CN116145064A - Method for improving creep property of titanium alloy - Google Patents
Method for improving creep property of titanium alloy Download PDFInfo
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- 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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- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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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
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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- Y02P10/25—Process efficiency
Abstract
The invention discloses a method for improving creep property of titanium alloy, which can control electron concentration of alloy to alpha 2 The phases are controlled. For high temperature titanium alloys hot worked in the alpha + beta two phase region, by T β Heat treatment at 20-60 deg.c below the phase transition temperature to obtain binary structure with primary alpha phase volume fraction of 20-50%, and then secondary ageing treatment at 550-700 deg.c for 2-10 hr to control nanometer size alpha in the microstructure 2 The volume fraction of the phase ensures the good matching of the thermal strength and the thermal stability of the titanium alloy, so that the comprehensive mechanical property of the high-temperature titanium alloy meets the service requirement at 550 ℃ and above.
Description
Technical Field
The invention belongs to the field of titanium alloy, and in particular relates to a method for improving creep property of titanium alloy, which can be used for a long time at 550 ℃ and above.
Background
The high-temperature titanium alloy is used at 400℃ or aboveTitanium alloys, including near alpha and martensitic alpha + beta two-phase high temperature titanium alloys. The high-temperature titanium alloy is usually solid-solution strengthened by adopting alloy elements and is matched with the comprehensive properties such as heat resistance, heat stability and the like by combining a thermal mechanical treatment process. However, when the use temperature exceeds 500 ℃, the solid solution strengthening effect of the alloy element is weakened, and the use requirements of creep deformation, durability and other heat strength indexes of the high-temperature titanium alloy cannot be ensured by means of solid solution strengthening. Alpha 2 The phase and silicide have higher strength at high temperature and thus can pass through alpha 2 The dispersion strengthening effect of the phase and silicide improves the heat resistance of the titanium-based alloy.
α 2 The phase is Ti 3 Intermetallic compound mainly composed of Al and having DO 19 Structural, ordered phases which typically precipitate during aging or during thermal exposure. When the electron concentration of the alloy exceeds 2.12 or the equivalent of aluminum exceeds 9%, α under appropriate conditions 2 The phase will be precipitated, the precipitation length of which is greater than that of alpha in the binary system of Ti-Al 2 Phase (Ti) 3 Al) has the same characteristics. Alpha 2 The phase is embrittling phase alpha 2 Phase precipitation will lead to embrittlement tendency of the alloy and reduce room temperature plasticity of the high temperature titanium alloy. Due to alpha 2 The high temperature strength of the phase is much higher than that of the alpha phase, which allows the use of alpha 2 Phase strengthening of high temperature titanium alloys is possible. Alpha 2 The strengthening effect of the phase is closely related to the volume fraction, size and distribution thereof.
α 2 The precipitation and growth of the phase are related to the chemical components, the thermo-mechanical treatment process and other factors of the titanium-based alloy, so that the alpha in the titanium-based alloy is controlled to ensure that the thermal stability and the thermal strength of the titanium-based alloy meet the use requirements 2 Phase precipitation and growth control are particularly important.
Disclosure of Invention
The traditional high-temperature titanium alloy with the use temperature below 550 ℃ is mainly reinforced by adopting technical measures such as grain refinement, solid solution reinforcement and the like. However, as the use temperature increases, the strengthening measures such as grain refinement and the like are not beneficial to the improvement of creep resistance of the titanium-based alloy, and the solid solution strengthening effect of alloy elements is also obviously reduced; thus, the precipitation strengthening effect of the second phase is adoptedThe high temperature strength, creep resistance and other heat strength performances of the Gao Taiji alloy become main technical means. By means of intermetallic compounds alpha 2 The precipitation strengthening effect of the phase improves the creep resistance of the titanium alloy and is one of the main technical approaches for developing novel high-temperature titanium alloy.
In order to meet the technical requirement of improving the heat resistance, the invention provides a method for improving the creep property of a titanium alloy, which comprises the following steps: alpha is coordinated and controlled by controlling the electron concentration and the heat treatment system of the alloy 2 The volume fraction of the phase is matched with the thermal stability and the thermal strength of the titanium-based alloy, so that the comprehensive mechanical property of the titanium alloy is improved.
