formed titanium-based composite material are improved. According to the invention, through the interaction of TiC and TiN at high temperature, a complex phase enhanced gradient interface is formed between the enhanced phase and the matrix, the interface bonding force is improved, the interface cracking of the titanium-based composite material after selective laser melting forming is reduced, and the forming quality and performance of the titanium-based composite material are improved.
The invention takes titanium-aluminum-molybdenum-vanadium-zirconium alloy powder and micron-sized TiC and TiN powder as raw materials, the powder is mixed and then placed in a QM series planetary ball mill for ball milling and powder mixing, and the composite powder which is provided with uniformly distributed ceramic reinforced phases, good flow property and is suitable for selective laser melting forming is finally obtained through the ball milling process. The ceramic reinforced titanium-based composite material prepared by adopting the selective laser melting technology not only shortens the production period and improves the production efficiency of products, but also can form parts with complex geometric shapes almost without subsequent machining treatment. The cooling speed of the molten pool is extremely high and can reach 10 when the selective laser melting forming is carried out3～108K/s, effectively avoids the generation of thick dendrites in the traditional processing technology, and improves the mechanical property of the part.
3. The invention can adjust the laser energy density by changing the laser power and the laser scanning speed, along with the change of the laser energy input of the powder bed, the thermodynamics and the dynamics characteristics of a molten pool formed by the action of the laser and the powder bed are also changed, and through reasonably selecting the laser process parameters and adjusting the laser energy input, the generation of metallurgical defects such as spheroidization effect, pores and the like is reduced, and the gradient interface complex-phase TiC + TiN enhanced titanium-aluminum-molybdenum-vanadium-zirconium composite material with forming quality and wear resistance is obtained.
Drawings
The foregoing and/or other advantages of the invention will become further apparent from the following detailed description of the invention when taken in conjunction with the accompanying drawings.
FIG. 1 is an optical image of a sample of the TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite prepared in example 1.
FIG. 2 is a schematic view of a gradient interface of complex phase TiC + TiN in a TiC + TiN/Ti-Al-Mo-V-Zr composite sample prepared in example 1 and SEM/EDS images thereof.
FIG. 3 is an SEM image of a sample of a TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite prepared in example 4.
FIG. 4 is an SEM image of a sample of the TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite prepared in comparative example 1.
FIG. 5 is an SEM image of a sample of the TiC/titanium-aluminum-molybdenum-vanadium-zirconium composite prepared in comparative example 2.
FIG. 6 is an SEM image of a sample of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite prepared in comparative example 3.
Detailed Description
The invention will be better understood from the following examples.
In the following examples, a titanium-aluminum-molybdenum-vanadium-zirconium alloy powder was used having an aluminum content of 6.23 wt.%, a zirconium content of 1.84 wt.%, a molybdenum content of 1.25 wt.%, a vanadium content of 1.53 wt.%, and the balance Ti, a particle size distribution in the range of 15 to 53 μm, a purity of more than 99.0%, and a powder flowability of 41s/50 g.
The grain size distribution range of the used TiC ceramic powder is 2-5 mu m, and the purity is more than 99%.
The grain size distribution range of the TiN ceramic powder is 3-10 mu m, and the purity is more than 99%.
Example 1
(1) Mixing TiC ceramic powder and TiN ceramic powder with titanium-aluminum-molybdenum-vanadium-zirconium metal powder according to the proportion of 15 wt% (percentage of the total mass of the alloy material), and performing ball milling and powder mixing to prepare 30 wt% TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a stainless steel tank is adopted in the process, and the ball milling media are stainless steel milling balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling speed is 250rpm, and the ball milling time is 4 h. Meanwhile, in order to prevent the temperature in the ball milling tank from being overhigh, the operation mode of the equipment is selected in a spaced mode during ball milling, namely the air cooling is suspended for 5min after the equipment operates for 15 min. The ball milling process requires that it be carried out under argon protection to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the file and importing the file into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 250W, the laser scanning speed is 1000mm/s, the scanning interval is 50 μm, the powder spreading thickness is 50 μm, a subarea island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the complex-phase ceramic reinforced titanium-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, fixing the titanium alloy substrate subjected to sand blasting treatment on a workbench of selective laser melting forming equipment for leveling, sealing a forming cavity by a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30mbar) to ensure O in a forming chamber2The content is less than 10 ppm. A typical selective laser fusion forming process is as follows: (a) the powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) the computer control system enables the forming substrate to descend by one powder layer thickness, conversely, enables the powder supply cylinder piston to ascend by one powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam completes scanning of a second powder layer according to the slicing information to obtain a second two-dimensional plane of the part; (c) and (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the TiC + TiN complex phase ceramic reinforced titanium-based composite material sample. And (3) grinding, polishing and corroding the complex phase reinforced titanium-based composite material block sample according to a standard metallographic sample preparation method. The high-density TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the selective laser melting process has no crack, ceramic reinforced particles are uniformly distributed in a matrix, and an optical image of a microstructure of the ceramic reinforced particles is shown in figure 1. SEM and EDS analyses were performed on the sample prepared in example 1, see fig. 2. As can be seen from the figure, the reinforcing phase in the titanium alloy matrix is formed by coating tiny burr-shaped TiN dendrites on TiC particles with larger sizes, and mutual diffusion of C and N atoms occurs at the interface between the TiC and the TiN to form a titanium carbonitride diffusion region, and no other new phase is generated, which indicates that the TiC and the TiN form a stable gradient interface structure in the titanium alloy matrix, and reduces the stress concentration of the interface, thereby avoiding the formation of cracks in the rapid solidification process.
