CN114703394A - High-temperature material and preparation method and application thereof - Google Patents
High-temperature material and preparation method and application thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
- B22F12/10—Auxiliary heating means
- B22F12/13—Auxiliary heating means to preheat the material
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
- B22F12/10—Auxiliary heating means
- B22F12/17—Auxiliary heating means to heat the build chamber or platform
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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- 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
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- 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
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/10—Pre-treatment
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- 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
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C32/001—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 only oxides
- C22C32/0015—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 only oxides with only single oxides as main non-metallic constituents
- C22C32/0031—Matrix based on refractory metals, W, Mo, Nb, Hf, Ta, Zr, Ti, V or alloys thereof
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- 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
- C22C32/0047—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 carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—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 carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
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- 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
- C22C32/0047—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 carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—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 carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
Abstract
The application discloses a high-temperature materialA preparation method and application thereof, relating to the field of aerospace manufacturing; the method aims to solve the problem that the prior art cannot meet the preparation requirements of aerospace high-temperature parts. The preparation method of the high-temperature material comprises the following steps: mixing Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder; 3D printing is carried out on the composite powder as a raw material to obtain the ceramic reinforced Ti2AlNb composite material.
Description
Technical Field
The application relates to the field of aerospace manufacturing, in particular to a high-temperature material and a preparation method and application thereof.
Background
With the rapid development of aerospace technology, the performance requirements on high-temperature structural materials are higher and higher. The conventional preparation methods comprise a smelting method and a powder metallurgy method, and the conventional methods are difficult to meet the requirements of rapid preparation, high efficiency, energy conservation and the like of aerospace high-temperature parts.
Disclosure of Invention
The application mainly aims to provide a high-temperature material, a preparation method and application thereof, and aims to solve the problem that the prior art cannot meet the preparation requirement of aerospace high-temperature parts.
In order to achieve the technical purpose, the technical scheme provided by the application is as follows: a preparation method of a high-temperature material comprises the following steps:
mixing Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder;
3D printing is carried out on the composite powder as a raw material to obtain the ceramic reinforced Ti2AlNb composite material.
As a possible embodiment of the present application, the Ti2The AlNb alloy comprises:
at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta.
As a possible embodiment of the present application, the Ti2The grain size of the AlNb alloy powder is as follows: 53 to 106 μm.
As a possible embodiment of the present application, the ceramic powder comprises: b is4C、TiB2And Y2O3At least one of (1).
In one possible embodiment of the present application, the ceramic powder has a particle size of 0.1 to 5 μm.
As a possible embodiment of the present application, the Ti2The mixing ratio of the AlNb alloy powder to the ceramic powder is as follows: 90-99.5: 0.5-10.
As one possible embodiment of the present application, the ceramic reinforced Ti is obtained by 3D printing the composite powder as a raw material2A step of AlNb composite material comprising:
the composite powder is used as a raw material and is 5-8 multiplied by 10-4Printing under Pa vacuum degree, wherein the thickness of the powder layer is 50-100 mu m, the current of the electron beam is 10-50 mA, the scanning speed of the electron beam is 1.5-3 m/s, the scanning interval is 0.1-0.15 mm, the preheating temperature of the powder layer is 1000-1250 ℃, and the ceramic reinforced Ti is obtained2AlNb composite material.
As one possible embodiment of the present application, the Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder, wherein the step of mixing AlNb alloy powder and ceramic powder comprises the following steps:
mixing Ti2And mixing the AlNb alloy powder and the ceramic powder through ball milling to obtain the composite powder.
As one possible embodiment of the present application, the Ti2Mixing AlNb alloy powder and ceramic powder through ball milling, wherein the ball milling parameters in the step of obtaining the composite powder are as follows:
the ball milling speed is 100-300 rpm, and the ball milling time is 12-24 hours.
In order to achieve the technical purpose, the application also provides a high-temperature material prepared by the preparation method.
As one possible embodiment of the present application, the following components are included in parts by weight:
90-99.5 parts of Ti2AlNb alloy powder and 0.5-10 parts of ceramic powder.