The technical scheme adopted by the invention is as follows:
a method for improving creep property of titanium alloy, which is characterized by comprising the following steps: using electron concentration formula ΣN i f i α ＝2(f Ti +f Zr )+3(f Al +f Ga +f V )+4(f Sn +f Nb )+5f Mo +6f o Calculating the electron concentration of the titanium alloy, wherein N i Represents the number of valence electrons of the ith element, f i Represents the atomic percent of the ith element in the alpha phase; when the electron concentration ΣN i f i α Alpha at > 2.12 2 The phase will be separated out, the electron concentration value is regulated and controlled by the alloy element content and the heat treatment process is combined to alpha 2 The phases are coordinated and controlled, so that the creep property of the titanium alloy is improved, and the service temperature of the titanium alloy is increased.
The invention obtains a double-state structure consisting of a primary alpha phase and a beta transition structure through double heat treatment, and carries out the treatment on alpha in a microstructure 2 The phases are coordinated and controlled, so that the titanium alloy is well matched with the heat stability and the heat strength
In order to obtain a binary structure with good comprehensive performance, the titanium alloy fully deformed by the alpha+beta two-phase region is subjected to a first reheating treatment in the two-phase region, wherein the heat treatment temperature is T β The temperature below the phase transition temperature is 20-60 ℃, the heat treatment time is 2-4 h, and the volume fraction of the primary alpha phase is controlled to be 20-50% by the heat treatment, so that a binary structure consisting of the primary alpha phase and the beta transition structure is obtained.
Carrying out second ageing treatment for 2-10 h on the titanium alloy subjected to the first reheating treatment at 550-700 ℃ and carrying out nano-size alpha in a microstructure 2 The volume fraction of the phases is coordinated and controlled, so that the creep property and the comprehensive property of the titanium alloy are improved.
The volume fraction of the primary alpha phase is effectively controlled by the first reheating treatment and the alpha phase is combined with the second reheating treatment 2 The volume fraction of the phase precipitation is coordinated and controlled to obtain a bimodal structure composed of a primary alpha phase and a beta transformation structure, so that the heat intensity of the titanium alloy is improved, the heat stability is ensured, and the comprehensive performance of the novel high-temperature titanium alloy meets the service requirement at 550 ℃ and above.
Compared with the prior art, the invention has the following advantages:
1. by controlling the electron concentration of the titanium alloy, the electron concentration of the titanium alloy is controlled to be alpha 2 The volume fraction of the phase is effectively controlled, the strength and the plasticity of the alloy are coordinated and controlled in a wider range, and the requirement of the service temperature above 550 ℃ is met.
2. By at T β The alpha and beta two-phase region below the phase transition temperature of 20-60 ℃ is subjected to first reheating treatment, the volume fraction of the primary alpha phase is controlled to be 20-50%, a binary structure consisting of the primary alpha phase and the beta transition structure is obtained, and the structure has excellent heat stability and heat intensity matching and good comprehensive performance.
3. Heat treatment is carried out at 550-700 ℃ for alpha 2 Volume fraction of phases is coordinated and controlled by alpha 2 The strengthening effect of the phase improves the creep and lasting resistance of the titanium alloy, and achieves the aim of improving the heat resistance of the alloy, thereby improving the temperature resistance of the high-temperature titanium alloy.
4. The primary alpha phase and alpha phase are realized through the regulation and control of the heat treatment temperature and the heat preservation time 2 The coordination control of phases is matched with the strong plastic indexes such as the thermal stability, the thermal strength and the like of the titanium alloy, improves the comprehensive mechanical property of the titanium alloy, and ensures the service requirement of the titanium alloy at 550 ℃ and above.
Detailed Description
The invention is further illustrated, but not limited, by the following examples.
Example 1
The electron concentration of the Ti-Al-Sn-Zr-Mo-Si near alpha high temperature titanium alloy is 2.13, the Mo equivalent is 1.0%, and the alpha+beta/beta phase transition temperature is 1015 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-grade sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo and other intermediate alloys, and preparing titanium alloy cast ingots with uniform components through three times of smelting by utilizing a vacuum consumable arc furnace. 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that after heat preservation is carried out for 2 hours at 990 ℃, air cooling is carried out, and the volume fraction of the primary alpha phase is about 20%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation at 600 ℃ for 6 hours, air cooling after heat preservation at 650 ℃ for 6 hours and air cooling after heat preservation at 700 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: alpha as the ageing temperature increases from 600 ℃ to 700 DEG C 2 The number of phases decreases, the size increases, alpha 2 The phase size is between 5nm and 15nm, and is mainly and uniformly precipitated in the primary alpha phase. The mechanical property test result shows that: aging samples at 700 ℃ have highest temperature and high-temperature strength; after 600 ℃/160MPa/100h creep test, the tested creep residual deformation 600 ℃ aged sample is 0.30%, 650 ℃ aged sample is 0.25%, 700 ℃ aged sample is 0.23%.