The obtained TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium block sample is subjected to room temperature microhardness test, and the microhardness can reach 813HV0.2The micro-hardness of the titanium alloy is 2.32 times that of the titanium alloy (the micro-hardness of the titanium alloy is 350HV), and the titanium alloy has good wear resistance.
Example 2
(1) TiC and TiN ceramic powder are mixed with titanium-aluminum-molybdenum-vanadium-zirconium metal powder according to the proportion of 12.5 wt.% respectively, and ball milling and powder mixing are carried out to prepare 25 wt% TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a stainless steel tank is adopted in the process, and the ball milling media are stainless steel milling balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling speed is 300rpm, and the ball milling time is 5 h. Meanwhile, in order to prevent the temperature in the ball milling tank from being overhigh, the operation mode of the equipment is selected in a spaced mode during ball milling, namely the air cooling is suspended for 5min after the equipment operates for 15 min. The ball milling process requires that it be carried out under argon protection to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the file and importing the file into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 275W, the laser scanning speed is 1200mm/s, the scanning interval is 50 μm, the powder spreading thickness is 50 μm, a subarea island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the titanium-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, fixing the titanium alloy substrate subjected to sand blasting treatment on a workbench of selective laser melting forming equipment for leveling, sealing a forming cavity by a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30mbar) to ensure O in a forming chamber2The content is less than 10 ppm. A typical selective laser fusion forming process is as follows: (a) the powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) the computer control system enables the forming substrate to descend by one powder layer thickness, conversely, enables the powder supply cylinder piston to ascend by one powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam completes scanning of a second powder layer according to the slicing information to obtain a second two-dimensional plane of the part; (c) and (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the TiC + TiN complex phase reinforced titanium-based composite material sample. And (3) grinding, polishing and corroding the complex phase reinforced titanium-based composite material block sample according to a standard metallographic sample preparation method. The high-density TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the selective laser melting process has no crack, ceramic reinforced particles are uniformly distributed in a matrix, the content of a reinforced phase is slightly reduced, and the TiC and TiN ceramic particles form a stable gradient interface structure in the titanium alloy matrix.
The obtained TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium blocky sample is subjected to room temperature microhardness test, and the microhardness is 786HV0.2The micro-hardness of the titanium alloy is 2.25 times that of the titanium alloy (the micro-hardness of the titanium alloy is 350HV), and the titanium alloy has good wear resistance.