As a possible embodiment of the present application, the Ti2The AlNb alloy comprises:
at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta.
As a possible embodiment of the present application, the Ti2The grain size of the AlNb alloy powder is as follows: 53 to 106 μm.
As one of the present applicationIn one possible embodiment, the ceramic powder comprises: b is4C、TiB2And Y2O3At least one of (1).
In one possible embodiment of the present application, the ceramic powder has a particle size of 0.1 to 5 μm.
In order to achieve the technical purpose, the application also provides an application of the high-temperature material, namely the high-temperature material is applied to the field of aerospace.
Ti2The AlNb metal compound material has the characteristics of low density, high temperature resistance, high strength and the like, and is widely applied to the preparation of high-temperature parts of aerospace engines. But Ti2AlNb metal compound material has limited application in industry due to low room temperature plasticity and wear resistance, and the application strengthens relative Ti by adding ceramic2Room temperature plasticity and wear resistance of the AlNb metal compound material are improved. Preparation of ceramic-reinforced Ti in the prior art2The AlNb composite material is mainly prepared by a smelting method and a powder metallurgy method, but the methods are difficult to meet the requirements of rapid preparation, high efficiency, energy conservation and the like of aerospace high-temperature parts; and, in general, ceramic-reinforced Ti2The parts prepared from the AlNb composite material are complex in structure, so that the preparation difficulty is high. According to the method, the three-dimensional model of the target part is drawn by using drawing software, the three-dimensional model of the target part is guided into layering software connected with a 3D printer for layering, the 3D printing process parameters are determined by combining with 3D printing raw material composite powder, and the 3D printing operation track code is obtained, so that the ceramic reinforced Ti with the complex structure is realized2And the AlNb composite material is quickly formed integrally.
Drawings
In order to more clearly illustrate the embodiments of the present application or the technical solutions in the prior art, the drawings used in the embodiments or the prior art descriptions will be briefly described below, it is obvious that the drawings in the following description are only some embodiments of the present application, and other drawings can be obtained by those skilled in the art according to the structures shown in the drawings without creative efforts.
FIG. 1 is an optical metallographic graph of a high-temperature material according to example 1 of the present application.
The implementation, functional features and advantages of the objectives of the present application will be further explained with reference to the accompanying drawings.
Detailed Description
The technical solutions in the embodiments of the present application will be described clearly and completely with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are only some embodiments of the present application, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application.
With the rapid development of aerospace technology, the performance requirements on high-temperature structural materials are higher and higher. The conventional preparation methods comprise a smelting method and a powder metallurgy method, and the conventional methods are difficult to meet the requirements of rapid preparation, high efficiency, energy conservation and the like of aerospace high-temperature parts.
In order to solve the technical problem, the application provides a preparation method of a high-temperature material, which comprises the following steps:
mixing Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder;
3D printing is carried out on the composite powder as a raw material to obtain the ceramic reinforced Ti2AlNb composite material.
Ti2The AlNb metal compound material has the characteristics of low density, high temperature resistance, high strength and the like, and is widely applied to the preparation of high-temperature parts of aerospace engines. But Ti2AlNb metal compound material has limited application in industry due to low room temperature plasticity and wear resistance, and the application strengthens relative Ti by adding ceramic2Room temperature plasticity and wear resistance of the AlNb metal compound material are improved. Preparation of ceramic-reinforced Ti in the prior art2The AlNb composite material is mainly prepared by a smelting method and a powder metallurgy method, but the methods are generally difficult to meet the requirements of rapid and efficient preparation of aerospace high-temperature parts,Energy conservation and the like; and, in general, ceramic-reinforced Ti2The parts prepared from the AlNb composite material are complex in structure, so that the preparation difficulty is high. According to the method, the three-dimensional model of the target part is drawn by using drawing software, the three-dimensional model of the target part is guided into layering software connected with a 3D printer for layering, the 3D printing process parameters are determined by combining with 3D printing raw material composite powder, and the 3D printing operation track code is obtained, so that the ceramic reinforced Ti with the complex structure is realized2And the AlNb composite material is quickly formed integrally.
