CN112322936A - Anti-oxidation high-temperature titanium alloy and preparation method thereof - Google Patents

Anti-oxidation high-temperature titanium alloy and preparation method thereof Download PDF

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CN112322936A
CN112322936A CN202011219506.3A CN202011219506A CN112322936A CN 112322936 A CN112322936 A CN 112322936A CN 202011219506 A CN202011219506 A CN 202011219506A CN 112322936 A CN112322936 A CN 112322936A
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titanium alloy
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CN112322936B (en
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肖文龙
许雅群
赵新青
马朝利
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Beihang University
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • 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
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • 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
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    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
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Abstract

The invention belongs to the field of titanium alloy materials, and particularly relates to an antioxidant high-temperature titanium alloy and a preparation method thereof, wherein the high-temperature titanium alloy is a near-alpha titanium alloy and comprises the following alloy components: al5.7wt% -7.0 wt%, Sn1.5wt% -3.0 wt%, Hf2.5wt% -5.0 wt%, Si0.2wt% -0.6 wt%, Nb1.5wt% -4.0 wt%, W0.5wt% -4.0 wt%, and the balance of Ti and unavoidable impurities; wherein, the content of Nb and W satisfies Nb/0.36+ W/0.22 and is less than or equal to 0.25. The high-temperature titanium alloy prepared by the invention has excellent oxidation resistance, high heat strength and good heat stability.

Description

Anti-oxidation high-temperature titanium alloy and preparation method thereof
Technical Field
The invention belongs to the field of titanium alloy materials, and particularly relates to an antioxidant high-temperature titanium alloy and a preparation method thereof.
Background
High-temperature titanium alloys are widely used for manufacturing fan blades, compressor blades, blisks and casings of aircraft engines because of their excellent specific strength, specific creep strength and specific fatigue strength. For an advanced aircraft engine, the amount of the high-temperature titanium alloy is at least 20% of the total structural mass of the engine. Because the blades of the compressor of the aircraft engine are close to the combustion chamber, the working temperature of the blades is generally 500-600 ℃ or even higher. However, the high temperature titanium alloy widely used internationally, such as IMI834 in UK, Ti1100 in USA and BT36 in Russia, can not break 600 ℃ for a long time.
At present, the development of the high-temperature titanium alloy to higher temperature is limited mainly by two aspects: firstly, the surface of the titanium alloy is unstable, which means that a layer of oxygen-rich brittle layer is generated on the surface of the high-temperature titanium alloy when the high-temperature titanium alloy is exposed in a high-temperature environment, microcracks are generated under the action of certain stress, so that the titanium alloy is finally brittle and broken due to oxidation, and the oxidation resistance is reduced along with the rise of the temperature; secondly, the microstructure is unstable, and the brittle phase alpha is easy to separate out from the high-temperature titanium alloy with high Al content after high-temperature long-term aging2，α2Although the phase can improve the strength of the alloy to a certain extent, the plasticity of the titanium alloy is seriously reduced, so that the heat strength and the heat stability of the alloy are difficult to match.