Example 2
The Ti-Al-Sn-Zr-Mo-Si-Nb series near alpha-type high temperature titanium alloy has electron concentration of 2.14 and Mo equivalent of 0.8 percent, and the alpha+beta/beta phase transition temperature is 1020 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. The titanium alloy cast ingot with uniform components is prepared by adopting 0-grade sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-Nb and other intermediate alloys and utilizing a vacuum consumable arc furnace through three times of smelting. 2) And (5) forging the cake material. Passing the ingot through beta sheetAfter two fires in the phase region are started, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that the temperature is kept for 2 hours at 995 ℃ and then the air cooling is carried out, and the volume fraction of the primary alpha phase is about 20%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation for 2h at 700 ℃, air cooling after heat preservation for 4h at 700 ℃ and air cooling after heat preservation for 8h at 700 ℃. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that as aging time increases from 2h to 8h at 700 ℃, α 2 The size of the phase is increased, the number is basically unchanged, alpha 2 The phase size is between 5nm and 15nm, and is mainly and uniformly precipitated in the primary alpha phase. The mechanical property test result shows that: the aging treatment temperature and the high-temperature strength are the highest when the temperature is kept at 700 ℃ for 8 hours, the residual deformation is tested after 600 ℃/160MPa/100 hours creep test, the aging treatment temperature is kept at 700 ℃ for 2 hours and is 0.28%, the aging sample is kept at 700 ℃ for 4 hours and is 0.22%, and the aging sample is kept at 700 ℃ for 8 hours and is 0.18%.
Example 3
The Ti-Al-Sn-Zr-Mo-Si-Nb-Ta is near alpha-type high-temperature titanium alloy, the electron concentration of the alloy is 2.146, the Mo equivalent is 0.6 percent, and the alpha+beta/beta phase transition temperature is 1020 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-Nb, al-Ta and other intermediate alloys, and preparing high-temperature titanium alloy ingots with uniform components by three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that after heat preservation for 2 hours at 990 ℃, water quenching is carried out, and the volume fraction of the primary alpha phase is about 30%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation at 600 ℃ for 6 hours, air cooling after heat preservation at 650 ℃ for 6 hours and air cooling after heat preservation at 700 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic groupThe observation result shows that: alpha as the ageing temperature increases from 600 ℃ to 700 DEG C 2 The number of phases decreases, the size increases, alpha 2 The phase size is between 5nm and 15nm, and is mainly and uniformly precipitated in the primary alpha phase. The mechanical property test result shows that: the temperature and high temperature strength of the 700 ℃ aging sample are the highest, 600 ℃/160MPa/100h creep residual deformation 600 ℃ aging sample is 0.32%, 650 ℃ aging sample is 0.27%, and 700 ℃ aging sample is 0.20%.
Example 4
The Ti-Al-Sn-Zr-Mo-Si-Nb-Ta-C is near alpha high temperature titanium alloy, the electron concentration of the alloy is 2.147, the Mo equivalent is 0.6 percent, and the alpha+beta/beta phase transition temperature is 1040 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and pure C, ti-Sn, al-Si, al-Mo, al-Nb, al-Ta and other intermediate alloys, and preparing high-temperature titanium alloy cast ingots with uniform components by three times of smelting by utilizing a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solid solution treatment system is that after heat preservation is carried out for 2 hours at 1000 ℃, water quenching is carried out, and the volume fraction of the primary alpha phase is about 40%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation for 2h at 650 ℃, air cooling after heat preservation for 4h at 650 ℃ and air cooling after heat preservation for 8h at 650 ℃. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microstructure observations indicate that as aging time increases at 650 ℃, α 2 The number of phases decreases, the size increases, alpha 2 The phase size is between 5nm and 15nm, and is mainly and uniformly precipitated in the primary alpha phase. The mechanical property test result shows that: the room temperature and high temperature strength of the aging at 650 ℃ for 8 hours is the highest, and after 600 ℃/160MPa/100 hours creep test, the residual deformation is 650 ℃ for 2 hours, 650 ℃ for 4 hours and 650 ℃ for 8 hours is 0.26 percent.