Ti2The AlNb metal compound material has the characteristics of low density, high temperature resistance, high strength and the like, and is widely applied to the preparation of high-temperature parts of aerospace engines. As an alternative embodiment of the present application, the Ti2The AlNb alloy comprises: at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta; alternatively, the Ti2The purity of the AlNb alloy was 99.5 at.%. As a possible embodiment of the present application, the Ti2The grain size of the AlNb alloy powder is as follows: 53 to 106 μm.
But Ti2AlNb metal compound material limits the application of the AlNb metal compound material in industry due to low room temperature plasticity and wear resistance, and the application strengthens the AlNb metal compound material relative to Ti by adding ceramic2Room temperature plasticity and wear resistance of the AlNb metal compound material are improved. As a possible embodiment of the present application, the ceramic powder comprises: b is4C、TiB2And Y2O3At least one of (a); optionally, the particle size of the ceramic powder is 0.1-5 μm; optionally, the ceramic powder has a purity of 99.5 at.%. Improving Ti by adding the ceramic powder2The room temperature plasticity and the wear resistance of the AlNb metal compound material are improved, and meanwhile, the Ti is also improved2High temperature resistance of the AlNb metal compound material.
In order to make the high-temperature material have better room-temperature plasticity, wear resistance and high-temperature resistance, as one possible embodiment of the application, the Ti is2The mixing ratio of the AlNb alloy powder to the ceramic powder is as follows: 90-99.5: 0.5-10.
The method comprises the steps of drawing a three-dimensional model of a target part by using drawing software, guiding the three-dimensional model of the target part into layering software connected with a 3D printer for layering, determining 3D printing process parameters by combining 3D printing raw material composite powder, and obtaining a 3D printing operation track code, so that the ceramic reinforced Ti with a complex structure is realized2And (4) quickly and integrally forming the AlNb composite material. As one possible embodiment of the application, the composite powder is used as a raw material to be subjected to 3D printing to obtain the ceramic reinforced Ti2A step of AlNb composite material comprising:
the composite powder is used as a raw material and is 5-8 multiplied by 10-4Printing under Pa vacuum degree, wherein the thickness of the powder layer is 50-100 mu m, the current of the electron beam is 10-50 mA, the scanning speed of the electron beam is 1.5-3 m/s, the scanning interval is 0.1-0.15 mm, the preheating temperature of the powder layer is 1000-1250 ℃, and the ceramic reinforced Ti is obtained2AlNb composite material.
To make Ti2The AlNb alloy powder and the ceramic powder are mixed more uniformly to ensure the printing quality. As one possible embodiment of the present application, the Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder, wherein the step of mixing AlNb alloy powder and ceramic powder comprises the following steps:
mixing Ti2And mixing the AlNb alloy powder and the ceramic powder through ball milling to obtain the composite powder.
As an alternative embodiment of the present application, Ti may be used2Putting the AlNb alloy powder and the ceramic powder into a ball milling tank according to a ratio, and putting the ball milling tank into a vacuum ball mill for low-speed ball milling and mixing to obtain composite powder; and 3D printing is carried out on the composite powder as a raw material to obtain the ceramic reinforced Ti2An AlNb composite material.
To make Ti2The AlNb alloy powder and the ceramic powder are mixed uniformly while maintaining Ti2As an optional embodiment of the present application, the sphericity of the AlNb alloy powder is 100-300 rpm, and the ball milling time is 12-24 hours. Optionally, the ball-milled grinding balls comprise: bearing steel, agate or ZrO2And (5) grinding balls. Alternatively,the vacuum degree of the vacuum planetary ball mill is 1 multiplied by 10-2Pa; the protective atmosphere in the vacuum planetary ball mill comprises: ar with a purity of 99.999 wt.%. Optionally, the rotation speed of the vacuum planetary ball mill is 50-300 rpm, and the ball milling time is 12-24 hours.