Disclosure of Invention
Therefore, the invention utilizes the alloy design and the multi-component composite micro-alloying method to play the synergistic effect of Hf, Nb and W, controls the surface oxide phase content and the oxide film form under the high-temperature environment, enables the alloy to generate a continuous and compact oxide film on the surface under the high-temperature environment, improves the oxidation activation energy and has excellent oxidation resistance. Hf element in the high-temperature titanium alloy designed by the invention is represented as beta stability element, and the Hf element and the W element have synergistic effect, so that the weak beta stability element Nb is promoted to be dissolved in alpha phase in a solid manner, the strain energy of the alpha phase is increased, and the brittle phase alpha is inhibited2Precipitation and growth of alpha2Although the phase can improve the heat resistance of the alloy to a certain extent, the phase can improve the heat resistance of the alloyThe thermal stability of the alloy is seriously reduced, and alpha is controlled2The precipitation and growth of the alloy are beneficial to the good matching of the heat resistance and the heat stability of the alloy. Specifically, the invention designs a Ti-Al-Sn-Hf-W-Nb high-temperature titanium alloy, which meets the following requirements by controlling the contents of Nb and W: nb/0.36+ W/0.22 is less than or equal to 0.25, so that the alloy is a near-alpha titanium alloy structure which comprises a matrix alpha phase and a small amount of beta phase. The alpha phase with the hexagonal close-packed structure is beneficial to maintaining the high-temperature performance of the titanium alloy, a small amount of body-centered cubic beta phase can improve the room-temperature plasticity of the alloy, but the beta phase is too much, so that the alloy can be softened at high temperature. And then smelting and forging to obtain the high-temperature titanium alloy with refined structure, and then carrying out solid solution stabilization treatment on the alloy to prepare the high-temperature titanium alloy.
In order to achieve the aim, the invention provides an oxidation-resistant high-temperature titanium alloy, which is a near-alpha titanium alloy and comprises the following alloy components: 5.7 wt% -7.0 wt% of AlAl, 1.5 wt% -3.0 wt% of Sns, 2.5 wt% -5.0 wt% of Hf2, 0.2 wt% -0.6 wt% of Si, 1.5 wt% -4.0 wt% of Nb1, 0.5 wt% -4.0 wt% of W, and the balance of Ti and inevitable impurities; wherein, the content of Nb and W satisfies Nb/0.36+ W/0.22 and is less than or equal to 0.25.
Preferably, the content of Nb and W satisfies Nb/0.36+ W/0.22-0.078.
Preferably, the content of Nb and W satisfies Nb/0.36+ W/0.22-0.101.
Preferably, the content of Nb and W satisfies that Nb/0.36+ W/0.22 is 0.146.
Preferably, the content of Nb and W satisfies Nb/0.36+ W/0.22-0.237.
Preferably, after the high-temperature titanium alloy is oxidized at 750 ℃ for 700 hours, a continuous and compact oxide film is generated on the surface, and the oxidation weight gain per unit area is not more than 1.7mg/cm2. The high-temperature titanium alloy is subjected to an oxidation experiment at 750 ℃, and a large amount of compact Al is generated on the surface2O3Phase, less porous TiO2And a continuous and compact oxide film is formed, so that the alloy has excellent oxidation resistance, and the alloy has good toughness matching.
Preferably, when the high-temperature titanium alloy is not subjected to high-temperature heat exposure, the compressive yield strength is more than or equal to 914MPa and the fracture strain is more than or equal to 24.4 percent at room temperature; at the temperature of 600-650 ℃, the compressive yield strength is more than or equal to 461MPa, and the fracture strain is more than or equal to 38.9 percent; after the high-temperature titanium alloy is exposed for 1000 hours at 600-650 ℃, the compressive yield strength is more than or equal to 973MPa and the fracture strain is more than or equal to 13.4% at room temperature; at 600-650 ℃, the compressive yield strength is more than or equal to 554MPa, and the fracture strain is more than or equal to 36.8%. After long-time high-temperature heat exposure, the strength of the high-temperature titanium alloy is increased by 20%, and the plasticity loss is not more than 5.5%.
The invention also provides a method for preparing the high-temperature titanium alloy, which comprises the following steps:
step 1: preparing raw materials of a pure aluminum ingot, an aluminum-silicon intermediate alloy, an aluminum-tungsten intermediate alloy, an aluminum-niobium intermediate alloy, a pure tin ingot, an aluminum-hafnium intermediate alloy and titanium sponge;
step 2: sequentially putting the raw materials into a furnace according to the melting point of the alloy from low to high, smelting in an argon environment, cooling, and taking out an alloy ingot;
and step 3: spraying an anti-oxidation coating on the surface of the alloy ingot, and then performing cogging forging at 850-1150 ℃, wherein the total deformation of the alloy ingot is 50-60 percent after 5 times of total forging;
and 4, step 4: putting the forged alloy ingot into a tube furnace, filling argon for protection in the tube furnace, carrying out solution treatment at 1050-1100 ℃ for 2h, and then carrying out air cooling to room temperature; and then stabilizing the alloy ingot at 670-760 ℃ for 2h in an argon environment, and then air-cooling to room temperature to prepare the high-temperature titanium alloy.