Example 3
(1) TiC and TiN ceramic powder are mixed with titanium-aluminum-molybdenum-vanadium-zirconium metal powder according to the proportion of 11 wt.% respectively, and ball milling and powder mixing are carried out to prepare 22 wt% TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a stainless steel tank is adopted in the process, and the ball milling media are stainless steel milling balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling rotation speed is 400rpm, and the ball milling time is 6 h. Meanwhile, in order to prevent the temperature in the ball milling tank from being overhigh, the operation mode of the equipment is selected in a spaced mode during ball milling, namely the air cooling is suspended for 5min after the equipment operates for 15 min. The ball milling process requires that it be carried out under argon protection to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the file and importing the file into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 225W, the laser scanning speed is 800mm/s, the scanning interval is 50 μm, the powder spreading thickness is 50 μm, a subarea island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the titanium-based composite powder prepared in the step (1) to selective laser melting forming. Adopts SLM-150 type selective laser melting equipment, and the system mainly comprises YLR-500 type optical fiber laser, laser forming chamber, automatic powder laying system, protective atmosphere device and meterComputer control circuitry and a cooling circulation system. Before forming, fixing the titanium alloy substrate subjected to sand blasting treatment on a workbench of selective laser melting forming equipment for leveling, sealing a forming cavity by a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30mbar) to ensure O in a forming chamber2The content is less than 10 ppm. A typical selective laser fusion forming process is as follows: (a) the powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) the computer control system enables the forming substrate to descend by one powder layer thickness, conversely, enables the powder supply cylinder piston to ascend by one powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam completes scanning of a second powder layer according to the slicing information to obtain a second two-dimensional plane of the part; (c) and (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the TiC + TiN complex phase reinforced titanium-based composite material sample. And (3) grinding, polishing and corroding the complex phase reinforced titanium-based composite material block sample according to a standard metallographic sample preparation method. The high-density TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the selective laser melting process has no crack generation, and ceramic reinforced particles are uniformly distributed in a matrix and have reduced content.
The obtained TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium blocky sample is subjected to room temperature microhardness test, and the microhardness is 769HV0.2The micro-hardness of the titanium alloy is 2.2 times that of the titanium alloy (the micro-hardness of the titanium alloy is 350HV), and the titanium alloy has good wear resistance.
Example 4
Mixing TiC and TiN ceramic powder with titanium-aluminum-molybdenum-vanadium-zirconium alloy powder prepared by an air atomization method according to the proportion of 10 wt.% of each powder, and performing ball milling on the mixed powder to prepare 20 wt.% of TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a stainless steel tank is adopted in the process, and the ball milling media are stainless steel milling balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling speed is 250rpm, and the ball milling time is 4 h. Meanwhile, in order to prevent the temperature in the ball milling tank from being overhigh, the operation mode of the equipment is selected in a spaced mode during ball milling, namely the air cooling is suspended for 5min after the equipment operates for 15 min. The ball milling process requires that it be carried out under argon protection to prevent oxidation or contamination of the titanium-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the file and importing the file into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 250W, the laser scanning speed is 1200mm/s, the scanning interval is 50 μm, the powder spreading thickness is 50 μm, a subarea island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the complex phase reinforced titanium-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, fixing the titanium alloy substrate subjected to sand blasting treatment on a workbench of selective laser melting forming equipment for leveling, sealing a forming cavity by a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30mbar) to ensure O in a forming chamber2The content is less than 10 ppm. A typical selective laser fusion forming process is as follows: (a) the powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) the computer control system makes the formed substrate descend by one powder layer thicknessConversely, the piston of the powder supply cylinder is raised by the thickness of a powder layer, the powder laying device re-lays a layer of powder to be processed, and the laser beam finishes scanning a second powder layer according to the slice information to obtain a second two-dimensional plane of the part; (c) and (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain a TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium complex phase ceramic reinforced titanium-based composite material sample. And (3) grinding, polishing and corroding the complex phase reinforced titanium-based composite material block sample according to a standard metallographic sample preparation method. The TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the selective laser melting process has no crack generation, the ceramic reinforced particles are uniformly distributed in the matrix and have reduced content, and an SEM image of a microstructure of the ceramic reinforced particles is shown in figure 3.
The obtained TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium blocky sample is subjected to room temperature microhardness test, and the microhardness can reach 758HV0.2The micro-hardness of the titanium alloy is 2.17 times that of the titanium alloy (the micro-hardness of the titanium alloy is 350HV), and the titanium alloy has good wear resistance.
Comparative example 1
The comparative example is the same as the example 1 except that in the step (1), the composite powder is prepared by a ball milling process without using TiC and TiN complex phase ceramic powder as a reinforcing phase raw material, graphene (15 wt.%), TiN (15 wt.%) and titanium-aluminum-molybdenum-vanadium-zirconium powder are used as raw materials according to a certain proportion, the content of TiC and TiN complex phase ceramic reinforcing phase generated after in-situ reaction is ensured to be 30 wt.%, the composite powder is prepared by ball milling, and selective laser melting forming is carried out, wherein the microstructure of the composite powder is shown in FIG. 4. Comparing fig. 1 and fig. 4, it can be seen that the TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material prepared by the in-situ reaction of the comparative example 1 has a microstructure with less particles of the complex phase reinforcing phase and uneven distribution. Under the action of high-energy laser, graphene and titanium alloy react to generate a TiC reinforcing phase, but the two do not completely react due to the selective laser melting rapid cooling/solidification process. Meanwhile, high-content graphene is easy to agglomerate, metallurgical defects such as pores and the like are generated in a laser forming sample, and titanium-based complex is reducedThe quality of the composite material. Comparative example 1 the microhardness of a TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite sample prepared in situ is 724HV0.2Compared with the titanium-based composite material directly added with the TiC + TiN complex phase reinforcing phase in the embodiment 1, the hardness is obviously reduced.