As an alternative embodiment of the application, when the vacuum ball mill is used, the vacuum degree of the inner chamber of the ball mill and the vacuum degree of the ball milling tank are reduced to 1 × 10 by a mechanical vacuum pump and a diffusion vacuum pump-2Pa, and introducing high-purity protective gas to make Ti2And uniformly mixing the AlNb powder and the ceramic powder in a protective atmosphere.
Ceramic reinforced Ti is generally prepared2The AlNb composite material is mainly prepared by a smelting method and a powder metallurgy method, but the methods are difficult to meet the requirements of rapid preparation, high efficiency, energy conservation and the like of aerospace high-temperature parts; and, in general, ceramic-reinforced Ti2The parts prepared from the AlNb composite material are complex in structure, so that the preparation difficulty is high. According to the method, the three-dimensional model of the target part is drawn by using drawing software, the three-dimensional model of the target part is guided into layering software connected with a 3D printer for layering, the 3D printing process parameters are determined by combining with 3D printing raw material composite powder, and the 3D printing operation track code is obtained, so that the ceramic reinforced Ti with the complex structure is realized2And the AlNb composite material is quickly formed integrally.
As one possible embodiment of the present application, the step of performing 3D printing on the composite powder as a raw material includes:
pumping the vacuum degree of the electron beam selective melting 3D printer to 6 multiplied by 10-4Pa；
Preheating the substrate through an electron beam, and spreading powder through a scraper when the temperature of the substrate reaches 1000-1300 ℃, wherein the powder spreading thickness is 50-100 mu m; in the printing process, according to different scanning lengths, the current of the electron beam is 10-50 mA, the scanning speed of the electron beam is 0.6-4 m/s, and the scanning distance is 0.1-0.15 mm;
and after printing one layer, descending the workbench, laying the next layer of powder by a scraper, preheating the powder layer by an electron beam, continuing printing after preheating is finished, and repeating the steps until the printing of the part is finished.
As one possible implementation of the present application, ceramic reinforced Ti for 3D printing is effectively reduced2Hot cracks and holes of AlNb material, and improvement of ceramic reinforced Ti2According to the preparation quality of the AlNb material, in the process of parts, the temperature of a substrate is kept between 1000 and 1250 ℃ by preheating a powder layer.
As a possible implementation manner of the present application, after the part printing is completed, the electron beam gun is turned off, and a small amount of He gas or Ar gas with a purity of 99.999 wt.% is charged to melt the forming chamber of the 3D printer in the selective electron beam area and cool down the printed part; and when the temperature of the substrate is reduced to 30 ℃, filling air into the electron beam selective melting 3D printer, opening the furnace door of the device, and taking out the printed parts.
As a possible implementation manner of the present application, an opening is formed above the ball milling tank, so as to facilitate a vacuum system of the vacuum planetary ball mill to vacuumize the ball milling tank; and the open pore of the ball milling tank is adhered with sponge to prevent powder from flying into the vacuum planetary ball mill.
By mixing one or more ceramic powders of different sizes with Ti2Uniformly mixing AlNb alloy powder under the protection of inert gas, and preparing the ceramic reinforced Ti by using an electron beam selective area melting 3D printing technology2The method for preparing the AlNb composite material has the advantages of simple process flow, low cost, high efficiency and the like. And ceramic-reinforced Ti produced by the above method2The AlNb composite material has high density and low thermal deformation, and solves the problem of ceramic reinforced Ti2The AlNb composite material is easy to crack in the 3D printing process. Based on this, the application also provides a high-temperature material, namely, the high-temperature material is prepared by the preparation method.
In order to make the prepared high-temperature material have better room-temperature plasticity, wear resistance and high-temperature resistance, the high-temperature-resistant material comprises the following components in parts by weight:
90-99.5 parts of Ti2AlNb alloy powder and 0.5-10 parts of ceramic powder.