The invention further provides the application of the high-temperature titanium alloy, and the high-temperature titanium alloy can be used for compressor blades of aero-engines close to combustion chambers.
The invention has the beneficial effects that:
1) the high-temperature titanium alloy has excellent oxidation resistance at the temperature of more than 650 ℃. The oxidation resistance is remarkably superior to that of typical high-temperature titanium alloys IMI834 and Ti1100 which are commercially applied;
2) after the high-temperature titanium alloy is subjected to thermal exposure for 1000 hours at 650 ℃, the compression strength is increased by 20%, the plasticity loss is not more than 5.5%, and the alloy still has good high-temperature strength and plasticity matching after the high-temperature long-time thermal exposure.
Drawings
FIG. 1 is a gold phase diagram of a high temperature titanium alloy prepared in example 1 of the present invention and a high temperature titanium alloy prepared in comparative example 1;
FIG. 2 is SEM images of the high temperature titanium alloy prepared in example 1 of the present invention and the high temperature titanium alloy prepared in comparative example 1 after oxidizing at 750 ℃ for 700 h;
FIG. 3 is a comparison of oxidation weight gain curves of the high temperature titanium alloy prepared in example 1 of the present invention and the high temperature titanium alloy prepared in comparative example 1 after oxidation at 750 ℃ for 700 hours;
FIG. 4 is a graph comparing the oxidation weight gain curve of the high temperature titanium alloy prepared in example 1 of the present invention oxidized at 750 ℃ for 700h with the oxidation weight gain curve of the typical high temperature titanium alloy IMI834 and Ti1100 prepared in comparative example 2 oxidized at 750 ℃ for 100 h;
FIG. 5 is a graph showing room temperature and high temperature (650 ℃) compressive properties of the high temperature titanium alloy prepared in example 1 of the present invention and the high temperature titanium alloy prepared in comparative example 3 in their original states;
FIG. 6 is a graph showing the room temperature and high temperature (650 ℃) compression properties of the high temperature titanium alloy prepared in example 1 of the present invention and the high temperature titanium alloy prepared in comparative example 3 after being exposed to 650 ℃ for 1000 hours.
Detailed Description
The present invention is further described below with reference to the accompanying drawings, examples and comparative examples, it being understood that the examples and comparative examples described below are intended to facilitate the understanding of the present invention and are not intended to limit it in any way.
Example 1
In this embodiment, a high temperature titanium alloy is prepared, which comprises the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 2.0%, W: 4.0 percent, wherein the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.237, and the balance is Ti and inevitable impurities. The preparation method comprises the following specific steps:
step 1: preparing pure aluminum ingots, aluminum-silicon intermediate alloys, aluminum-tungsten intermediate alloys, aluminum-niobium intermediate alloys, pure tin ingots, aluminum-hafnium intermediate alloys and titanium sponge according to the mass percentage of the elements, and ultrasonically cleaning the raw materials to remove surface impurities.
Step 2: the raw materials are sequentially put into a water-cooled copper crucible vacuum consumable arc furnace from low to high according to the melting point of the alloy, and then the smelting furnace is vacuumized until the vacuum degree reaches 10-3Pa, then filling argon into the furnace, smelting for 6 times, cooling, and taking out the alloy ingot.
And step 3: spraying an anti-oxidation coating on the surface of an alloy ingot, performing cogging forging at 850-1150 ℃, and performing total forging for 5 times, wherein the specific process refers to the following table 1, and the total deformation is 50%.
