CN110643851A - TiAl-based composite material and thermal mechanical treatment method thereof - Google Patents
TiAl-based composite material and thermal mechanical treatment method thereof Download PDFInfo
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- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 99
- 239000002131 composite material Substances 0.000 title claims abstract description 93
- 238000000034 method Methods 0.000 title claims abstract description 26
- 238000010438 heat treatment Methods 0.000 claims abstract description 36
- 238000005242 forging Methods 0.000 claims abstract description 17
- 230000000930 thermomechanical effect Effects 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims description 29
- 238000003723 Smelting Methods 0.000 claims description 23
- 238000001125 extrusion Methods 0.000 claims description 23
- 239000000243 solution Substances 0.000 claims description 19
- 239000000463 material Substances 0.000 claims description 17
- 239000012535 impurity Substances 0.000 claims description 8
- 238000002156 mixing Methods 0.000 claims description 8
- 239000002994 raw material Substances 0.000 claims description 8
- 238000002844 melting Methods 0.000 claims description 6
- 230000032683 aging Effects 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 238000000137 annealing Methods 0.000 claims description 5
- 239000011810 insulating material Substances 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 238000003825 pressing Methods 0.000 claims description 5
- 239000010935 stainless steel Substances 0.000 claims description 5
- 229910001220 stainless steel Inorganic materials 0.000 claims description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 4
- 230000003014 reinforcing effect Effects 0.000 claims description 4
- 239000006104 solid solution Substances 0.000 claims description 4
- 230000007704 transition Effects 0.000 claims description 4
- 238000010275 isothermal forging Methods 0.000 claims description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 239000001257 hydrogen Substances 0.000 claims description 2
- 229910052739 hydrogen Inorganic materials 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 239000001301 oxygen Substances 0.000 claims description 2
- 229910052760 oxygen Inorganic materials 0.000 claims description 2
- 238000010791 quenching Methods 0.000 claims description 2
- 230000000171 quenching effect Effects 0.000 claims description 2
- 229910052715 tantalum Inorganic materials 0.000 claims description 2
- 229910033181 TiB2 Inorganic materials 0.000 abstract description 46
- 229910045601 alloy Inorganic materials 0.000 abstract description 27
- 239000000956 alloy Substances 0.000 abstract description 27
- 239000013078 crystal Substances 0.000 abstract description 13
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 abstract description 11
- 238000006243 chemical reaction Methods 0.000 abstract description 10
- 238000011065 in-situ storage Methods 0.000 abstract description 10
- 230000005496 eutectics Effects 0.000 abstract description 5
- 238000001192 hot extrusion Methods 0.000 abstract description 3
- 230000008569 process Effects 0.000 abstract description 3
- 238000005272 metallurgy Methods 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 11
- 239000010936 titanium Substances 0.000 description 10
- 230000002787 reinforcement Effects 0.000 description 7
- 239000000835 fiber Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000002360 preparation method Methods 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000004663 powder metallurgy Methods 0.000 description 3
- 239000000758 substrate Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910006281 γ-TiAl Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
- 238000010168 coupling process Methods 0.000 description 1
- 238000005859 coupling reaction Methods 0.000 description 1
- 238000010406 interfacial reaction Methods 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 229910001845 yogo sapphire 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
- C22C14/00—Alloys based on titanium
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Crystallography & Structural Chemistry (AREA)
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Abstract
The invention relates to a TiAl-based composite material reinforced by TiB2 whiskers generated by in-situ self-generation and a thermo-mechanical treatment method thereof. According to a calculation formula of the addition control amount of the B element, a proper amount of the B element is added into the TiAl alloy, so that long and thin secondary TiB2 whiskers are formed in the TiAl alloy through in-situ self-generation of L → beta + TiB2 and L + beta → alpha + TiB2 eutectic reaction, and meanwhile, the generation of coarse and large granular primary TiB2 phases is avoided, so that the TiAl-based composite material reinforced by the TiB2 whiskers can be prepared through an ingot metallurgy method. Then, the TiB2/TiAl composite material can be prepared into a fine-grain bar or a fine-grain cake blank through sheath hot extrusion or sheath forging, the slender TiB2 crystal whiskers are crushed into short crystal whiskers, and the short crystal whiskers are treated through a special heat treatment process to obtain a fine-grain basket-shaped structure or a fine-grain full-lamellar structure. The TiB2/TiAl composite material has high strength from room temperature to 850 ℃ and excellent room temperature plasticity, so the TiB2/TiAl composite material has good application prospect in the field of aerospace.
Description
Technical Field
The invention belongs to the field of composite material preparation, relates to a TiAl-based composite material and a thermal mechanical treatment method thereof, and particularly relates to an in-situ self-generated TiB2 whisker reinforced TiAl-based composite material and a thermal processing and thermal treatment method thereof.
Background
The gamma-TiAl based intermetallic compound alloy has excellent performances of low density, high specific strength, high specific modulus, high creep resistance, oxidation resistance, combustion resistance and the like, so the gamma-TiAl based intermetallic compound alloy is a new generation of high-temperature structural material which attracts much attention, and the gamma-TiAl based intermetallic compound alloy is a key material of a new generation of high thrust-weight ratio aircraft engine at present.
The TiAl-based composite material is prepared by adding granular and fibrous reinforcements into the TiAl alloy, and the high-temperature strength and the high-temperature durability of the TiAl alloy can be improved. However, the room temperature plasticity of the TiAl alloy is only 1-2%, and when the reinforcing body is added into the TiAl alloy, the room temperature plasticity is further reduced, so that the large-size TiAl-based composite material is difficult to prepare. The TiAl-based composite material has the advantages that the reinforcement and the matrix of the TiAl-based composite material often have strong interface reaction in the preparation process, so that the performance of the composite material is obviously reduced. For example, a powder metallurgy method is used to prepare a SiC fiber reinforced TiAl-based composite material, because the difference in linear expansion coefficient between SiC fiber and TiAl alloy is too large, thermal stress generated during cooling causes cracks to be generated in the radial direction of the SiC fiber. Preparation of Al by powder metallurgy2O3Fiber-reinforced TiAl composites, discovery of Al2O3The interface reaction of the fiber and the TiAl matrix is extremely violent. The hot-working performance of the powder metallurgy TiAl composite material is very poor, and strong stress strain concentration is generated near a reinforcing body in the hot deformation process, so that cracks are formed.
Disclosure of Invention
The purpose of the invention is: provides a TiAl-based composite material and a thermo-mechanical treatment method thereof, aiming at solving the technical problems that the existing TiAl-based composite material substrate and a reinforcement body generate interface reaction or stress concentration near the interface generates larger brittleness, and the high-strength plastic TiAl-based composite material is difficult to prepare.
In order to solve the technical problem, the technical scheme of the invention is as follows:
on one hand, the invention provides a TiAl-based composite material, which comprises the following components in percentage by atom: 0.5 to 1.5 percent of B, 42 to 45.5 percent of Al, 1 to 2 percent of Cr, 3 to 6 percent of Nb, 0.1 to 0.5 percent of Ta, 0 to 0.2 percent of Si, 0 to 2 percent of C, and the balance of Ti and inevitable impurities, wherein the oxygen content is less than or equal to 0.2 percent by weight, the nitrogen content is less than or equal to 0.03 percent by weight, and the hydrogen content is less than or equal to 0.02 percent by weight;
the elastic modulus E of the TiAl-based composite material is more than or equal to 150 GPa;
the TiAl-based composite material has the reinforcing body of TiAl-based composite material which is TiB distributed in a dispersed way2Short whiskers; the length of the whisker is less than or equal to 30 mu m.
Preferably, the invention provides a TiAl-based composite material, which contains, by atomic percentage: 45.5% of Al, 0.5% of B, 1.5% of Cr, 4% of Nb, 0.2% of Ta, 0.2% of Si, and the balance of Ti and inevitable impurities.
Preferably, the invention provides another TiAl-based composite material, which contains, in atomic percent: 44% of Al, 0.8% of B, 1% of Cr, 4% of Nb, 0.2% of Ta, and the balance of Ti and inevitable impurities.
Preferably, the present invention provides a third TiAl-based composite material, wherein the TiAl-based composite material contains, in atomic percent: 42% of Al, 0.5% of B, 1.5% of Cr, 5% of Nb, 0.2% of Ta, and the balance of Ti and inevitable impurities.
On the other hand, the invention provides a preparation method of the TiAl composite material, which comprises the following steps:
the method comprises the following steps: smelting of cast ingots: uniformly mixing the raw materials according to the component ratio, and pressing the mixture into an electrode block on a press machine; carrying out three times of vacuum consumable melting; obtaining a composite material ingot with the diameter of phi 180 mm-phi 300 mm;
step two: extrusion deformation: performing sheath extrusion deformation on the obtained composite material cast ingot, adding a heat insulating material between the sheath and the composite material cast ingot, and performing air cooling or furnace cooling on the composite material bar to room temperature after the extrusion deformation;
step three: homogenizing and annealing: heating the material obtained in the last step to 1050-1200 ℃, preserving heat for 6-48 hours, and then cooling to room temperature or directly heating to a solid solution temperature;
step four: solution heat treatment: carrying out solution heat treatment on the homogenized and annealed material in a two-phase region or a single-phase region;
step five: aging heat treatment: and heating the material subjected to the solution heat treatment to 850-950 ℃, preserving the heat for 2-8 hours, and then cooling the material to room temperature.
Parameters in the first step: the smelting vacuum degree is lower than 5Pa, the smelting current is 3 kA-6 kA, and the smelting voltage is 23-27V.
The parameters of the second step are as follows: the sheath material is made of stainless steel, the extrusion deformation temperature range is 1100-1250 ℃, and the extrusion ratio is more than 6: 1.
The two-phase region solution heat treatment is a gamma + alpha two-phase region solution heat treatment, and specifically comprises the following steps:
the heat treatment temperature is 1200-Tα-15 ℃ of which TαIs gamma → alpha phase transition temperature; and preserving the heat for 0.5-6 hours, and then air-cooling or furnace-cooling to room temperature.
The single-phase zone solution heat treatment is alpha single-phase zone solution heat treatment, and specifically comprises the following steps:
heat treatment temperature Tα+5℃～Tα+20 ℃ where T isαIs gamma → alpha phase transition temperature; keeping the temperature for 5 min-2 hours, and then air cooling, furnace cooling or oil quenching to room temperature
Before the third step, isothermal forging is also included, specifically:
heating the composite material bar to 1050-1250 ℃, heating the forging die to 900-1150 ℃, and forging the deformation rate of 0.001s-1～0.05s-1And the forging deformation is more than or equal to 40 percent, and the forging is cooled in air or furnace to room temperature after the forging deformation.
The invention has the beneficial effects that:
(1) TiAl-based composite material (TiB)2TiAl) reinforcement TiB2The whiskers are generated in situ directly from the liquid phase by eutectic reaction, TiB2Between the whisker reinforcement body and the TiAl alloy matrixThere is an interfacial reaction problem.
(2) In situ self-generated TiB2The crystal whisker can obviously refine the casting structure and is beneficial to improving the TiB2Thermal processing property of the TiAl composite material.
(3)TiB2Elongated TiB after thermal mechanical treatment of/TiAl composite material2The crystal whiskers are broken into short crystal whiskers, and TiB is dispersedly distributed2The short whiskers can inhibit the growth of crystal grains, improve plasticity and improve strength.
In the past, researchers have generally added B as a trace element to TiAl alloys in amounts less than 0.2 at% because of concerns about large amounts of TiB2The particles may cause a decrease in room temperature plasticity. Since the addition amount of B in these TiAl alloys is low, there is not a sufficient amount of TiB2And the strengthening effect is not obvious, so that the strength of the TiAl alloy cannot be effectively improved. The research shows that the content of B is more than 0.5at percent, the grain size of TiAl alloy cast ingots can be reduced by one order of magnitude, and the upper limit of the content of B is well controlled, so that TiB can be ensured2Grow into whisker shape through eutectic reaction without growing into coarse granular TiB2The elongated whisker-shaped TiB2The phase is broken into short crystal whiskers through subsequent hot processing, and TiB can be obviously improved2The TiAl composite material has high temperature strength and excellent room temperature plasticity, so that it has excellent engineering application foreground.
Drawings
In order to more clearly illustrate the technical solution of the present invention, the drawings used in the embodiment of the present invention will be briefly explained. It is obvious that the drawings described below are only some embodiments of the invention, and that for a person skilled in the art, other drawings can be obtained from these drawings without inventive effort.
FIG. 1 is TiB2TiB in TiAl composite material2Crystal whisker TEM morphology;
FIG. 2 is a graph showing the effect of B content on TiAl alloy grain size;
FIG. 3 shows TiB in the composite material after hot extrusion and deformation in example 12Short whiskers.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention. It is to be understood that the embodiments described are only a few embodiments of the present invention, 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 invention.
Features of various aspects of embodiments of the invention will be described in detail below. In the following detailed description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. It will be apparent, however, to one skilled in the art that the present invention may be practiced without these specific details. The following description of the embodiments is merely intended to better understand the present invention by illustrating examples thereof. The present invention is not limited to any particular arrangement or method provided below, but rather covers all product structures, any modifications, alterations, etc. of the method covered without departing from the spirit of the invention.
In the drawings and the following description, well-known structures and techniques are not shown to avoid unnecessarily obscuring the present invention.
Example 1:
the method adds a proper amount of B element into the TiAl alloy, and generates elongated TiB in situ on the TiAl alloy substrate by ingot melting2Whisker and preparing TiB through subsequent thermal mechanical treatment2A TiAl composite material. TiB in composite materials2Phase L → beta + TiB in the process of liquid metal solidification2And L + beta → alpha + TiB2Elongated secondary TiB grown by eutectic reaction and in-situ coupling of matrix2The whiskers (see figure 1) had a width of about 0.5 μm and a length of several tens of microns.
TiB of the invention2the/TiAl composite material can be produced in the following way:
TiB of example 12The TiAl composite material is prepared by the following steps:
TiB2the raw materials of the/TiAl composite material adopt zero-order sponge titanium, A00-grade high-purity aluminum, metal Cr, Al-Nb intermediate alloy, Al-Ta intermediate alloy, Al-Si intermediate alloy and Al-Ti-B intermediate alloy. Comprises the following components in percentage by atom: 45.5% of Al, 0.5% of B, 1.5% of Cr, 4% of Nb, 0.2% of Ta, 0.2% of Si and the balance of Ti.
After the raw materials are uniformly mixed, pressing the mixture into an electrode block on a press machine. After welding the electrode block, carrying out three times of smelting in a vacuum consumable melting furnace, wherein the smelting vacuum degree is lower than 5Pa, the smelting current is controlled within the range of 3 kA-6 kA according to the size of the ingot, the smelting voltage is 23-25V, and an ingot with the diameter of phi 220mm is obtained after three times of smelting.
Mixing TiB2Performing sheath extrusion deformation on/TiAl composite material cast ingot, wherein the sheath material is made of stainless steel, and the sheath and TiB2Adding heat insulating material between TiAl composite material ingots, extruding at 1200-1250 deg.c in the extrusion ratio of 10 to 1, and air cooling the bar material to room temperature after extrusion deformation. After hot extrusion deformation, TiB2TiB in TiAl composite material2The phases were broken into fine and dispersed whiskers with an average length of 15 μm and aligned in the direction of extrusion deformation, as shown in FIG. 3.
Blanking an extrusion bar, performing isothermal die forging, heating the blank to 1150 ℃, heating a forging die to 1000 ℃, and controlling the forging deformation rate at 0.001s-1～0.01s-1Within the range, the forging deformation is 50%, and the forging is cooled to room temperature after the forging deformation.
Mixing TiB2Carrying out homogenizing annealing treatment of 1150 ℃/16 hour/air cooling on the/TiAl composite material extrusion bar or isothermal forging; then solution treatment of 1300 ℃/0.5 hour/air cooling is carried out; finally, carrying out aging heat treatment at 900 ℃/6 h furnace cooling.
Table 1 and Table 2 show the room temperature and 850 ℃ tensile properties of example 1, respectively. Thermomechanically treated TiB2The room temperature plasticity of the/TiAl composite material can reach more than 2 percent, the room temperature yield strength reaches more than 600MPa, and the yield strength at 850 ℃ is still kept more than 400MPa。
TABLE 1 tensile Properties at room temperature for example 1
TABLE 2 tensile Properties at 850 ℃ of example 1
Example 2:
TiB of example 22The TiAl composite material is prepared by the following steps:
TiB of example 22The raw material of the/TiAl composite material adopts zero-order sponge titanium, A00-grade high-purity aluminum, metal Cr, Al-Nb intermediate alloy and TiB2And (3) powder. Comprises the following components in percentage by atom: 44% of Al, 0.8% of B, 1% of Cr, 4% of Nb, 0.2% of Ta and the balance of Ti.
After the raw materials are uniformly mixed, pressing the mixture into an electrode block on a press machine. After welding the electrode block, carrying out three times of smelting in a vacuum consumable melting furnace, wherein the smelting vacuum degree is lower than 5Pa, the smelting current is controlled within the range of 3 kA-6 kA according to the size of the ingot, the smelting voltage is 23-25V, and an ingot with the diameter of phi 220mm is obtained after three times of smelting.
Mixing TiB2Performing sheath extrusion deformation on/TiAl composite material cast ingot, wherein the sheath material is made of stainless steel, and the sheath and TiB2Adding heat insulating material between TiAl composite material ingots, extruding at 1200-1250 deg.c in the extrusion ratio of 10 to 1, and air cooling the bar material to room temperature after extrusion deformation.
Mixing TiB2Carrying out homogenizing annealing treatment on the/TiAl composite material extrusion bar at 1150 ℃/16 h/air cooling; then solid solution treatment of 1280 ℃/0.5 hour/air cooling is carried out; finally, carrying out aging heat treatment at 900 ℃/6 h furnace cooling.
Table 3 and Table 4 show the room temperature and 850 ℃ tensile properties of example 2, respectively. Thermomechanically treated TiB2The room temperature plasticity of the/TiAl composite material can reach 2 percent, the room temperature yield strength reaches more than 550MPa, and the yield strength at 850 ℃ is still kept at 400MPaThe above.
TABLE 3 tensile Properties at room temperature for example 2
TABLE 4 tensile Properties at 850 ℃ of example 2
Example 3:
TiB of example 32The TiAl composite material is prepared by the following steps:
TiB of example 32The raw material of the/TiAl composite material adopts zero-order sponge titanium, A00-grade high-purity aluminum, metal Cr, Al-Nb intermediate alloy and TiB2And (3) powder. Comprises the following components in percentage by atom: 42% of Al, 0.5% of B, 1.5% of Cr, 5% of Nb, 0.2% of Ta and the balance of Ti.
After the raw materials are uniformly mixed, pressing the mixture into an electrode block on a press machine. After welding the electrode block, carrying out three times of smelting in a vacuum consumable melting furnace, wherein the smelting vacuum degree is lower than 5Pa, the smelting current is controlled within the range of 3 kA-6 kA according to the size of the ingot, the smelting voltage is 23-25V, and an ingot with the diameter of phi 300mm is obtained after three times of smelting.
Mixing TiB2Performing sheath extrusion deformation on/TiAl composite material cast ingot, wherein the sheath material is made of stainless steel, and the sheath and TiB2Adding heat insulating materials between/TiAl composite material ingots, extruding at 1150-1200 ℃ in a ratio of 10:1, and cooling the bar to room temperature after extrusion deformation.
Mixing TiB2Carrying out uniform annealing treatment at 1100 ℃/16 h/air cooling on the/TiAl composite material extrusion bar; then solid solution treatment of 1210 ℃/0.5 hour/air cooling is carried out; finally, carrying out aging heat treatment at 900 ℃/6 h furnace cooling.
Table 5 and Table 6 show the room temperature and 850 ℃ tensile properties of example 2, respectively. Thermomechanically treated TiB2The room temperature plasticity of the/TiAl composite material can reach 2 percent, the room temperature yield strength reaches more than 800MPa, and the yield strength is still kept at 50 ℃ at 850 DEG CAbove 0 MPa.
TABLE 5 tensile Properties at room temperature for example 3
TABLE 6 tensile Properties at 850 ℃ of example 3
The method for preparing the in-situ self-generated TiAl-based composite material by adopting the ingot metallurgy method has the following advantages:
(1) TiAl-based composite material (TiB)2TiAl) reinforcement TiB2The whiskers are generated in situ directly from the liquid phase by eutectic reaction, TiB2The problem of interface reaction does not exist between the whisker reinforcement and the TiAl alloy matrix. As shown in FIG. 1, the TEM photograph shows TiB2The whisker and the TiAl alloy substrate have good interface bonding and no interface reaction.
(2) In situ self-generated TiB2The crystal whisker can obviously refine the casting structure and is beneficial to improving the TiB2Thermal processing property of the TiAl composite material. As shown in FIG. 2, when the B content reaches 0.5 at%, TiB2The grain size of the/TiAl composite material is reduced by an order of magnitude compared with the grain size of the TiAl alloy without adding B.
(3)TiB2Elongated TiB after thermal mechanical treatment of/TiAl composite material2The crystal whiskers are broken into short crystal whiskers, and TiB is dispersedly distributed2The short whiskers can inhibit the growth of crystal grains, improve plasticity and improve strength.
The composite material has excellent high-temperature strength and high-temperature durability, and simultaneously has good room-temperature plasticity. TiB2The TiAl composite material has a service temperature of 850 deg.C, and can be used for manufacturing parts such as blades, casings and diffusers of aero-engines and heat-resistant parts of hypersonic aircrafts
Finally, it should be noted that: the above embodiments are only for illustrating the technical solutions of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive various equivalent modifications or substitutions within the technical scope of the present invention, and these modifications or substitutions should be covered within the scope of the present invention.
Claims (10)
1. A TiAl-based composite material, characterized in that: the TiAl-based composite material comprises the following components in percentage by atom: 0.5 to 1.5 percent of B, 42 to 45.5 percent of Al, 1 to 2 percent of Cr, 3 to 6 percent of Nb, 0.1 to 0.5 percent of Ta, 0 to 0.2 percent of Si, 0 to 2 percent of C, and the balance of Ti and inevitable impurities, wherein the oxygen content is less than or equal to 0.2 percent by weight, the nitrogen content is less than or equal to 0.03 percent by weight, and the hydrogen content is less than or equal to 0.02 percent by weight;
the elastic modulus E of the TiAl-based composite material is more than or equal to 150 GPa;
the TiAl-based composite material has the reinforcing body of TiAl-based composite material which is TiB distributed in a dispersed way2Short whiskers, wherein the length of the whiskers is less than or equal to 30 microns.
2. The TiAl-based composite material according to claim 1, characterized in that: the TiAl-based composite material comprises the following components in percentage by atom: 45.5% of Al, 0.5% of B, 1.5% of Cr, 4% of Nb, 0.2% of Ta, 0.2% of Si, and the balance of Ti and inevitable impurities.
3. The TiAl-based composite material according to claim 1, characterized in that: the TiAl-based composite material comprises the following components in percentage by atom: 44% of Al, 0.8% of B, 1% of Cr, 4% of Nb, 0.2% of Ta, and the balance of Ti and inevitable impurities.
4. The TiAl-based composite material according to claim 1, characterized in that: the TiAl-based composite material comprises the following components in percentage by atom: 42% of Al, 0.5% of B, 1.5% of Cr, 5% of Nb, 0.2% of Ta, and the balance of Ti and inevitable impurities.
5. A thermal mechanical treatment method of a TiAl-based composite material is characterized in that: the method of thermomechanical treatment using the TiAl-based composite material according to claim 1, comprising the steps of:
the method comprises the following steps: smelting of cast ingots: uniformly mixing the raw materials according to the component ratio, and pressing the mixture into an electrode block on a press machine; carrying out three times of vacuum consumable melting; obtaining a composite material ingot with the diameter of phi 180 mm-phi 300 mm;
step two: extrusion deformation: performing sheath extrusion deformation on the obtained composite material cast ingot, adding a heat insulating material between the sheath and the composite material cast ingot, and performing air cooling or furnace cooling on the composite material bar to room temperature after the extrusion deformation;
step three: homogenizing and annealing: heating the material obtained in the last step to 1050-1200 ℃, preserving heat for 6-48 hours, and then cooling to room temperature or directly heating to a solid solution temperature;
step four: solution heat treatment: carrying out solution heat treatment on the homogenized and annealed material in a two-phase region or a single-phase region;
step five: aging heat treatment: and heating the material subjected to the solution heat treatment to 850-950 ℃, preserving the heat for 2-8 hours, and then cooling the material to room temperature.
6. The method for thermomechanical treatment of TiAl-based composite materials according to claim 5, characterized in that: parameters in the first step are set as follows:
the smelting vacuum degree is lower than 5Pa, the smelting current is 3 kA-6 kA, and the smelting voltage is 23-27V.
7. The method for thermomechanical treatment of TiAl-based composite materials according to claim 5, characterized in that: and in the second step, the jacket material is stainless steel, the extrusion deformation temperature range is 1100-1250 ℃, and the extrusion ratio is more than 6: 1.
8. The method for thermomechanical treatment of TiAl-based composite materials according to claim 5, characterized in that: the two-phase region solution heat treatment in the fourth step is a gamma + alpha two-phase region solution heat treatment, which comprises the following specific steps:
the heat treatment temperature is 1200-Tα-15 ℃ of which TαIs gamma → alpha phase transition temperature; keeping the temperature for 0.5 to 6 hours, andand then air cooling or furnace cooling is carried out to the room temperature.
9. The method for thermomechanical treatment of TiAl-based composite materials according to claim 5, characterized in that: in the fourth step, the single-phase zone solution heat treatment is alpha single-phase zone solution heat treatment, which comprises the following specific steps:
heat treatment temperature Tα+5℃～Tα+20 ℃ where T isαIs gamma → alpha phase transition temperature; preserving the temperature for 5min to 2 hours, and then air cooling, furnace cooling or oil quenching to room temperature.
10. The method for thermomechanical treatment of TiAl-based composite materials according to claim 5, characterized in that: before the third step, isothermal forging is also included, specifically:
heating the composite material bar to 1050-1250 ℃, heating the forging die to 900-1150 ℃, and forging the deformation rate of 0.001s-1～0.05s-1And the forging deformation is more than or equal to 40 percent, and the forging is cooled in air or furnace to room temperature after the forging deformation.
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