CN109694971B - Powder metallurgy titanium-aluminum-based composite material and preparation method thereof - Google Patents
Powder metallurgy titanium-aluminum-based composite material and preparation method thereof Download PDFInfo
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- CN109694971B CN109694971B CN201910068972.7A CN201910068972A CN109694971B CN 109694971 B CN109694971 B CN 109694971B CN 201910068972 A CN201910068972 A CN 201910068972A CN 109694971 B CN109694971 B CN 109694971B
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- 239000002131 composite material Substances 0.000 title claims abstract description 53
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 title claims abstract description 51
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 18
- 238000002360 preparation method Methods 0.000 title claims abstract description 17
- 239000000843 powder Substances 0.000 claims abstract description 79
- 239000002245 particle Substances 0.000 claims abstract description 17
- 238000000713 high-energy ball milling Methods 0.000 claims abstract description 9
- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Inorganic materials O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 claims abstract description 9
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims abstract description 4
- 238000000498 ball milling Methods 0.000 claims description 32
- 238000005245 sintering Methods 0.000 claims description 25
- 238000000034 method Methods 0.000 claims description 19
- 238000010438 heat treatment Methods 0.000 claims description 12
- 229910000831 Steel Inorganic materials 0.000 claims description 10
- 239000010959 steel Substances 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 8
- 238000001035 drying Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 17
- 239000000956 alloy Substances 0.000 abstract description 11
- 229910045601 alloy Inorganic materials 0.000 abstract description 10
- 238000005275 alloying Methods 0.000 abstract description 8
- 239000002994 raw material Substances 0.000 abstract description 3
- 238000005452 bending Methods 0.000 abstract description 2
- 239000011159 matrix material Substances 0.000 description 10
- 230000008569 process Effects 0.000 description 8
- 238000002490 spark plasma sintering Methods 0.000 description 8
- 238000004321 preservation Methods 0.000 description 7
- 239000010936 titanium Substances 0.000 description 7
- 239000013078 crystal Substances 0.000 description 6
- 229910000838 Al alloy Inorganic materials 0.000 description 5
- 229910010038 TiAl Inorganic materials 0.000 description 5
- 239000011812 mixed powder Substances 0.000 description 5
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 5
- 238000001291 vacuum drying Methods 0.000 description 5
- 238000000227 grinding Methods 0.000 description 4
- 238000011065 in-situ storage Methods 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- 229910052593 corundum Inorganic materials 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 229910001845 yogo sapphire Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000003631 expected effect Effects 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000009740 moulding (composite fabrication) Methods 0.000 description 1
- 238000007709 nanocrystallization Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 229910006281 γ-TiAl Inorganic materials 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- 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
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22C32/001—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
- C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
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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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
- B22F2003/1051—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding by electric discharge
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- Metallurgy (AREA)
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- Optics & Photonics (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a powder metallurgy titanium-aluminum-based composite material and a preparation method thereof, wherein the composite material comprises the following element powder components in percentage by weight: 30.0-40.0% of Ti powder and TiO22.0-8.0% of powder and Nb2O51.0-5.0% of powder and the balance of Al powder. The invention takes the element powder as the raw material, can realize the alloying among the alloy elements by high-energy ball milling, and prepare the titanium-aluminum-based composite material, and the preparation method has the advantages of simple and easy operation, simple preparation process flow, simple and convenient equipment operation, and cheap and easily obtained raw materials. The obtained composite material has fine tissue particles which can reach the nanometer level, is uniformly distributed, has higher bending strength, compressive strength, hardness and interface strength, further improves the stability and wear resistance, realizes that the titanium-aluminum-based composite material with better performance can be obtained under the condition of low cost, and has wider application in the field of high-temperature structural materials.
Description
Technical Field
The invention relates to a preparation method of a titanium-aluminum-based composite material, in particular to a powder metallurgy titanium-aluminum-based composite material and a preparation method thereof, belonging to the technical field of high-temperature structural material processing.
Background
At present, with the rapid development of the industry in China, the titanium-aluminum-based alloy has higher and higher requirements on the application aspect of materials, and as a new metal compound structural material, the titanium-aluminum-based alloy has a series of characteristics of high melting point, low density, high specific strength, high specific modulus and the like, and in addition, the titanium-aluminum-based alloy can still maintain high enough strength and rigidity at high temperature and has the outstanding characteristics of good creep resistance, oxidation resistance and the like. The high-temperature structural material has the most potential in the high-temperature technical fields of aviation, aerospace and the like.
Most of titanium-aluminum-based composite materials are prepared by a traditional casting method, titanium powder and aluminum powder are directly subjected to alloying treatment after being melted, the obtained cast structure is generally in a thick dendritic shape, shrinkage porosity and component segregation exist, so that brittleness is increased, room-temperature ductility is low, formability is poor, performance is affected in the using process, and service life is shortened. Therefore, a preparation method which can replace casting is needed to be found, and the titanium-aluminum-based composite material with better performance can be obtained at lower cost.
The powder metallurgy method can effectively reduce material macrosegregation, refine crystal grains, avoid difficult ingot cogging and directly carry out conventional forging or rolling forming, and is a hot spot of domestic and foreign research at present. For example, patent No. CN201210131206.9 discloses a method for preparing a powder metallurgy ultra-fine grain titanium-aluminum-based alloy plate, which comprises preparing a pre-alloy by a rotary electrode atomization method, and forming and sintering the pre-alloy to obtain the titanium-aluminum-based alloy plate. The preparation of the pre-alloyed powder has high requirements on equipment, low yield and high production cost. The particle size of the pre-alloyed powder is generally thicker (30-200 m), the shape is spherical or spheroidal, the specific surface area is small, and the sintering performance is poor, so that the high-density alloy material can be prepared only by adopting a reinforced sintering process, and the sintering methods also have high requirements on equipment and high cost, and limit the application range of the sintering methods.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide a powder metallurgy titanium-aluminum-based composite material and a preparation method thereof, and solves the problems of high cost, complex process, high equipment requirement, poor performance and the like of the conventional preparation method.
In order to solve the technical problems, the invention adopts the following technical scheme: a powder metallurgy titanium-aluminum matrix composite comprises the following element powder components in percentage by weight: 30.0-40.0% of Ti powder and TiO22.0-8.0% of powder and Nb2O51.0-5.0% of powder and the balance of Al powder. The proportion is selected to directly enable the element powder to be alloyed through high-energy ball milling to form a gamma-TiAl matrix, and the dispersion component with the mass fraction of about 10-15% is synthesized in situSecond phase Al of cloth2O3The particles do not need to be added with second phase particles from the outside, so that the interface between the composite materials is not polluted, and the bonding strength of the interface of the composite materials is improved. Second phase Al produced2O3The particles can refine TiAl structure particles, and Nb is added2O5The addition of the particles adds some room temperature ductility to the composite.
The preparation method of the powder metallurgy titanium-aluminum-based composite material comprises the following steps:
1) proportioning the components of the element powder, putting the mixture into a vacuum ball mill, adding steel balls and a ball milling medium, and performing high-energy ball milling to enable the element powder to be alloyed;
2) and drying the ball-milling alloyed powder, and sintering by discharging plasma to obtain the powder metallurgy titanium-aluminum-based composite material.
The method adopts Spark Plasma Sintering (SPS), the sintering method utilizes the action of strong pulse current to promote the solidification of the material, has the characteristics of high temperature rise speed, low sintering temperature and the like, can effectively reduce the sintering temperature of the TiAl alloy, has short heat preservation time of a sample at a high temperature stage, and can effectively reduce the reduction of material density caused by the Kerkadall effect. In addition, the content of Nb element is small (not more than 5%), and the segregation of Nb element does not influence the structure performance.
Preferably, the mass ratio of the steel balls to the total amount of the element powder is 3-5: 1.
Preferably, the ball milling medium is absolute ethyl alcohol, and the rotating speed of the ball mill is 250-500 r/min. The absolute ethyl alcohol is used as a ball milling medium, so that materials can be prevented from being bonded on the steel balls in the ball milling process, the ball milling efficiency is improved, and the absolute ethyl alcohol is volatile, so that the slurry after ball milling can be dried at low temperature without being oxidized.
Preferably, the mass ratio of the ball milling medium to the total amount of the element powder is 3-5: 1, and the ball milling time is 2-6 h. Preferably, the mass ratio of the ball milling medium to the total amount of the element powder is 3:1, and the ball milling time is 6 hours.
The ball-to-material ratio is the ratio of the mass of the grinding balls (ball-milling media) to the mass of the materials (total amount of element powder), if the ball-to-material ratio is too small, the ball-milling strength cannot be achieved, and the impact grinding effect in the ball-milling process cannot meet the requirement; if the ball-to-material ratio is too large, impact and friction among grinding balls and between the grinding balls and a ball-milling tank are increased, useless power loss is caused, power consumption is increased during ball milling, yield is reduced, abrasion of the ball-milling tank is aggravated, metal consumption is increased, consumed metal is also introduced into materials as impurities, and the ball-to-material ratio of 3:1 meets the requirement in the same ball-milling time.
The ball milling time can influence the alloying degree and the grain refinement degree, in the ball milling process, new surfaces of the powder are continuously exposed due to friction and impact, and the powder is seriously deformed to form the defects of high-density dislocation and the like, so that the free energy of elements is improved, and finally the nano crystallization and the alloying are realized. The ball milling time is too long or too short to achieve the expected effect.
Preferably, the drying temperature is 40-60 ℃, and the drying time is 25-40 h.
Preferably, the spark plasma sintering is carried out under the condition that the pressure is 40MPa, the temperature is raised to 1000-1250 ℃ at the temperature rise rate of 80-100 ℃/min, the temperature is preserved for 10-30 min, and then the temperature is lowered to the room temperature at 300 ℃/min.
The sintering pressure and the density of the sintered body structure have great influence, and the particles are deformed or broken due to overhigh sintering pressure, and the requirement on equipment is higher; and the density of a pressed compact is insufficient due to too low sintering pressure, the densification of a sintered body is difficult to complete, pores exist among particles, and a sintered block is difficult to form. Therefore, the invention selects a sintering pressure 40MPa which can be met by the equipment and can complete the densification of the sintered body. The too high sintering temperature or the too long heat preservation time can cause the coarse grains and reduce the mechanical property of the composite material; the internal stress caused by the sintering process cannot be fully released due to the excessively low sintering temperature or the excessively short heat preservation time; under the sintering condition of the invention, the composite material sintered block with fine crystal grains and excellent performance can be obtained. The cooling rate is 300 ℃/min in the SPS sintering process, the growth of crystal grains can be well controlled by rapid cooling, and the mechanical property of the composite material is improved.
Compared with the prior art, the invention has the following beneficial effects:
1. the invention takes the element powder as the raw material, can realize the alloying among the alloy elements by high-energy ball milling, and prepare the titanium-aluminum-based composite material.
2. In the titanium-aluminum-based composite material prepared by the invention, the second phase Al which is dispersedly distributed is synthesized in situ2O3The particles are distributed on the TiAl crystal boundary of the matrix in a net-shaped mode, and Al2O3Al used as reinforcing phase energy for refining titanium-aluminum alloy structure and synthesized in situ2O3The titanium-aluminum-based composite material prepared by the method has higher bending strength, compression strength, hardness and interface strength compared with the common titanium-aluminum-based composite material, so that the stability and wear resistance of the titanium-aluminum-based composite material are improved, the titanium-aluminum-based composite material with better performance can be obtained at low cost, and the titanium-aluminum-based composite material can be widely applied to the field of high-temperature structural materials.
Drawings
FIG. 1 is a microstructure diagram of a titanium-aluminum-based composite material prepared in example 1.
Detailed Description
The present invention will be described in further detail with reference to examples.
Preparation method of powder metallurgy titanium-aluminum-based composite material
Example 1
Respectively mixing 24.0g of Ti powder, 30.0g of Al powder and 4.8g of TiO powder with the granularity of 300 meshes2Powder, 3.0g Nb2O5Putting the powder into a vacuum ball mill, adding 180g of steel balls and 60g of absolute ethyl alcohol for high-energy ball milling at the rotating speed of 250r/min, and alloying the powder after 2 hours of ball milling; and then, carrying out vacuum drying on the alloyed powder at 50 ℃ for 30h, putting the dried mixed powder into SPS equipment for sintering under the condition that the pressure is 40MPa, heating to 1000 ℃ at the heating rate of 100 ℃/min, carrying out heat preservation for 10min, and then cooling to room temperature at the temperature of 300 ℃/min to finally obtain the titanium-aluminum matrix composite. And preparing the composite material into a sample to obtain a prefabricated sample.
The titanium-aluminum-based composite material obtained in this example was observed under a scanning electron microscope, and the results are shown in fig. 1.
As can be seen from the figure, the sintered structure mainly comprises a gray γ -TiAl phase as a matrix, and the black phase distributed along the grain boundary is Al2O3The particle and grey fraction are alpha2-Ti3An Al phase with a small amount of high brightness Al distributed in the crystal boundary3And (3) Nb particles. In-situ synthesized reinforced phase Al2O3The titanium-aluminum-based composite material is distributed on a TiAl crystal boundary of a matrix in a net-shaped mode, and has better interface strength, stability and high-temperature performance compared with the common titanium-aluminum-based composite material.
Example 2
Respectively mixing 18.0g of Ti powder, 40.0g of Al powder and 1.2g of TiO powder with the granularity of 300 meshes2Powder, 0.6g Nb2O5Putting the powder into a vacuum ball mill, adding 300g of steel balls and 60g of absolute ethyl alcohol for high-energy ball milling, and alloying the powder after ball milling for 2 hours; and then carrying out vacuum drying on the alloyed powder for 25h at 60 ℃, putting the dried mixed powder into SPS equipment for sintering under the condition that the pressure is 40MPa, heating to 1000 ℃ at the heating rate of 100 ℃/min, carrying out heat preservation for 10min, and then cooling to room temperature at 300 ℃/min to finally obtain the titanium-aluminum matrix composite. And preparing the composite material into a sample to obtain a prefabricated sample.
Example 3
23.0g of Ti powder, 33.0g of Al powder and 3.5g of TiO powder with the granularity of 300 meshes are respectively mixed2Powder, 0.8g Nb2O5The powder was charged into a vacuum ball mill, and 420g of a steel ball and 60g of anhydrous ethanol were added theretoHigh-energy ball milling is carried out, the rotating speed is 250r/min, and the powder is alloyed after ball milling for 2 hours; and then, carrying out vacuum drying on the alloyed powder at 50 ℃ for 30h, putting the dried mixed powder into SPS equipment for sintering under the condition that the pressure is 40MPa, heating to 1000 ℃ at the heating rate of 100 ℃/min, carrying out heat preservation for 10min, and then cooling to room temperature at the temperature of 300 ℃/min to finally obtain the titanium-aluminum matrix composite. And preparing the composite material into a sample to obtain a prefabricated sample.
Example 4
20.0g of Ti powder, 37.0g of Al powder and 2.0g of TiO powder with the granularity of 300 meshes are respectively mixed2Powder, 1.0g Nb2O5The powder is put into a vacuum ball mill, then 180g of steel balls and 60g of absolute ethyl alcohol are added for high-energy ball milling, the rotating speed is 250r/min, and the powder is alloyed after 2 hours of ball milling; and then, carrying out vacuum drying on the alloyed powder for 40h at 40 ℃, putting the dried mixed powder into SPS equipment for sintering under the condition that the pressure is 40MPa, heating to 1250 ℃ at the heating rate of 80 ℃/min, preserving the heat for 10min, and cooling to room temperature at 300 ℃/min to finally obtain the titanium-aluminum matrix composite. And preparing the composite material into a sample to obtain a prefabricated sample.
Example 5
20.0g of Ti powder, 36.0g of Al powder and 1.8g of TiO powder with the granularity of 300 meshes are respectively mixed2Powder, 0.8g Nb2O5Putting the powder into a vacuum ball mill, adding 180g of steel balls and 60g of absolute ethyl alcohol for high-energy ball milling at the rotating speed of 250r/min, and alloying the powder after ball milling for 6 hours; and then, carrying out vacuum drying on the alloyed powder at 50 ℃ for 30h, putting the dried mixed powder into SPS equipment for sintering under the condition that the pressure is 40MPa, heating to 1000 ℃ at the heating rate of 100 ℃/min, carrying out heat preservation for 10min, and then cooling to room temperature at the temperature of 300 ℃/min to finally obtain the titanium-aluminum matrix composite. And preparing the composite material into a sample to obtain a prefabricated sample.
Secondly, product detection
1. The results of texture characterization of the titanium-aluminum powder prepared in examples 1 to 5 are shown in table 1.
TABLE 1
| Preparing sample | Average size of particles (. mu.m) | Uniformity of distribution |
| Example 1 | 21.8 | 0.58 |
| Example 2 | 20.5 | 0.52 |
| Example 3 | 19.1 | 0.50 |
| Example 4 | 22 | 0.60 |
| Example 5 | 20.8 | 0.72 |
As can be seen from Table 1, the titanium-aluminum-based powder prepared by the invention has fine and uniform particles, and the particle size of part of the powder can reach the nanometer level; in the range of the embodiment, the larger the ball-to-material ratio is, the smaller the distribution uniformity of the obtained titanium-aluminum-based composite material is, and the larger the particle size variation range is; the longer the ball milling time, the higher the distribution uniformity of the mechanical alloying powder.
2. The mechanical properties of the prepared samples prepared from the titanium-aluminum-based composite materials of examples 1 to 5 were measured, and the results are shown in table 2.
TABLE 2
| Preparing sample | Compression Performance at room temperature/MPa | Hardness HV/MPa |
| Example 1 | 1459 | 490.4 |
| Example 2 | 1463 | 475.1 |
| Example 3 | 1456 | 487.9 |
| Example 4 | 1433 | 480.6 |
| Example 5 | 1449 | 489.7 |
As can be seen from Table 2, the preforms prepared at the appropriate ball milling parameters had higher room temperature compressibility and hardness values, and thusThe hardness and wear resistance of the titanium-aluminium alloy are improved, mainly due to the Al grown in situ2O3The titanium-aluminum alloy can be used as a reinforcing phase to refine the structure of the titanium-aluminum alloy and improve the mechanical property of the titanium-aluminum alloy.
The above description is only exemplary of the present invention and should not be taken as limiting, and any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (6)
1. The preparation method of the powder metallurgy titanium-aluminum-based composite material is characterized in that the composite material comprises the following element powder components in percentage by weight: 30.0-40.0% of Ti powder and TiO22.0-8.0% of powder and Nb2O51.0-5.0% of powder and the balance of Al powder;
the preparation method comprises the following steps:
1) proportioning the components of the element powder, putting the mixture into a vacuum ball mill, adding steel balls and a ball milling medium, and performing high-energy ball milling, wherein the rotating speed of the ball mill is 250r/min, and the ball milling time is 2-6 h, so that the element powder is alloyed;
2) drying the ball-milled alloyed powder, and sintering the powder by discharge plasma to obtain the powder metallurgy titanium-aluminum-based composite material; wherein the discharge plasma sintering is carried out by heating to 1000-1250 ℃ at a heating rate of 80-100 ℃/min under the condition that the pressure is 40MPa, preserving the temperature for 10-30 min, and then cooling to room temperature at 300 ℃/min.
2. The method for preparing a powder metallurgy titanium-aluminum-based composite material according to claim 1, comprising the following elemental powder components in percentage by weight: 35.0-38.0% of Ti powder and TiO22.0-6.0% of powder and Nb2O51.0-5.0% of powder and the balance of Al powder.
3. The method for preparing the powder metallurgy titanium-aluminum based composite material according to claim 1 or 2, wherein the particle size of the element powder is 100-300 meshes.
4. The preparation method of the powder metallurgy titanium-aluminum-based composite material according to claim 1, wherein the mass ratio of the steel ball to the total amount of the element powder is 3-7: 1.
5. The method for preparing a powder metallurgy titanium-aluminum-based composite material according to claim 1, wherein the ball milling medium is absolute ethyl alcohol.
6. The preparation method of the powder metallurgy titanium-aluminum-based composite material according to claim 1, wherein the drying temperature is 40-60 ℃, and the drying time is 25-40 h.
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