TABLE 1 forging Process
Figure BDA0002761570340000041
And 4, step 4: and (3) filling argon gas for protection in a tubular furnace, carrying out solution treatment at 1100 ℃ for 2h, air-cooling to room temperature, and then carrying out stabilization treatment at 750 ℃ for 2h, air-cooling to room temperature to obtain the high-temperature titanium alloy.
Comparative example 1
The comparative example prepares a high-temperature titanium alloy consisting of the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 2.0%, W: 0% by weight, and the balance Ti and inevitable impurities. The specific preparation steps are the same as those in the examples, and are not described herein again.
Comparing the phase structure of the high-temperature titanium alloy with the composition prepared in example 1 and the high-temperature titanium alloy (without W) in comparative example 1, it can be seen from fig. 1 that the α -phase lath of the high-temperature titanium alloy prepared in example 1 is significantly refined, the width is 500-600 nm, the fine-grain strengthening effect is significant at room temperature, and the addition of W element with high melting point in example 1 is beneficial to improving the high-temperature strength of the alloy.
Example 2
The high temperature titanium alloys prepared in example 1 and comparative example 1 were oxidized at 750 ℃ for 700 hours, respectively.
FIG. 2 is an SEM image of the high temperature titanium alloy prepared in example 1 and the high temperature titanium alloy prepared in comparative example 1 after oxidizing at 750 ℃ for 700h, and it can be seen that they are compared with those of comparative example1, the oxide film generated on the surface of the high-temperature titanium alloy prepared in the example 1 (the content of Nb and W is satisfied, and Nb/0.36+ W/0.22 is equal to 0.237) is more continuous and compact after the high-temperature titanium alloy is oxidized at 750 ℃ for 700 h. It can be seen from this example that the co-addition of Nb and W promotes densification of Al in the alloy2O3The formation of the thin film suppresses the diffusion of O into the substrate.
FIG. 3 shows the oxidation weight gain per unit area of the high temperature titanium alloy of example 1 and comparative example 1 after oxidizing at 750 ℃ for 700h as a function of time, and it can be seen that the oxidation weight gain per unit area of the alloy of example 1 after oxidizing at 700h is not more than 1.7mg/cm2While the alloy of comparative example 1 after 700h of high-temperature oxidation has an oxidation weight increase of 2.6mg/cm2This shows that example 1 has significantly improved oxidation performance and significantly reduced oxidation weight gain compared to comparative example 1.
Comparative example 2
After typical high-temperature titanium alloy Ti1100 (USA) and IMI834 (UK) are oxidized for 100h at 750 ℃, the oxidation weight gain per unit area of the two alloys is shown in figure 4, and the oxidation weight gain per unit area of the high-temperature titanium alloy Ti1100 reaches 1.99mg/cm2The oxidation weight gain of the unit area of the high-temperature titanium alloy IMI834 reaches 1.82mg/cm2The oxidation weight gain of the titanium alloy prepared in the embodiment 2 of the invention in unit area after high-temperature oxidation for 700h is not more than 0.6mg/cm2. Obviously, compared with high-temperature titanium alloys Ti1100 and IMI834, the high-temperature titanium alloy designed by the invention has higher oxidation resistance.
Comparative example 3
The comparative example prepares a high-temperature titanium alloy consisting of the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 4.0%, W: 4.0 percent, wherein the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.293, and the balance is Ti and inevitable impurities. The specific preparation steps are the same as those in example 1, and are not described herein again.