Comparative example 2
The comparative example is the same as the example 1 except that in the step (1), the composite powder is prepared by ball milling without using TiC and TiN multiphase ceramic powder as the raw material, and the composite powder is prepared by ball milling with single TiC ceramic powder (15 wt.%) as the raw material, and the area-selection laser melting forming is carried out, wherein the microstructure of the area-selection laser melting forming is shown in FIG. 5. Comparing fig. 1 and 5, it can be seen that cracks of larger size are formed in the microstructure of the TiC/titanium-aluminum-molybdenum-vanadium-zirconium composite and extend through the entire formed specimen, as compared to the TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite. The TiC ceramic particles with larger size are not completely melted in the laser forming process, and stress concentration is easy to occur at the edges of the brittle TiC ceramic particles in the non-equilibrium process of laser rapid solidification, so that cracks are generated prematurely and are expanded to the whole sample; meanwhile, high residual stress is easily generated at the interface of the ceramic/substrate, so that the bonding force of the interface of the ceramic/substrate is low, cracking is induced, and early fracture failure occurs, thereby reducing the forming quality and performance of the material. The TiC/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the comparative example 2 has the microhardness of 681HV0.2Compared with the titanium-based composite material of the TiC + TiN complex phase reinforcing phase in the embodiment 1, the hardness is obviously reduced. Because the formed sample is cracked, the fluctuation of the measured value of the microhardness is large, and the accuracy of the measured value is influenced to a certain extent.
Comparative example 3
The comparative example is the same as the example 1 except that in the step (1), the composite powder is prepared by ball milling without using TiC and TiN multiphase ceramic powder as raw materials, and the composite powder is prepared by ball milling with single TiN ceramic powder (15 wt.%) as raw materials, and the area-selection laser melting forming is carried out, wherein the microstructure of the area-selection laser melting forming is shown in FIG. 6. Comparing fig. 1 and 6, it can be seen that large cracks are formed in the microstructure of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite compared to the TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite. Large size TiN ceramic particlesThe granules are not completely melted in the laser forming process, and stress concentration is easy to occur at the edges of the brittle TiN ceramic granules with larger size and cracks are generated too early in the unbalanced process of laser rapid solidification; meanwhile, high residual stress is easily generated at the interface of the ceramic/substrate, so that the bonding force of the interface of the ceramic/substrate is low, cracking is induced, and early fracture failure occurs, thereby reducing the forming quality and performance of the material. The microhardness of the TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite material sample prepared in the comparative example 3 is 729HV0.2Compared with the titanium-based composite material of the TiC + TiN complex phase reinforcing phase in the embodiment 1, the hardness is obviously reduced. Because the formed sample is cracked, the fluctuation of the measured value of the microhardness is large, and the accuracy of the measured value is influenced to a certain extent.
Comparative example 4
The specific procedure of this comparative example is substantially the same as example 1, except that: in the step (1) of the comparative example, the TiC and TiN ceramic powders are mixed with the titanium-aluminum-molybdenum-vanadium-zirconium metal powder according to the proportion of 25 wt.% of each, and the ball milling mixed powder is carried out to prepare the 50 wt% TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder. In the comparative example, because the addition amount of TiC and TiN ceramics is too high, high residual stress is easily generated at the edge of the ceramic particles in the subsequent rapid solidification process, stress concentration occurs and early fracture occurs, so that the formed sample is seriously deformed and cracked, and the mechanical property is greatly reduced.