Ti2AlNb metal compound materialThe high-temperature-resistant high-strength high-density polyethylene has the characteristics of low density, high temperature resistance, high strength and the like, and is widely applied to preparation of high-temperature parts of aerospace engines. As an alternative embodiment of the present application, the Ti2The AlNb alloy comprises: at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta; alternatively, the Ti2The purity of the AlNb alloy was 99.5 at.%. As a possible embodiment of the present application, the Ti2The grain diameter of the AlNb alloy powder is as follows: 53 to 106 μm.
But Ti2AlNb metal compound material limits the application of the AlNb metal compound material in industry due to low room temperature plasticity and wear resistance, and the application strengthens the AlNb metal compound material relative to Ti by adding ceramic2Room temperature plasticity and wear resistance of the AlNb metal compound material are improved. As a possible embodiment of the present application, the ceramic powder comprises: b is4C、TiB2And Y2O3At least one of; optionally, the particle size of the ceramic powder is 0.1-5 μm; optionally, the ceramic powder has a purity of 99.5 at.%. Improving Ti by adding the ceramic powder2The room temperature plasticity and the wear resistance of the AlNb metal compound material are improved, and meanwhile, the Ti is also improved2High temperature resistance of the AlNb metal compound material.
In order to achieve the technical purpose, the application also provides the application of the high-temperature material in the aerospace field.
The technical solution described in the present application will be further described in detail with reference to the following specific embodiments:
example 1
Step S1: preparing Ti with chemical composition of Ti-22Al-25Nb (at.%) by plasma rotating electrode method2The AlNb powder has a particle size of 53-106 μm.
Step S2: mixing Ti2AlNb powder and B having a particle size of 0.5 to 2 μm4C powder and Y having a particle diameter of 0.05 to 0.1 μm2O3The powder is mixed according to the mass percentage of 98.9:1:0.1, and the mixed powder is poured into the chamber filled with ZrO2In a ball milling tank for milling balls, the ball material ratio is 20: 1.
Step S3: ball millingThe pot is put into a vacuum ball mill and fixed, a mechanical pump and a diffusion pump are started, and the vacuum degree of the vacuum ball mill is pumped to 1 multiplied by 10-2Pa, then closing the vacuum pump, filling high-purity Ar gas, adjusting the rotating speed of the vacuum ball mill to 100rpm, and carrying out ball milling for 24 hours.
Step S4: and pouring the ball-milling powder out of the ball-milling tank, screening the ball-milling powder with the diameter of 65-150 micrometers by using 100-mesh and 250-mesh screens, and putting the ball-milling powder into a powder box of the selective electron beam melting 3D printer.
Step S5: place the base plate on the workstation of electron beam selective melting 3D printer forming chamber, adjusted base plate and scraper position, closed the furnace gate of electron beam selective melting 3D printer, opened the vacuum mechanical pump and the molecular pump of electron beam selective melting 3D printer, begin the evacuation.
Step S6: and (3) introducing the part digital model into an industrial personal computer of the selective electron beam melting 3D printer, inputting 3D printing process parameters, setting the thickness of the powder layer to be 50 mu m, and setting the scanning interval to be 0.15 mm. When the vacuum degree of the 3D printer reaches 6 multiplied by 10 when the electron beam selective melting-4And when Pa is needed, turning on a power supply of the electron beam gun, and preheating the substrate by defocusing the electron beam.
Step S7: when the temperature of the substrate reaches 1250 ℃, a first layer of powder is paved through a scraper, then the powder layer is continuously preheated through an electron beam, after the preheating is finished, the powder layer is printed through a focused electron beam, the current of the electron beam is set to be 10-50 mA according to different scanning lengths, and the scanning speed is set to be 0.6-4 m/s; and after printing one layer, descending the workbench, laying the next layer of powder by a scraper, preheating the powder layer by an electron beam, continuing printing after preheating is finished, and repeating the steps until the printing of the part is finished. In the printing process, the substrate temperature is kept between 1000 and 1250 ℃ by preheating the powder layer.
Step S8: after printing is finished, closing the electron beam gun, and filling high-purity He gas to melt the forming chamber of the 3D printer and reduce the temperature of printing parts in the selective electron beam melting zone; when the temperature of the substrate is reduced to 30 ℃, air is filled into the electron beam selective melting 3D printer, the furnace door of the device is opened, and the printed parts are taken out.