Example 5
The electron concentration of the Ti-Al-Sn-Zr-Mo-W-Si series alpha+beta high temperature titanium alloy is 2.13, the Mo equivalent is 2.5%, and the alpha+beta/beta phase transition temperature is 990 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-W and other intermediate alloys, and preparing high-temperature titanium alloy cast ingots with uniform components through three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that the temperature is kept at 950 ℃ for 2 hours and then the air cooling is carried out, and the volume fraction of the primary alpha phase is about 30%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems of air cooling after heat preservation at 550 ℃ for 6 hours, air cooling after heat preservation at 600 ℃ for 6 hours and air cooling after heat preservation at 650 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: alpha was observed for all 3 heat treatment samples 2 Phase, alpha 2 The phase is evenly precipitated in the primary alpha phase, and the size is between 5 and 10 nm; as the aging temperature increases, α 2 The phase size is increased, the quantity is less, namely, in 3 heat treatment systems, the sample alpha is aged at 550 DEG C 2 The phase size is minimum, the quantity is maximum, the distribution is most diffuse, and the aging sample alpha is 650 DEG C 2 The phase size is the largest and the number is the smallest.
The mechanical property test result shows that: after a creep test at 550 ℃/300MPa/100h, the creep residual deformation of the 3 heat treatment systems is respectively 0.27% of an aging sample at 550 ℃, 0.23% of an aging sample at 600 ℃ and 0.25% of an aging sample at 650 ℃.
Example 6
The electron concentration of the Ti-Al-Sn-Zr-Mo-W-Si series alpha+beta high temperature titanium alloy is 2.135, the Mo equivalent is 4.5%, and the alpha+beta/beta phase transition temperature is 985 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-W and other intermediate alloys, and preparing high-temperature titanium alloy cast ingots with uniform components through three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. Passing the ingot through betaAfter two fires in the single-phase zone are fired, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that the temperature is kept at 945 ℃ for 2 hours, then the air cooling is carried out, and the volume fraction of the primary alpha phase is about 30%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems of air cooling after heat preservation at 550 ℃ for 6 hours, air cooling after heat preservation at 600 ℃ for 6 hours and air cooling after heat preservation at 650 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: alpha was observed for all 3 heat treatment samples 2 Phase, alpha 2 The phase is evenly precipitated in the primary alpha phase, and the size is between 5 and 10 nm; as the aging temperature increases, α 2 The phase size is increased, the quantity is less, namely, in 3 heat treatment systems, the sample alpha is aged at 550 DEG C 2 The phase size is the smallest and the number is the largest, and the aging of sample alpha is 650 DEG C 2 The phase size is the largest and the number is the smallest. The mechanical property test result shows that: after a creep test at 550 ℃/300MPa/100h, the creep residual deformation of the 3 heat treatment systems is respectively 0.25% of an aging sample at 550 ℃, 0.20% of an aging sample at 600 ℃ and 0.18% of an aging sample at 650 ℃.
Comparative example 1
Ti-Al-Sn-Zr-Mo-Si based near alpha type high temperature titanium alloy (corresponding to example 1) having an electron concentration of 2.11 and a Mo equivalent of 1.0 and an alpha+beta/beta phase transition temperature of 1015 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo and other intermediate alloys, and preparing high-temperature titanium alloy ingots with uniform components through three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that after heat preservation is carried out for 2 hours at 990 ℃, water quenching is carried out, and the volume fraction of the primary alpha phase is about 20%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation at 600 ℃ for 6 hours, air cooling after heat preservation at 650 ℃ for 6 hours and air cooling after heat preservation at 700 ℃ for 6 hours. 5) At the position ofAnd cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: no alpha was observed for all 3 heat treatment samples 2 Phase, illustrating ordered alpha in high temperature titanium alloy when the electron concentration of the alloy is 2.11 2 The phase cannot be precipitated. The mechanical property test result shows that: the room temperature strength, the high temperature strength and the creep property of the high temperature titanium alloy under the 3 aging system are not greatly different. However, after 600 ℃/160MPa/100h creep test, the creep residual deformation of the alloy is about 0.5%, which is obviously lower than the creep performance of the high-temperature titanium alloy in example 1.
Comparative example 2
Ti-Al-Sn-Zr-Mo-Si-Nb-Ta is a near alpha-type high temperature titanium alloy (corresponding to embodiment 3), the electron concentration of the alloy is 2.118, the Mo equivalent is 0.6%, and the alpha+beta/beta phase transition temperature is 1020 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-Nb, al-Ta and other intermediate alloys, and preparing high-temperature titanium alloy ingots with uniform components by three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that the temperature is maintained at 995 ℃ for 2 hours, then water quenching is carried out, and the volume fraction of the primary alpha phase is about 20%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems, namely air cooling after heat preservation at 600 ℃ for 6 hours, air cooling after heat preservation at 650 ℃ for 6 hours and air cooling after heat preservation at 700 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: no alpha was observed for all 3 heat treatment samples 2 Phase, illustrating ordered alpha in high temperature titanium alloy when the electron concentration of the alloy is 2.118 2 The phase cannot be precipitated. The mechanical property test result shows that: the room temperature strength, the high temperature strength and the creep property of the high temperature titanium alloy under the 3 aging system are not greatly different. However, after 600 ℃/160MPa/100h creep test, the creep residual deformation of the alloy is about 0.41 percent,significantly lower than the creep properties of the high temperature titanium alloy of example 3.
Comparative example 3
Ti-Al-Sn-Zr-Mo-W-Si series alpha+beta type high temperature titanium alloy (corresponding to example 5), the electron concentration of the alloy was 2.117 and the Mo equivalent was 2.5%, the α+β/β phase transition temperature was 990 ℃.
The preparation method of the titanium alloy comprises the following steps: 1) Smelting the cast ingot. Adopting 0-level sponge Ti, sponge Zr, pure Al and other pure metals and Ti-Sn, al-Si, al-Mo, al-W and other intermediate alloys, and preparing high-temperature titanium alloy cast ingots with uniform components through three times of smelting by using a vacuum consumable arc furnace; 2) And (5) forging the cake material. After the ingot is cogged by two fires in a beta single-phase zone, at T β After three-fire heat processing at 30-50 deg.c, the material is forged into cake with phi 300X 70mm, with deformation amount of over 60% in each fire. 3) And (5) solution treatment. The solution treatment system is that the temperature is kept at 950 ℃ for 2 hours and then the air cooling is carried out, and the volume fraction of the primary alpha phase is about 30%; 4) And (5) aging treatment. The aging treatment system comprises 3 aging treatment systems of air cooling after heat preservation at 550 ℃ for 6 hours, air cooling after heat preservation at 600 ℃ for 6 hours and air cooling after heat preservation at 650 ℃ for 6 hours. 5) And cutting off a chord direction sample on the cake material for microscopic structure observation and mechanical property test.
Microscopic observations indicate that: no alpha was observed for all 3 heat treatment samples 2 Phase, illustrating ordered alpha in high temperature titanium alloy when the electron concentration of the alloy is 2.117 2 The phase cannot be precipitated.
The mechanical property test result shows that: the room temperature strength, the high temperature strength and the creep property of the high temperature titanium alloy under the 3 aging system are not greatly different. However, after a creep test at 550 ℃/300MPa/100h, the creep deformation residual of the alloy is about 0.52%, which is obviously lower than the creep performance of the high-temperature titanium alloy in example 5.
The foregoing description is only a preferred embodiment of the present invention, and is not intended to limit the present invention, and any simple modification, variation and equivalent structural changes of the foregoing embodiment according to the present technology fall within the scope of the technical solution of the present invention.
Furthermore, descriptions of well-known structures and techniques are omitted so as to not unnecessarily obscure the present invention.
Claims (5)
1. A method for improving creep property of titanium alloy, which is characterized by comprising the following steps: using electron concentration formula ΣN i f i α ＝2(f Ti +f Zr )+3(f Al +f Ga +f V )+4(f Sn +f Nb )+5f Mo +6f o Calculating the electron concentration of the titanium alloy, wherein N i Represents the number of valence electrons of the ith element, f i Represents the atomic percent of the ith element in the alpha phase; when the electron concentration ΣN i f i α Alpha at > 2.12 2 The phase will precipitate, and the electron concentration value and the heat treatment process are combined to obtain alpha 2 The phases are coordinated and controlled, so that the creep property of the titanium alloy is improved.
2. The method for improving creep properties of a titanium alloy according to claim 1, wherein: obtaining a bimodal structure consisting of a primary alpha phase and a beta transformed structure by double heat treatment, and subjecting the microstructure to alpha 2 The phases are coordinated and controlled, so that the titanium alloy is well matched with heat stability and heat intensity.
3. The method for improving creep properties of a titanium alloy according to claim 1 or 2, wherein: at T β And (3) carrying out first reheating treatment on the high-temperature titanium alloy for 2-4 hours in an alpha+beta two-phase region with the temperature of 20-60 ℃ below the phase transition temperature, and controlling the volume fraction of the primary alpha phase to be 20-50% to obtain a binary structure consisting of the primary alpha phase and the beta transition structure.
4. The method for improving creep properties of a titanium alloy according to claim 1 or 2, wherein: performing a second aging treatment at 550-700 ℃ for 2-10 h, and performing a second aging treatment on the nano-size alpha in the microstructure 2 The volume fraction of the phases is coordinated and controlled, so that the creep property and the comprehensive property of the titanium alloy are improved.
5. A titanium alloy prepared by the method of claim 1, wherein: the titanium alloy can meet the service requirement of 550 ℃ and above.
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