Comparative example 5
The specific procedure of this comparative example is substantially the same as example 1, except that: in steps (2) and (3) of the comparative example, the prepared TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium composite powder is formed by a hot isostatic pressing method. In the comparative example, ceramic particles in the formed TiC + TiN/titanium-aluminum-molybdenum-vanadium-zirconium sample are not uniformly distributed, the ceramic particles and the matrix do not react, and the interface bonding between the ceramic particles and the matrix is poor, so that the mechanical property of the sample is seriously reduced. Microhardness of the formed sample was 554HV0.2Compared with the titanium-based composite material of TiC + TiN complex phase reinforced phase in the embodiment 1, the hardness is greatly reduced.
As can be seen from the embodiment 1 and the comparative examples 1 to 5, cracks of a TiC + TiN complex phase reinforced composite material sample formed by selective laser melting are obviously reduced, the forming quality is obviously improved, the microhardness is maintained at a higher level, the TiC + TiN complex phase reinforced composite material sample has excellent wear resistance, the mechanical property is optimized and is 2.1 to 2.3 times of the microhardness of the titanium alloy, the TiC + TiN complex phase reinforced composite material sample is mainly attributed to that the larger TiC and TiN particles are partially melted in the titanium alloy matrix and interact in the selective laser melting forming process to form a TiC-Ti (C, N) -TiN gradient interface structure, fine TiN dendrites wrap around the TiC ceramic particles which are not completely melted, the interface combination between the reinforced particles and the matrix is improved, the cracks in the titanium matrix composite material are reduced, and the forming quality and the microhardness are obviously improved.
The invention provides a thought and a method for a wear-resistant gradient interface complex phase reinforced titanium alloy material and a preparation method thereof, and a method and a way for realizing the technical scheme are numerous, the above description is only a preferred embodiment of the invention, and it should be noted that for a person skilled in the art, a plurality of improvements and decorations can be made without departing from the principle of the invention, and the improvements and decorations should also be regarded as the protection scope of the invention. All the components not specified in the present embodiment can be realized by the prior art.
Claims (8)
1. A wear-resistant gradient interface complex phase reinforced titanium alloy material is characterized by consisting of a titanium alloy matrix, and a TiC ceramic reinforced phase and a TiN ceramic reinforced phase which are 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.%, the vanadium content is 1.0-1.8 wt.%, and the balance is Ti;
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;
and a TiC-Ti (C, N) -TiN gradient interface structure is formed at the interface of the titanium carbide and the titanium nitride.
2. The wear-resistant gradient interface complex phase reinforced titanium alloy material as recited in claim 1, wherein the mass fraction of the TiC ceramic reinforcing phase and the TiN ceramic reinforcing phase are equal.
3. The preparation method of the wear-resistant gradient interface complex phase reinforced titanium alloy material as recited in claim 1, characterized by comprising the following steps:
(1) taking titanium alloy matrix powder, TiC ceramic powder and TiN ceramic powder, and carrying out ball milling and mixing uniformly under the protection of inert gas by a ball mill to obtain composite powder;
(2) establishing a three-dimensional entity geometric model of a target part by using Soildworks software, then carrying out layered slicing on the model by using Magics software, planning a laser scanning path, dispersing a three-dimensional entity into a series of two-dimensional data, storing and guiding the two-dimensional data into selective laser melting forming equipment;
(3) and (3) melting and solidifying the composite powder in the step (1) layer by the selective laser melting and forming equipment according to the file imported in the step (2), and finally forming the target part to be established.
4. The preparation method of the wear-resistant gradient interface complex-phase reinforced titanium alloy material as claimed in claim 3, wherein in the step (1), the particle size distribution range of the titanium alloy matrix powder is 15-53 μm, the purity is more than 99.0%, and the powder fluidity is 35-42 s/50 g.
5. The preparation method of the wear-resistant gradient interface complex-phase reinforced titanium alloy material as claimed in claim 3, wherein in the step (1), the grain size distribution range of the TiC ceramic powder is 2-5 μm, and the purity is greater than 99%.
6. The preparation method of the wear-resistant gradient interface complex-phase reinforced titanium alloy material as claimed in claim 3, wherein in the step (1), the TiN ceramic powder has a particle size distribution range of 3-10 μm and a purity of more than 99%.
7. The preparation method of the wear-resistant gradient interface complex-phase reinforced titanium alloy material as claimed in claim 3, wherein in the step (1), the ball mill is a QM series planetary ball mill, the ball-to-material ratio is 2:1, the ball milling rotation speed is 250-400 rpm, and the ball milling time is 4-6 h.