Example 3
The mechanical properties of the high-temperature titanium alloys prepared in example 1 and comparative example 3 were tested by a compression tester at room temperature and 650 ℃, respectively, and as shown in fig. 5, when the high-temperature titanium alloy prepared in example 1 is not subjected to 650 ℃ (i.e. in the original state), the compressive yield strength is not less than 914MPa and the breaking strain is not less than 24.4% at room temperature; at 650 ℃, the compressive yield strength is more than or equal to 461MPa, and the fracture strain is more than or equal to 38.9 percent. When the high-temperature titanium alloy prepared in the comparative example 3 is not subjected to 650 ℃ heat exposure (namely in an original state), the compressive yield strength is more than or equal to 931MPa and the breaking strain is more than or equal to 21.4% at room temperature; but at 650 ℃, the compressive yield strength is more than or equal to 248MPa, and the fracture strain is more than or equal to 35.6 percent. Comparative example 3 the alloy was made to be an α + β two-phase structure by adding an excess of β stabilizing elements Nb and W. At high temperatures, excessive body-centered cubic beta phase causes the alloy to soften rapidly at high temperatures, reducing the strength at 650 ℃.
And then, sealing the two high-temperature titanium alloys in vacuum, carrying out heat exposure for 1000h at 650 ℃, taking out, and testing the mechanical properties of the titanium alloys at room temperature and 650 ℃ by using a compression tester respectively. As can be seen from FIG. 6, after the high temperature titanium alloy prepared in example 1 is exposed for 1000h at 650 ℃, the compressive yield strength is not less than 973MPa and the fracture strain is not less than 13.4% at room temperature; at 650 ℃, the compressive yield strength is more than or equal to 554MPa, and the fracture strain is more than or equal to 36.8 percent. After the high-temperature titanium alloy prepared in the comparative example 3 is subjected to thermal exposure for 1000 hours at 650 ℃, the compressive yield strength is more than or equal to 889MPa and the fracture strain is more than or equal to 21.8 percent at room temperature; at 650 ℃, the compressive yield strength is more than or equal to 267MPa, and the fracture strain is more than or equal to 37.2 percent.
Comparing example 1 with comparative example 3, it was found that the high temperature strength of the high temperature titanium alloy prepared in example 1 was increased by 20% and the plastic loss was not more than 5.5% after the high temperature long-term heat exposure. The high-temperature titanium alloy prepared by the comparative example 3(Nb/0.36+ W/0.22 is 0.293) has the strength of less than 300MPa at high temperature and cannot meet the use requirement.
In conclusion, the high-temperature titanium alloy prepared by the invention has good mechanical properties, and still has good toughness matching after long-term heat exposure at high temperature, and particularly the high-temperature performance is obviously improved.
Example 4
In this embodiment, a high temperature titanium alloy is prepared, which comprises the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 1.5%, W: 0.8 percent, and the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.078, and the balance is Ti and inevitable impurities. The specific preparation steps are the same as those in example 1, and are not described herein again.
Example 5
In this embodiment, a high temperature titanium alloy is prepared, which comprises the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 1.5%, W: 1.3 percent, and the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.101, and the balance is Ti and inevitable impurities. The specific preparation steps are the same as those in example 1, and are not described herein again.
Example 6
In this embodiment, a high temperature titanium alloy is prepared, which comprises the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 2.0%, W: 2.0 percent, and the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.146, and the balance is Ti and inevitable impurities. The specific preparation steps are the same as those in example 1, and are not described herein again.
Example 7
In this embodiment, a high temperature titanium alloy is prepared, which comprises the following components in percentage by mass: al: 6.5%, Sn: 2.0%, Hf: 4.0%, Si: 0.2%, Nb: 4.0%, W: 3.0 percent, and the content of Nb and W meets the following requirements: nb/0.36+ W/0.22 is 0.25, and the balance is Ti and inevitable impurities. The specific preparation steps are the same as those in example 1, and are not described herein again.
The six high temperature titanium alloys prepared in example 1, comparative example 3, and examples 4 to 7 were tested for mechanical properties at room temperature and 650 deg.c using a tensile tester, respectively, and the results are shown in table 2 below.