The method of this example is carried out by adding B4C powder and Ti2Ti in the AlNb powder reacts in situ to generate fine TiB and TiC ceramic phase, thereby preparing TiB + TiC + Y2O3Composite ceramic reinforced Ti2AlNb composite material, the TiB + TiC + Y2O3Composite ceramic reinforced Ti2The optical gold phase diagram of the AlNb composite material is shown in FIG. 1, and it can be seen that the TiB + TiC + Y2O3Composite ceramic reinforced Ti2The AlNb composite material has no obvious crack defects, and the porosity is 99.2%.
Example 2
Step S1: preparing Ti with chemical composition of Ti-22Al-25Nb (at.%) by plasma rotating electrode method2The AlNb powder has a particle size of 53-106 μm.
Step S2: mixing Ti2AlNb powder and LaB with particle size of 0.2-1 μm6The powder is mixed according to the mass percent of 98:2, and the mixed powder is poured into the mixture filled with ZrO2In a ball milling tank for milling balls, the ball material ratio is 20: 1.
Step S3: putting the ball milling tank into a vacuum ball mill, fixing, opening a mechanical pump and a diffusion pump, and pumping the vacuum degree of the vacuum ball mill to 1 × 10-2Pa, then closing the vacuum pump, filling high-purity Ar gas, adjusting the rotating speed of the vacuum ball mill to 100rpm, and carrying out ball milling for 24 hours.
Step S4: and pouring the ball-milling powder out of the ball-milling tank, screening the ball-milling powder with the diameter of 65-150 mu m by using 100 and 250 meshes of screens, and putting the ball-milling powder into a powder box of the selective electron beam melting 3D printer.
Step S5: the method comprises the steps of placing a substrate on a workbench of a forming chamber of the selective electron beam melting 3D printer, adjusting the positions of the substrate and a scraper, closing a furnace door of the selective electron beam melting 3D printer, opening a vacuum mechanical pump and a molecular pump of the selective electron beam melting 3D printer, and starting to vacuumize.
Step S6: and (3) introducing the part digital model into an industrial personal computer of the selective electron beam melting 3D printer, inputting 3D printing process parameters, setting the thickness of the powder layer to be 50 mu m, and setting the scanning interval to be 0.15 mm. When the vacuum degree of the 3D printer is melted in the electron beam selective area6×10-4And when Pa is needed, turning on a power supply of the electron beam gun, and preheating the substrate by defocusing the electron beam.
Step S7: when the temperature of the substrate reaches 1250 ℃, a first layer of powder is paved through a scraper, then the powder layer is continuously preheated through an electron beam, after the preheating is finished, the powder layer is printed through a focused electron beam, the current of the electron beam is set to be 10-50 mA according to different scanning lengths, and the scanning speed is set to be 0.6-4 m/s; and after printing one layer, descending the workbench, laying the next layer of powder by a scraper, preheating the powder layer by an electron beam, continuing printing after preheating is finished, and repeating the steps until the printing of the part is finished. In the printing process, the substrate temperature is kept between 1000 and 1250 ℃ by preheating the powder layer.
Step S8: after printing is finished, closing the electron beam gun, and filling high-purity He gas to melt the forming chamber of the 3D printer and reduce the temperature of printing parts in the selective electron beam melting zone; when the temperature of the substrate is reduced to 30 ℃, air is filled into the electron beam selective melting 3D printer, the furnace door of the device is opened, and the printed parts are taken out.
The method described in this example was carried out by adding LaB6Powder and Ti2Ti and trace O in the AlNb powder react to generate fine TiB and La in situ2O3Ceramic phase, thereby producing TiB + La2O3Composite ceramic reinforced Ti2AlNb composite material.