8. The preparation method of the wear-resistant gradient interface complex-phase reinforced titanium alloy material as claimed in claim 3, wherein in the step (3), the laser power adopted by the selective laser melting forming equipment is 225-275W, and the laser scanning speed is 800-1200 mm/s.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010787663.8A CN112030037B (en) | 2020-08-07 | 2020-08-07 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof |
| GBGB2218372.7A GB202218372D0 (en) | 2020-08-07 | 2021-08-05 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method therefor |
| PCT/CN2021/110799 WO2022028517A1 (en) | 2020-08-07 | 2021-08-05 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method therefor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010787663.8A CN112030037B (en) | 2020-08-07 | 2020-08-07 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112030037A CN112030037A (en) | 2020-12-04 |
| CN112030037B true CN112030037B (en) | 2021-08-06 |
Family
ID=73582729
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010787663.8A Active CN112030037B (en) | 2020-08-07 | 2020-08-07 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof |
Country Status (3)
| Country | Link |
|---|---|
| CN (1) | CN112030037B (en) |
| GB (1) | GB202218372D0 (en) |
| WO (1) | WO2022028517A1 (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112030037B (en) * | 2020-08-07 | 2021-08-06 | 南京航空航天大学 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof |
| CN113843419A (en) * | 2021-09-04 | 2021-12-28 | 安徽中科春谷激光产业技术研究院有限公司 | Selective laser melting preparation in-situ generated TiC + Ti3SiC2Method for reinforcing titanium-based composite material |
| CN114807928B (en) * | 2022-04-22 | 2023-05-16 | 西安石油大学 | Titanium alloy surface bionic high-entropy alloy tissue wear-resistant layer and preparation method and application thereof |
| CN115533116A (en) * | 2022-09-19 | 2022-12-30 | 华东理工大学 | Multicomponent alloy composite material and preparation method thereof |
| CN115415513B (en) * | 2022-09-23 | 2023-04-28 | 西北工业大学 | Titanium alloy and ceramic reinforced phase ball milling powder mixing process optimization method based on uniformity |
| CN116397133A (en) * | 2023-05-18 | 2023-07-07 | 大连理工大学 | Porcelain powder reinforced titanium-based alloy composite material based on SLM (selective laser sintering) forming and preparation method thereof |
| CN117418143B (en) * | 2023-12-19 | 2024-03-26 | 汕头大学 | Ceramic reinforced metal matrix composite gradient coating and preparation method and application thereof |
Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1988003574A1 (en) * | 1986-11-05 | 1988-05-19 | Martin Marietta Corporation | Process for producing metal-second phase composites and product |
| 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 |
| CN101223294A (en) * | 2005-01-31 | 2008-07-16 | 材料及电化学研究公司 | Method for the manufacture of titanium alloy structure |
| CN101775518A (en) * | 2010-04-02 | 2010-07-14 | 哈尔滨工业大学 | Device and method for preparing particle-reinforced gradient composite materials by using ultrasonic waves |
| CN103045914A (en) * | 2012-12-06 | 2013-04-17 | 南京航空航天大学 | Preparation method of nano silicon carbide reinforced aluminum-based composite material |
| CN105308200A (en) * | 2013-06-10 | 2016-02-03 | 住友电气工业株式会社 | Cermet, method for producing cermet, and cutting tool |
| CN105764634A (en) * | 2013-07-04 | 2016-07-13 | 斯内克马公司 | Process for additive manufacturing of parts by melting or sintering particles of powder(s) using a high-energy beam with powders adapted to the targeted process/material pair |
| CN107058901A (en) * | 2017-02-09 | 2017-08-18 | 江苏汇诚机械制造有限公司 | A kind of preparation method of high-toughness heat-resistant TiC/TiN steel bonded carbide |
| CN107130138A (en) * | 2017-05-19 | 2017-09-05 | 淮阴工学院 | The method of medical high abrasion titanium alloy composite material and 3D printing gradient in-situ nano complex phase anti-attrition medical titanium alloy |
| CN108411300A (en) * | 2018-04-18 | 2018-08-17 | 上海工程技术大学 | A kind of Laser Cladding on Titanium Alloy nickel-based self-lubricating coating and preparation method thereof |
| CN110241419A (en) * | 2019-07-24 | 2019-09-17 | 青岛滨海学院 | A kind of surface has titanium alloy material and the application of resistance to high temperature oxidation and wear-resistant coating |
