CN114150181A - Low-cost easy-deformation light high-strength TiAl alloy and preparation method thereof - Google Patents

Low-cost easy-deformation light high-strength TiAl alloy and preparation method thereof Download PDF

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CN114150181A
CN114150181A CN202111410812.XA CN202111410812A CN114150181A CN 114150181 A CN114150181 A CN 114150181A CN 202111410812 A CN202111410812 A CN 202111410812A CN 114150181 A CN114150181 A CN 114150181A
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deformation
alloy
temperature
tial alloy
gamma
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许昊
陈�光
祁志祥
郑功
陈旸
李沛
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Nanjing University of Science and Technology
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/002—Hybrid process, e.g. forging following casting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
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    • C22B9/20—Arc remelting
    • 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
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Abstract

The invention discloses a low-cost easy-deformation light high-strength TiAl alloy and a preparation method thereof, wherein the alloy component is Ti- (40-45) Al- (3-8) Mn, the cost of raw materials is lower than 70 yuan/kg, and the density is as low as 4g/cm3. The method comprises the following steps: vacuum induction melting for 1 time and vacuum consumable melting for 1 time to obtain alloy ingot, performing multi-pass high-temperature forging and pressing deformation on the cut sample to eliminate casting defects, wherein the deformation temperature is selected from (beta + alpha) two-phase region because beta phase has more independent phases<111>(110) The sliding system can improve the hot workability, simultaneously, the existence of the alpha phase can inhibit the growth of crystal grains, the total deformation is selected to be 70 percent, and the cooling mode is selected to be air cooling. The alloy material has room temperature tensile strength of 870MPa and elongationThe percentage is 1.5 percent, the tensile strength at 700 ℃ is 670MPa, the elongation is 11 percent, and the urgent requirements of future aerospace weaponry on light high-temperature structural materials with high specific strength and high specific stiffness are met.