Table 2 shows the tensile mechanical properties of six high-temperature titanium alloys at room temperature and a high temperature of 650 DEG C
Figure BDA0002761570340000071
As can be seen from the above Table 2, the titanium alloy composition is controlled within the range of Nb/0.36+ W/0.22 ≤ 0.25, which is beneficial for obtaining better mechanical properties, especially high temperature mechanical properties at 650 ℃.
It will be apparent to those skilled in the art that various modifications and improvements can be made to the embodiments of the present invention without departing from the inventive concept thereof, and these modifications and improvements are intended to be within the scope of the invention.

Claims (9)

1. The oxidation-resistant high-temperature titanium alloy is characterized in that the high-temperature titanium alloy is a near-alpha titanium alloy and comprises the following alloy components: 5.7 wt% -7.0 wt% of AlAl, 1.5 wt% -3.0 wt% of Sn1, 2.5wt% -5.0 wt% of Hf2, 0.2 wt% -0.6 wt% of Si0, 1.5 wt% -4.0 wt% of Nb1, 0.5 wt% -4.0 wt% of W, and the balance of Ti and inevitable impurities; wherein, the content of Nb and W satisfies Nb/0.36+ W/0.22 and is less than or equal to 0.25.
2. A high temperature titanium alloy according to claim 1, wherein the Nb and W contents satisfy Nb/0.36+ W/0.22-0.078.
3. A high temperature titanium alloy as claimed in claim 1, wherein the Nb and W contents satisfy 0.101-0.36 + 0.22.
4. A high temperature titanium alloy as claimed in claim 1, wherein the Nb and W contents satisfy 0.146 Nb/0.36+ W/0.22.
5. A high temperature titanium alloy as claimed in claim 1, wherein the Nb and W contents satisfy Nb/0.36+ W/0.22-0.237.
6. A high temperature titanium alloy as claimed in claim 1, wherein the surface of the high temperature titanium alloy is oxidized at 750 ℃ for 700h to form a continuous and dense oxide film, and the oxidation weight increase per unit area is not more than 1.7mg/cm2。
7. A high temperature titanium alloy as claimed in claim 1, wherein said high temperature titanium alloy has a compressive yield strength of not less than 914MPa and a strain at break of not less than 24.4% at room temperature without high temperature thermal exposure; at the temperature of 600-650 ℃, the compressive yield strength is more than or equal to 461MPa, and the fracture strain is more than or equal to 38.9 percent;
after the high-temperature titanium alloy is exposed for 1000 hours at 600-650 ℃, the compressive yield strength is more than or equal to 973MPa and the fracture strain is more than or equal to 13.4% at room temperature; at 600-650 ℃, the compressive yield strength is more than or equal to 554MPa, and the fracture strain is more than or equal to 36.8%.
8. A method of making a high temperature titanium alloy according to any one of claims 1 to 7, comprising the steps of:
step 1: preparing raw materials of pure aluminum ingots, aluminum-silicon intermediate alloys, aluminum-tungsten intermediate alloys, aluminum-niobium intermediate alloys, pure tin ingots, aluminum-hafnium intermediate alloys and titanium sponge according to target components;
step 2: sequentially putting raw materials into a furnace according to the melting point of the alloy from low to high, smelting in an argon environment, cooling, and taking out an alloy ingot;
and step 3: spraying an anti-oxidation coating on the surface of the alloy ingot, and then performing cogging forging at 850-1150 ℃, wherein the total deformation of the alloy ingot is 50-60 percent after 5 times of total forging;
and 4, step 4: putting the forged alloy ingot into a tube furnace, filling argon for protection in the tube furnace, carrying out solution treatment at 1050-1100 ℃ for 2h, and then carrying out air cooling to room temperature; and then stabilizing the alloy ingot at 670-760 ℃ for 2h in an argon environment, and then air-cooling to room temperature to prepare the high-temperature titanium alloy.
9. Use of a high temperature titanium alloy according to any one of claims 1 to 7 in a compressor blade in an aircraft engine close to a combustion chamber.
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