| CN110408817A (en) * | 2019-05-10 | 2019-11-05 | 东北大学 | A kind of TiC/TiN/B4C particle enhanced nickel base composite material and preparation method thereof |
| US10865464B2 (en) * | 2016-11-16 | 2020-12-15 | Hrl Laboratories, Llc | Materials and methods for producing metal nanocomposites, and metal nanocomposites obtained therefrom |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09176759A (en) * | 1997-02-07 | 1997-07-08 | Toshiba Corp | Production of erosion resistant alloy |
| CN104073750B (en) * | 2014-04-11 | 2016-02-10 | 上海交通大学 | TiC short fiber reinforced titanium matrix composite and preparation method thereof |
| US9849532B2 (en) * | 2014-06-12 | 2017-12-26 | Kennametal Inc. | Composite wear pad and methods of making the same |
| CN107737932B (en) * | 2017-10-26 | 2019-08-06 | 西北工业大学 | A kind of integrated laser increasing material manufacturing method that titanium or titanium alloy constituency are strengthened |
| CN107916380A (en) * | 2017-11-27 | 2018-04-17 | 上海万泽精密铸造有限公司 | Fibre reinforced titanium matrix composite and preparation method thereof |
| CN108213438A (en) * | 2018-03-29 | 2018-06-29 | 山东建筑大学 | A kind of titanium alloy high-strength direct rack processing method |
| CN108754491A (en) * | 2018-05-31 | 2018-11-06 | 株洲辉锐增材制造技术有限公司 | A kind of titanium alloy surface method of modifying and its surface modified titanium alloy |
| CN112030037B (en) * | 2020-08-07 | 2021-08-06 | 南京航空航天大学 | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof |
-
2020
- 2020-08-07 CN CN202010787663.8A patent/CN112030037B/en active Active
-
2021
- 2021-08-05 GB GBGB2218372.7A patent/GB202218372D0/en active Pending
- 2021-08-05 WO PCT/CN2021/110799 patent/WO2022028517A1/en active Application Filing
Patent Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1988003574A1 (en) * | 1986-11-05 | 1988-05-19 | Martin Marietta Corporation | Process for producing metal-second phase composites and product |
| 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 |
| CN101223294A (en) * | 2005-01-31 | 2008-07-16 | 材料及电化学研究公司 | Method for the manufacture of titanium alloy structure |
| CN101775518A (en) * | 2010-04-02 | 2010-07-14 | 哈尔滨工业大学 | Device and method for preparing particle-reinforced gradient composite materials by using ultrasonic waves |
| CN103045914A (en) * | 2012-12-06 | 2013-04-17 | 南京航空航天大学 | Preparation method of nano silicon carbide reinforced aluminum-based composite material |
| CN105308200A (en) * | 2013-06-10 | 2016-02-03 | 住友电气工业株式会社 | Cermet, method for producing cermet, and cutting tool |
| CN105764634A (en) * | 2013-07-04 | 2016-07-13 | 斯内克马公司 | Process for additive manufacturing of parts by melting or sintering particles of powder(s) using a high-energy beam with powders adapted to the targeted process/material pair |
| US10865464B2 (en) * | 2016-11-16 | 2020-12-15 | Hrl Laboratories, Llc | Materials and methods for producing metal nanocomposites, and metal nanocomposites obtained therefrom |
| CN107058901A (en) * | 2017-02-09 | 2017-08-18 | 江苏汇诚机械制造有限公司 | A kind of preparation method of high-toughness heat-resistant TiC/TiN steel bonded carbide |
| CN107130138A (en) * | 2017-05-19 | 2017-09-05 | 淮阴工学院 | The method of medical high abrasion titanium alloy composite material and 3D printing gradient in-situ nano complex phase anti-attrition medical titanium alloy |
| CN108411300A (en) * | 2018-04-18 | 2018-08-17 | 上海工程技术大学 | A kind of Laser Cladding on Titanium Alloy nickel-based self-lubricating coating and preparation method thereof |
| CN110408817A (en) * | 2019-05-10 | 2019-11-05 | 东北大学 | A kind of TiC/TiN/B4C particle enhanced nickel base composite material and preparation method thereof |
| CN110241419A (en) * | 2019-07-24 | 2019-09-17 | 青岛滨海学院 | A kind of surface has titanium alloy material and the application of resistance to high temperature oxidation and wear-resistant coating |
Non-Patent Citations (5)
| Title |
|---|
| Development of interfacial stress during selective laser melting of TiC reinforced TiAl composites: Influence of geometric feature of reinforcement;Chenglong Ma等;《Materials and Design》;20180718;1-11 * |
| Interfacial structure and wear properties of selective laser melted Ti/(TiC+TiN) composites with high content of reinforcements;Lixia Xi等;《Journal of Alloys and Compounds 》;20210310;1-9 * |