Description

Low-cost easy-deformation light high-strength TiAl alloy and preparation method thereof
Technical Field
The invention particularly relates to a low-cost easy-deformation light high-strength TiAl alloy and a preparation method thereof, belonging to the field of light alloy material preparation.
Background
The lightweight of aerospace weaponry equipment is an urgent need of the national major strategy. The theoretical density of the TiAl intermetallic compound is only 3.9g/cm3The material is less than 1/2 of the nickel-based high-temperature alloy, is the only light heat-resistant metal structural material which can be used for a long time in an oxidation environment of more than 600 ℃ so far, realizes weight reduction by replacing the nickel-based high-temperature alloy with TiAl alloy, and has great significance.
In 2016, European airbus used a wrought TNM (Ti-43.5Al-4Nb-1Mo-0.1B) alloy in place of nickel-base superalloy to produce the last stage low pressure turbine blades of the PW1100G-JM engine of an A320neo aircraft. The engine combines aerodynamic and other technical improvements to realize 12-15% oil saving and 15-20 db noise reduction, and 2700-3600 tons of CO are reduced for each airplane every year2And 50-55% of NOx emission. Obviously, the TiAl alloy is an international development direction for replacing nickel-based high-temperature alloy to manufacture hot-end parts of aerospace weapons and equipment at the temperature of more than 600 ℃.
Compared with the foreign world, the TiAl alloy is still in the early stage of laboratory research and industrialization at home and is not practically applied. The difficulties mainly include: firstly, the TiAl alloy has intrinsic brittleness and low room-temperature tensile plasticity; secondly, the TiAl alloy has large deformation resistance and is difficult to be hot-formed; thirdly, TiAl alloy develops to a plurality of components, and the material cost continuously rises. Therefore, the development of the light high-strength TiAl alloy which is easy to deform at low cost is the premise for realizing the application.
Disclosure of Invention
The invention aims to provide a low-cost easy-deformation light high-strength TiAl alloy material.
The technical solution for realizing the purpose of the invention is as follows: a low-cost easy-deformation light high-strength TiAl alloy material comprises the alloy components of Ti- (40-45) Al- (3-8) Mn.
Preferably, the TiAl alloy material has the following structural characteristics: fine black gamma crystal grains are dispersed and distributed in equiaxed alpha2Gamma sheet and white betaoBetween phases, where the gamma size ≈ 5 μm, α2The/gamma dimension is approximately equal to 40 mu m.
Preferably, the TiAl alloy material has room temperature tensile strength of 870MPa, elongation of 1.5%, 700 ℃ tensile strength of 670MPa, and elongation of 11%.
The method for preparing the TiAl alloy material comprises the following steps:
the method comprises the following steps: mechanically polishing the surface of a metal raw material to remove oxide skin, and then batching about 25kg per ingot according to the alloy components;
step two: preparing an induction cast ingot by adopting a vacuum induction smelting furnace, sequentially adding Al, Mn and Ti into a smelting crucible, covering a furnace cover, vacuumizing to 0.1Pa, filling high-purity argon (99.99%) with the pressure of 0.04-0.06 MPa into the furnace, and smelting for 1 time to obtain a uniform induction cast ingot (phi 80 multiplied by 1200 mm);
step three: preparing an alloy ingot by adopting a vacuum consumable melting furnace, taking an induction ingot as an electrode, closing a furnace door, vacuumizing to 0.1Pa, filling high-purity argon (99.99%) with the pressure of 0.04-0.06 MPa into the furnace, and smelting for 1 time to obtain a uniform alloy ingot (phi 120 x 550 mm);
step four: cutting a sample (phi 50 multiplied by 110mm) from the middle part of the alloy ingot by using a wire cut electric discharge machine;
step five: and (3) carrying out high-temperature forging on the sample by adopting a hydraulic press to eliminate casting defects, and selecting characteristic deformation temperature, deformation pass, deformation and cooling mode to obtain target structure and performance.
Further, the purity of the alloy component in the step one is more than 99.9%.
Further, the vacuum induction melting power in the step two is 100 KW.
Further, the vacuum consumable melting power in the third step is 80 KW.
Furthermore, the deformation temperature in the fifth step is in a (beta + alpha) two-phase region, preferably 1300 ℃, the deformation passes are 3 times, the deformation amount of each pass is 23 percent, the total deformation amount is 70 percent, and the cooling mode is air cooling.
Compared with the prior art, the invention has the following remarkable advantages: (1) has a series of advantages of low cost, easy deformation, light weight, high strength and the like. (2) The material has high tensile strength and good plasticity at high temperature. (3) Isothermal/sheath deformation is not needed, the preparation cost is reduced, the processing procedures are reduced, the process is simple, and the operation is easy.
Drawings
FIG. 1 is a flow chart of the preparation of TiAl alloy material of the present invention.
FIG. 2 is a structural view of EPMA after forging deformation of the alloy of example 1.
FIG. 3 is a structural view of EPMA of the alloy of comparative example 1 after forging deformation.
FIG. 4 is a structural view of EPMA after forging deformation of the alloy of comparative example 2.
FIG. 5 is a structural view of EPMA after forging deformation of the alloy of comparative example 3.
Detailed Description
The innovation point of the invention is that the low-cost easy-deformation light high-strength TiAl alloy is prepared by utilizing Mn element micro-alloying. Mn can reduce stacking fault energy and promote twinning, and plays an important role in improving the plasticity of the alloy. Mn can also promote a large amount of body-centered cubic beta phases precipitated from the TiAl alloy at high temperature, the beta phases have more independent <111> (110) slip systems, the hot working performance of the alloy is improved, and the growth of crystal grains can be inhibited in the hot working and heat treatment processes of a (beta + alpha) two-phase region. The industrial prices of Mn are only 1/3 of Cr, 1/4 of Ni, 1/10 of Mo, 1/23 of Nb and 1/133 of V, so that the material cost can be greatly reduced.
The innovation point of the invention is that the deformation temperature selects a (beta + alpha) two-phase region. The traditional TiAl alloy generally selects a (beta + alpha + gamma) three-phase region, the temperature is about 1100-1200 ℃, although a multiphase competition mechanism can be used for avoiding the growth of grains, the content of a high-temperature beta phase is only 40-50%, the hot processing performance is reduced, the temperature is preferably 1300 ℃, and at the moment, the content of the high-temperature beta phase reaches 90%, so that the hot processing performance is improved, and the growth of grains is avoided by using a two-phase competition mechanism.
The innovation point of the invention is that the deformation passes are selected for 3 times, the deformation of each pass is 23 percent, and the total deformation is 70 percent. Practice proves that multi-pass forging can promote the recrystallization degree of the alloy, effectively refine grains and strengthen mechanical properties, the multi-pass forging is obviously superior to single-pass forging under the condition of consistent total deformation, but the more passes are not required to be performed at high temperature, the better is, and the invention proves that the optimal deformation pass is 3 times aiming at the TiAl alloy material.
The preparation process of the low-cost easily-deformable light-weight high-strength TiAl alloy material related to the following examples is shown in figure 1, and the deformation process is shown in Table 1.
TABLE 1
Figure BDA0003373737390000031
Example 1
The method comprises the following steps: the selected alloy component is Ti-43Al-4Mn (atomic percentage), and the purity of each metal component selected by the alloy ingot prepared by the invention is shown in Table 2. Firstly, mechanically polishing the surface of a metal raw material to remove oxide skin, and preparing the material according to a designed component proportion, wherein each ingot is about 25 kg;
TABLE 2
Figure BDA0003373737390000032
Step two: preparing an induction cast ingot by adopting a vacuum induction smelting furnace, sequentially adding Al, Mn and Ti into a smelting crucible, covering a furnace cover, vacuumizing to 0.1Pa, filling high-purity argon (99.99%) with the pressure of 0.04-0.06 MPa into the furnace, smelting for 1 time to obtain a uniform induction cast ingot (phi 80 multiplied by 1200mm), and adopting the power of 100KW during smelting;
step three: preparing an alloy ingot by using a vacuum consumable melting furnace, taking an induction ingot as an electrode of the vacuum consumable melting furnace, closing a furnace door, vacuumizing to 0.1Pa, filling high-purity argon (99.99%) with the pressure of 0.04-0.06 MPa into the furnace, and obtaining a uniform alloy ingot (phi 120 multiplied by 550mm) by 1-time melting, wherein the power adopted during the melting is 80 KW;
step four: cutting a sample (phi 50 multiplied by 110mm) from the middle part of the alloy ingot by using a wire cut electric discharge machine;
step five: and (3) forging and pressing the sample at high temperature by adopting a hydraulic press, wherein the deformation temperature is 1300 ℃, the deformation passes are 3 times, the deformation amount of each pass is 23 percent, the total deformation amount is 70 percent, and the cooling mode is selected to be air cooling, so that the deformation test bar for eliminating the casting defects is obtained.
The deformation structure of the prepared material is shown in figure 2, and fine black gamma grains are dispersed and distributed in isometric alpha2Gamma sheet and white betaoBetween phases, where the gamma size ≈ 5 μm, α2The/gamma dimension is approximately equal to 40 mu m.
The tensile property test result of the prepared material at room temperature and 700 ℃ shows that: the tensile strength of the material at room temperature reaches 871MPa, the plasticity reaches 1.58%, the tensile strength at 700 ℃ reaches 673MPa, and the plasticity reaches 11.4%.
Comparative example 1
The first step, the second step, the third step and the fourth step are the same as those in the embodiment 1.
Step five: and (3) forging and pressing the sample at high temperature by adopting a hydraulic press, wherein the deformation temperature is 1300 ℃, the deformation passes are 4 times, the deformation amount of each pass is 18 percent, the total deformation amount is 70 percent, and the cooling mode is selected to be air cooling, so that the deformation test bar for eliminating the casting defects is obtained.
The deformation structure of the prepared material is shown in figure 3, and fine black gamma grains are dispersed and distributed on equiaxed alpha2Gamma sheet and white betaoBetween phases, where the gamma size ≈ 3 μm, α2The/gamma dimension is approximately equal to 20 mu m.
The tensile property test result of the prepared material at room temperature and 700 ℃ shows that: the tensile strength of the material at room temperature reaches 869MPa, the plasticity reaches 0.97%, the tensile strength at 700 ℃ reaches 668MPa, and the plasticity reaches 9.9%. The plasticity is significantly lower than in example 1.
Comparative example 2
The first step, the second step, the third step and the fourth step are the same as those in the embodiment 1.
Step five: and (3) forging and pressing the sample at high temperature by adopting a hydraulic press, wherein the deformation temperature is 1300 ℃, the deformation passes are 2 times, the deformation amount of each pass is 35 percent, the total deformation amount is 70 percent, and the cooling mode is selected to be air cooling, so that the deformation test bar for eliminating the casting defects is obtained.
The deformation structure of the prepared material is shown in figure 4, and fine black gamma grains are dispersed and distributed on equiaxed alpha2Gamma sheet and white betaoBetween phases, where the gamma size ≈ 7 μm, α2The/gamma dimension is about 38 μm.
The tensile property test result of the prepared material at room temperature and 700 ℃ shows that: the tensile strength of the material at room temperature reaches 797MPa, the plasticity reaches 1.45 percent, the tensile strength at 700 ℃ reaches 595MPa, and the plasticity reaches 11.1 percent. The strength is significantly lower than in example 1.
Comparative example 3
The first step, the second step, the third step and the fourth step are the same as those in the embodiment 1.
Step five: and (3) forging and pressing the sample at high temperature by adopting a hydraulic press, increasing the deformation temperature from 1300 ℃ in a (beta + alpha) two-phase region to 1340 ℃ in a beta single-phase region, wherein the deformation passes are 3 times, the deformation amount of each pass is 23 percent, the total deformation amount is 70 percent, and the cooling mode is selected for air cooling to obtain the deformation test bar for eliminating the casting defects.
The deformation structure of the prepared material is shown in figure 5, and fine black gamma crystal grains are dispersed and distributed in a strip-shaped alpha2Gamma sheet and white betaoBetween the phases, where γ grows slightly, with a size ≈ 8 μm, α2The/gamma changes from equiaxed to elongated. The texture was significantly worse than in example 1.
The tensile property test result of the prepared material at room temperature and 700 ℃ shows that: the tensile strength of the material at room temperature reaches 683MPa, the plasticity reaches 0.48 percent, the tensile strength at 700 ℃ reaches 481MPa, and the plasticity reaches 7.3 percent. The performance is significantly lower than in example 1.
The performance against ratio after forging deformation of the alloys of example 1 and comparative examples 1 to 3 is shown in Table 3.
TABLE 3
Figure BDA0003373737390000051

Claims (8)

1. The low-cost easy-deformation light high-strength TiAl alloy is characterized in that the alloy component is Ti- (40-45) Al- (3-8) Mn.
2. The TiAl alloy of claim 1, wherein the TiAl alloy is characterized by a structure: fine black gamma crystal grains are dispersed and distributed in equiaxed alpha2Gamma sheet and white betaoBetween phases, where the gamma size ≈ 5 μm, α2The/gamma dimension is approximately equal to 40 mu m.
3. The TiAl alloy according to claim 1, wherein the TiAl alloy has a tensile strength of 870MPa at room temperature, an elongation of 1.5%, a tensile strength of 670MPa at 700 ℃ and an elongation of 11%.
4. A method for producing a TiAl alloy according to any one of claims 1 to 3, comprising, in order:
the method comprises the steps of material preparation, preparation of an induction ingot by a vacuum induction melting method, preparation of an alloy ingot by a vacuum consumable melting method and high-temperature forging, wherein the deformation temperature in the high-temperature forging process is in a (beta + alpha) two-phase region, the deformation passes are 3 times, the deformation amount of each pass is 23%, the total deformation amount is 70%, and the cooling mode is air cooling.
5. The method of claim 4, wherein the deformation temperature is 1300 ± 10 ℃.
6. The method of claim 4, wherein the alloy constituents are greater than 99.9% pure when dosed.
7. The method of claim 4, wherein the vacuum induction melting power is 100KW and the vacuum induction melting is performed for 1 pass.
8. The method defined in claim 4 wherein the vacuum consumable melting power is 80KW and the vacuum consumable melting is 1 pass.
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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2011036877A (en) * 2009-08-10 2011-02-24 Seimitsu Kogyo Kk METHOD FOR PRODUCING TiAl ALLOY INGOT, AND TiAl ALLOY INGOT PRODUCED BY THE METHOD
CN103820677A (en) * 2014-03-12 2014-05-28 北京工业大学 Novel Mn-contained beta-gamma TiAl intermetallic compound material with high Nb content and preparation method thereof
CN110643851A (en) * 2019-10-15 2020-01-03 中国航发北京航空材料研究院 TiAl-based composite material and thermal mechanical treatment method thereof
CN111254314A (en) * 2020-03-10 2020-06-09 上海航天精密机械研究所 TiAl alloy with low-temperature superplasticity and preparation method of component thereof
CN112063944A (en) * 2020-07-30 2020-12-11 西北工业大学 Heat treatment method for controlling beta solidification casting TiAl alloy fine grain structure

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2011036877A (en) * 2009-08-10 2011-02-24 Seimitsu Kogyo Kk METHOD FOR PRODUCING TiAl ALLOY INGOT, AND TiAl ALLOY INGOT PRODUCED BY THE METHOD
CN103820677A (en) * 2014-03-12 2014-05-28 北京工业大学 Novel Mn-contained beta-gamma TiAl intermetallic compound material with high Nb content and preparation method thereof
CN110643851A (en) * 2019-10-15 2020-01-03 中国航发北京航空材料研究院 TiAl-based composite material and thermal mechanical treatment method thereof
CN111254314A (en) * 2020-03-10 2020-06-09 上海航天精密机械研究所 TiAl alloy with low-temperature superplasticity and preparation method of component thereof
CN112063944A (en) * 2020-07-30 2020-12-11 西北工业大学 Heat treatment method for controlling beta solidification casting TiAl alloy fine grain structure

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
TOSHIMITSUTETSUI ET AL.: "A newly developed hot worked TiAl alloy for blades and structural components", 《SCRIPTA MATERIALIA》, vol. 47, no. 6, 25 July 2002 (2002-07-25), pages 2 - 4 *
张俊红: "TiAl基合金的组织超塑性研究", 《中国优秀博硕学位论文全文数据库（博士） 工程科技Ⅰ辑》, 15 December 2004 (2004-12-15), pages 3 *

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