It can be seen that the present application is achieved by combining one or more ceramic powders of different sizes with Ti2Uniformly mixing AlNb alloy powder under the protection of inert gas, and preparing the ceramic reinforced Ti by using an electron beam selective area melting 3D printing technology2The method for preparing the AlNb composite material has the advantages of simple process flow, low cost, high efficiency and the like. And ceramic-reinforced Ti produced by the above method2The AlNb composite material has high density and low thermal deformation, and solves the problem of ceramic reinforced Ti2The AlNb composite material is easy to crack in the 3D printing process.
The above description is only an alternative embodiment of the present application, and not intended to limit the scope of the present application, and all modifications and equivalents of the technical solutions that can be directly or indirectly applied to other related fields without departing from the spirit of the present application are intended to be included in the scope of the present application.
Claims (16)
1. The preparation method of the high-temperature material is characterized by comprising the following steps of:
mixing Ti2Mixing AlNb alloy powder and ceramic powder to obtain composite powder;
3D printing is carried out on the composite powder as a raw material to obtain the ceramic reinforced Ti2AlNb composite material.
2. The method for preparing a high-temperature material according to claim 1, wherein the Ti is2The AlNb alloy comprises:
at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta.
3. The method for preparing a high-temperature material according to claim 2, wherein the Ti is2The grain diameter of the AlNb alloy powder is as follows: 53 to 106 μm.
4. The method of manufacturing a high-temperature material according to claim 1, wherein the ceramic powder includes: b is4C、TiB2And Y2O3At least one of (a).
5. A method for producing a high-temperature material according to claim 4, wherein the ceramic powder has a particle size of 0.1 to 5 μm.
6. The method for preparing a high-temperature material according to claim 1, wherein the Ti is2The mixing ratio of the AlNb alloy powder to the ceramic powder is as follows: 90-99.5: 0.5-10.
7. The method for preparing the high-temperature material according to claim 1, wherein the composite powder is used as a raw material to be subjected to 3D printing to obtain the high-temperature materialCeramic reinforced Ti2A step of AlNb composite material comprising:
the composite powder is used as a raw material and is 5-8 multiplied by 10-4Printing under Pa vacuum degree, wherein the thickness of the powder layer is 50-100 mu m, the current of the electron beam is 10-50 mA, the scanning speed of the electron beam is 1.5-3 m/s, the scanning interval is 0.1-0.15 mm, the preheating temperature of the powder layer is 1000-1250 ℃, and the ceramic reinforced Ti is obtained2AlNb composite material.
8. The method for preparing a high-temperature material according to claim 1, wherein the step of mixing Ti with the high-temperature material is performed by a chemical vapor deposition method2Mixing AlNb alloy powder and ceramic powder to obtain composite powder, wherein the step of mixing AlNb alloy powder and ceramic powder comprises the following steps:
mixing Ti2And mixing the AlNb alloy powder and the ceramic powder through ball milling to obtain the composite powder.
9. The method for preparing a high-temperature material according to claim 8, wherein the step of adding Ti to the high-temperature material is performed by2Mixing AlNb alloy powder and ceramic powder through ball milling, wherein ball milling parameters in the step of obtaining the composite powder are as follows:
the ball milling speed is 100-300 rpm, and the ball milling time is 12-24 hours.
10. A high-temperature material produced by the production method according to any one of claims 1 to 9.
11. The high-temperature material as claimed in claim 10, which comprises the following components in parts by weight:
90-99.5 parts of Ti2AlNb alloy powder and 0.5-10 parts of ceramic powder.
12. The high temperature material of claim 11, wherein the Ti is2The AlNb alloy comprises:
at least one of Ti-22Al-25Nb, Ti-22Al-27Nb, and Ti-22Al-20Nb-7 Ta.
13. According to the claimThe high-temperature material according to claim 11, wherein the Ti is2The grain size of the AlNb alloy powder is as follows: 53 to 106 μm.
14. The high-temperature material as claimed in claim 11, wherein the ceramic powder comprises: b is4C、TiB2And Y2O3At least one of (a).
15. A high-temperature material according to claim 11, wherein the ceramic powder has a particle size of 0.1 to 5 μm.
16. Use of a high-temperature material according to any one of claims 11-15, wherein the high-temperature material is used in the field of aerospace.
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