| Microstructure and corrosion behavior of TiC/Ti(CN)/TiN multilayer CVD coatings on high strength steels;Jin Zhang等;《Applied Surface Science》;20130518;626-631 * |
| Ti合金插层厚度对反应连接TiB2基陶瓷ｉ－６Ａｌ－４Ｖ梯度复合材料的影响;宋亚林等;《复合材料学报》;20160831;1769-1776 * |
| 基于选区激光熔化的金属零件快速成形现状与技术展望;顾冬冬等;《航空制造技术》;20120831;32-37 * |
Also Published As
| Publication number | Publication date |
|---|---|
| GB202218372D0 (en) | 2023-01-18 |
| CN112030037A (en) | 2020-12-04 |
| WO2022028517A1 (en) | 2022-02-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112030037B (en) | Wear-resistant gradient interface complex-phase reinforced titanium alloy material and preparation method thereof | |
| Shi et al. | Development of metal matrix composites by laser-assisted additive manufacturing technologies: a review | |
| Dadbakhsh et al. | Selective laser melting to manufacture “in situ” metal matrix composites: a review | |
| Cai et al. | In-situ preparation and formation of TiB/Ti-6Al-4V nanocomposite via laser additive manufacturing: Microstructure evolution and tribological behavior | |
| Zhou et al. | Microstructure evolution and mechanical properties of in-situ Ti6Al4V–TiB composites manufactured by selective laser melting | |
| Zhang et al. | Influence of Y2O3 addition on the microstructure of TiC reinforced Ti-based composite coating prepared by laser cladding | |
| Guo et al. | Selective laser melting additive manufacturing of pure tungsten: Role of volumetric energy density on densification, microstructure and mechanical properties | |
| Wang et al. | Microstructure evolution and EBSD analysis of a graded steel fabricated by laser additive manufacturing | |
| Hu et al. | Laser engineered net shaping of quasi-continuous network microstructural TiB reinforced titanium matrix bulk composites: Microstructure and wear performance | |
| Gu et al. | Laser additive manufacturing (AM): classification, processing philosophy, and metallurgical mechanisms | |
| Jia et al. | Selective laser melting additive manufacturing of TiC/Inconel 718 bulk-form nanocomposites: Densification, microstructure, and performance | |
| Chen et al. | In situ TiC/Inconel 625 nanocomposites fabricated by selective laser melting: Densification behavior, microstructure evolution, and wear properties | |
| Xue et al. | Effect of SiC particle size on densification behavior and mechanical properties of SiCp/AlSi10Mg composites fabricated by laser powder bed fusion | |
| CN105803271A (en) | Aluminium-based nanocomposite based on SLM forming and preparation method of nanocomposite | |
| Oyelola et al. | Machining of functionally graded Ti6Al4V/WC produced by directed energy deposition | |
| Verma et al. | Effect of boron addition on microstructure, hardness and wear performance of Ti-6Al-4 V alloy manufactured by laser powder bed fusion additive manufacturing | |
| CN111500905A (en) | High-silicon aluminum alloy modified based on selective laser melting nano ceramic | |
| Gao et al. | Strengthening mechanism of Y2O3 nanoparticles on microstructure and mechanical properties of the laser additive manufacturing joint for large thickness TC4 titanium alloy | |
| Shalnova et al. | Direct energy deposition of SiC reinforced Ti–6Al–4V metal matrix composites: Structure and mechanical properties | |
| Xiao et al. | In-situ synthesis of high strength and toughness TiN/Ti6Al4V sandwich composites by laser powder bed fusion under a nitrogen-containing atmosphere | |
| CN105728725A (en) | Method for preparing multielement transition interface cooperative-reinforced nickel base composite material by 3D printing | |
| Gong et al. | Laser energy density dependence of performance in additive/subtractive hybrid manufacturing of 316L stainless steel | |
| CN113881873B (en) | High-density trans-scale solid solution ceramic reinforced aluminum matrix composite and preparation method thereof | |
| Luo et al. | Microstructural evolution and mechanical properties of Alloy 718 fabricated by selective laser melting following different post-treatments | |
| Wang et al. | Cracking mechanism and its susceptibility to scanning speed during laser power bed fusion processed high-strength 2024Al alloy |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |