Method for improving mechanical properties of high-temperature titanium alloy containing ta, product and application

Abstract

This invention discloses a method, product, and application for improving the mechanical properties of Ta-containing high-temperature titanium alloys, belonging to the field of titanium alloy forging technology. The titanium alloy contains Ti, Al, W, Si, C, Sn, and Ta by mass ratio, with a Ta content of 2-6%. The preparation method includes: mixing raw materials, pressing them into electrodes, and welding them into consumable electrodes; obtaining an ingot through vacuum consumable arc melting; hot deformation through two-stage single-phase forging, two-stage two-phase hot deformation forging, and three-stage two-phase hot rolling; followed by solution treatment and aging treatment; and then an eighth-stage two-phase hot rolling and annealing treatment to finally obtain the Ta-containing high-temperature titanium alloy. This method, through the synergistic effect of multi-stage hot deformation and heat treatment processes, effectively promotes the uniform solid solution of Ta and the formation of a stable strengthening phase, enabling the alloy to maintain excellent high-temperature strength and plasticity at 700℃, making it suitable for high-temperature components in aerospace engines.

Description

Technical Field

[0001] This invention belongs to the field of titanium alloy forging technology, and particularly relates to a method, product and application for improving the mechanical properties of high-temperature titanium alloys containing Ta. Background Technology

[0002] High-temperature titanium alloys, characterized by high specific strength and excellent high-temperature service stability, serve as fundamental materials for key high-temperature components in aerospace engines, high-performance industrial gas turbines, and high-end equipment and special engineering fields. They are crucial for achieving lightweight components and long service life, and have gradually become an important design direction for medium- and high-temperature structural materials. With the advancement of aero-engine and special engineering technologies towards higher thrust-to-weight ratios and higher efficiency, the size of load-bearing components is continuously increasing, while higher requirements are being placed on service temperature and overall performance. Raising the upper limit of titanium alloy service temperature, overcoming the synergistic bottlenecks in high-temperature, lightweight, and complex component manufacturing, and developing a new generation of high-temperature titanium alloys have become important technological pathways for improving system performance and achieving engineering goals.

[0003] Service temperatures above 650℃ represent a critical performance bottleneck for titanium alloys. In this temperature range, alloys generally exhibit significant decreases in high-temperature strength, reduced microstructural stability, and severely inadequate creep and endurance resistance, making it difficult to meet the long-term reliable service requirements of medium- and high-temperature load-bearing components. Mature alloy systems capable of stable service under medium- and high-temperature conditions and meeting engineering application needs are limited, failing to cover the diverse performance requirements of different structural forms, manufacturing processes, and service environments. Therefore, to support the engineering applications of next-generation aero-engines, gas turbines, and other critical equipment, it is urgent to develop alloys with excellent high-temperature mechanical properties at 700℃ and compatible forging processes. Summary of the Invention

[0004] To address the aforementioned technical problems, this invention proposes a method, product, and application for improving the mechanical properties of Ta-containing high-temperature titanium alloys. To achieve the above objectives, this invention provides the following technical solution:

[0005] A method for improving the mechanical properties of high-temperature titanium alloys containing Ta includes the following steps: S1. Mix the raw materials Ti, Al, W, Si, C, Sn and Ta in the specified ratio, press them into electrode blocks, and weld them into consumable electrodes; S2. Vacuum consumable electrode is subjected to consumable arc melting to obtain ingot; S3. The ingot is sequentially subjected to two-stage forging in the single-phase region, two-stage hot deformation forging in the two-phase region, and three-stage hot rolling in the two-phase region, including: First-stage single-phase forging: heating the ingot to T β1The ingot is forged at 120–150℃ and held at this temperature for 120–150 min. A high-speed forging machine is used to perform a "one-upset-one-drawing" forging process. During the upsetting stage, the compressive deformation is 50–60%, corresponding to a deformation rate of 50–60 mm / min; during the drawing stage, the tensile deformation is 45–55%, corresponding to a deformation rate of 30–40 mm / min. The final forging temperature during the forging process is maintained at ≥T. β1 After forging at +20℃, the material is air-cooled to room temperature and its surface is then ground. T β1 The temperature ranges from 1020 to 1060℃. Second-stage single-phase forging: The forging obtained from the first-stage single-phase forging is heated to T. β1 The ingot is forged at 80–100℃ and held at this temperature for 120–150 min. A high-speed forging machine is used to perform a "one-upset-one-drawing" forging process. During the upsetting stage, the compressive deformation is 45–55%, corresponding to a deformation rate of 45–55 mm / min; during the drawing stage, the tensile deformation is 40–50%, corresponding to a deformation rate of 25–35 mm / min. The final forging temperature during the forging process is maintained at ≥T. β1 After forging at +20℃, the surface is cooled to room temperature by air cooling and then ground. Third-stage two-phase zone hot deformation forging: The forging blank obtained from the second-stage single-phase zone forging is heated to T. β1 - (20~40℃), and hold at this temperature for 150~180min, using a high-speed forging mill to perform a "drawing" forging process on the workpiece. During the drawing stage, the tensile deformation is 40~50%, corresponding to a deformation rate of 30~35mm / min, a single feed rate of 200~220mm, and a high-speed forging mill frequency of 3s / cycle. The final forging temperature during the forging process is maintained at ≥T. β1 -100℃, after forging, air-cooled to room temperature, and its surface is ground. Fourth-stage two-phase zone hot deformation forging: The forging billet obtained after the third-stage two-phase zone hot deformation forging is heated to T. β1 - (30~50℃), and hold at this temperature for 150~180min, using a high-speed forging mill to perform a "drawing" forging process on the workpiece. During the drawing stage, the tensile deformation is 35~40%, corresponding to a deformation rate of 25~30mm / min, a single feed rate of 200~220mm, and a high-speed forging mill frequency of 3s / cycle; the final forging temperature during the forging process is ≥T β1 -120℃, after forging, air-cooled to room temperature, and its surface is ground. Fifth-stage two-phase zone hot rolling: The forging billet obtained from the fourth-stage two-phase zone hot deformation forging is heated to T.β1 - (10~30℃), and hold at this temperature for 150~180min, using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece, wherein the total deformation per single pass is 35~40%, the bite rate is 0.5~0.8m / s, the feed rate is 2.5~3.5m / s, and the final forging temperature during the rolling process is maintained at ≥T β1 -100℃, after forging, air-cooled to room temperature, and its surface is ground. Sixth-stage two-phase zone hot rolling: The workpiece obtained after the fifth-stage two-phase zone hot rolling is heated to T. β1 - (20~40℃), and hold at this temperature for 150~180min, using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece, wherein the total deformation per single pass is 30~35%, the bite rate is 0.8~1.0m / s, the feed rate is 3.0~4.0m / s, and the final forging temperature during the rolling process is ≥T β1 -100℃, after forging, air-cooled to room temperature, and its surface is ground. Seventh-stage two-phase zone hot rolling: The workpiece obtained after the sixth-stage two-phase zone hot rolling is heated to T. β1 - (30~50℃), and hold at this temperature for 150~180min, using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece, wherein the total deformation per hot pass is 25~30%, the bite rate is 1.0m / s, the feed rate is 4.0m / s, and the final forging temperature during the rolling process is ≥T β1 -120℃, after forging, air-cooled to room temperature, and its surface is ground. S4. The workpiece obtained by hot rolling in the seven-phase region is subjected to solution treatment and aging treatment. S5. Perform an eighth hot rolling in the two-phase zone on the workpiece that has undergone the aging treatment. S6. The workpiece obtained by hot rolling in the second phase region after the eighth heat treatment is annealed to obtain a high-temperature titanium alloy containing Ta.

[0006] Further, in step S1, the mass ratio of Ti, Al, W, Si, C, Sn and Ta is (77.25~81.25)∶5.8∶2.5∶0.4∶0.05∶8∶(2~6). The specific preparation steps of the consumable electrode are as follows: Ti, Al, W, Si, C, Sn and Ta are mixed, and after thorough stirring, they are pressed into electrode blocks of Ф150mm×(200~300)mm. Four to six electrode blocks are then welded into a consumable electrode with dimensions of Ф150mm×(1100~1300)mm. The stirring rate is 20~30rpm, and the stirring time is 3~6h. The Al, W, Si and C elements can be added as single-element powders or intermediate alloys. The Sn element needs to be added as an Al-Sn alloy. The Ta element needs to be added as a single-element powder. The Ti element is added as 0-1 grade sponge titanium (complies with grade 0A in GB / T2524 standard, with a particle size of 0.84~12.6mm) powder. The C element is added in the form of carbon powder.

[0007] Beneficial effects: By introducing Sn as an Al-Sn master alloy, the uniform distribution of Sn in the titanium matrix is ​​effectively promoted, which is conducive to the formation of Ti-Al-Sn ordered phase compounds such as Ti3(Al,Sn) and Ti4(Al,Sn), significantly improving the phase transformation temperature and medium-to-high temperature microstructure stability of the alloy. Simultaneously, the addition of the refractory high-temperature element Ta (with a relatively large atomic mass, prone to precipitation and stratification causing compositional inhomogeneity) in the form of elemental powder, combined with a rationally controlled low-speed, long-time stirring process, avoids stratification and compositional segregation caused by Ta's high density, allowing it to achieve a dispersed distribution in the consumable electrode and fully exert its high-temperature solid solution strengthening effect. The synergistic effect of the above composition design and process control, while ensuring compositional uniformity and engineering feasibility, achieves a simultaneous improvement in the alloy's high-temperature strength, microstructure stability, and overall service performance.

[0008] Further, in step S2, the vacuum consumable arc melting is performed three times in a vacuum environment and a 99.99% argon atmosphere (volume concentration) to obtain a uniformly composed Ta-containing titanium alloy ingot; the vacuum degree of the vacuum environment is 0.15–0.20 Pa; the surface oxide layer of the Ta-containing titanium alloy ingot should be removed; the specific parameters of the three consumable arc meltings are as follows: First vacuum self-consuming arc melting: current 30-32kA, voltage 42-44V, speed 300-400mm / min; Second vacuum self-consuming arc melting: current 32-34kA, voltage 44-46V, speed 275-375mm / min; The third vacuum self-consuming arc melting process: current 34-36kA, voltage 46-48V, speed 250-350mm / min.

[0009] Beneficial effects: By performing multiple vacuum consumable arc melting processes under high vacuum (0.15-0.20 Pa) and high-purity argon protection conditions, and by progressively increasing the melting current and voltage while decreasing the melting speed, the heat input of the molten pool and the convection intensity of the liquid metal can be significantly enhanced. This allows the refractory high-density Ta element to be fully dissolved and diffused during the melting process, preventing Ta segregation and promoting its uniform solid solution in the titanium matrix. The multiple melting processes effectively reduce macroscopic segregation of the ingot and improve compositional uniformity. Combined with the post-melting treatment to remove the surface oxide layer, the adverse effects of impurity enrichment on the microstructure and properties can be further reduced, resulting in a Ta-containing high-temperature titanium alloy ingot with uniform microstructure, stable composition, and excellent high-temperature performance.

[0010] Further, in step S3, the ingot is sequentially subjected to two-stage forging in the single-phase region, two-stage hot deformation forging in the two-phase region, and three-stage hot rolling in the two-phase region, collectively referred to as the hot deformation process. The thickness of the titanium alloy plate can be increased by adding hot rolling stages according to the required plate thickness, and the process of adding stages is the same as the seventh stage of two-phase region hot rolling.

[0011] Beneficial effects: Addressing the low diffusion rate of the refractory high-temperature element Ta in a titanium matrix, this invention employs a high-temperature, multi-pass uniform hot deformation process by relatively increasing the forging temperature and the number of forging passes. This process continuously introduces structural defects such as high-density dislocations, subgrain boundaries, and dynamic recrystallization interfaces into the alloy, providing sufficient driving force and rapid diffusion channels for alloy element diffusion. This significantly promotes the uniform diffusion and redistribution of Ta and Sn elements in the matrix. Furthermore, the multiple hot deformation processes effectively break up the coarse as-cast structure, refine the grains, and homogenize the phase distribution, suppressing unstable microstructure evolution during high-temperature service. This facilitates the synergistic improvement of high-temperature solid solution strengthening, ordered phase strengthening, and microstructure stability, thereby enhancing the alloy's high-temperature strength, creep resistance, and long-term service reliability.

[0012] Further, in step S4, the specific steps of the solution treatment are as follows: heating the workpiece obtained after the seventh hot rolling in the two-phase region to T. β2 - (20~30℃), hold for 180~240min, and air-cool to room temperature. The specific steps of the aging treatment are as follows: heat the workpiece obtained after solution treatment to 700±10℃, hold for 180~240min, and air-cool to room temperature, wherein T β2 The temperature ranges from 1090 to 1130℃.

[0013] Beneficial effects: By heating the Ta-containing titanium alloy after hot deformation to a temperature below the β-phase transformation point T of the forging, β2Solution treatment at 20–30℃ with sufficient holding time allows for further uniform solution dissolution of alloying elements such as Ta and Sn while maintaining the stability of the α / β dual-phase microstructure, effectively avoiding the risk of grain coarsening caused by complete β-conversion. Furthermore, solution treatment at this temperature promotes recrystallization and regulates the dual-phase content, resulting in an optimal microstructure. Subsequent aging treatment at 700±10℃ facilitates the stable precipitation and regulation of the Ti-Al-Sn ordered phase and related strengthening structures, achieving a synergistic effect of ordered phase strengthening and matrix solid solution strengthening.

[0014] Further, in step S5, the specific operation steps of the eighth hot rolling in the two-phase region are as follows: heating the workpiece obtained after aging treatment to T β2 - (80~100℃), hold for 120~150min, employ a hot deformation process of "unidirectional rolling" on the workpiece using a rolling mill, wherein the total deformation per hot pass is 5~8%, the bite rate is 0.4~0.6m / s, the feed rate is 2.0~3.0m / s, and the final forging temperature during the rolling process is ≥T β2 After forging at -150℃, the material is air-cooled to room temperature and its surface is then ground.

[0015] Beneficial effects: Introducing a single-pass, small-deformation unidirectional hot rolling process within the low α+β two-phase temperature range allows for controlled hot deformation of the sheet metal without disrupting the existing stable phase structure. This effectively introduces appropriate dislocations and subgrain boundaries into the microstructure, achieving precise control over the microstructure. The increased dislocation density and subgrain refinement effect provide supplementary strengthening of the sheet metal. While maintaining a stable α / β phase ratio, it improves the yield strength and high-temperature load-bearing capacity of the sheet metal, achieving both strength enhancement and optimized microstructure stability.

[0016] Further, in step S6, the specific operation steps of the annealing treatment are as follows: heat the workpiece obtained by the eighth hot rolling in the two-phase region to 700±10℃ and hold it for 180~240min.

[0017] Beneficial effects: Effectively promotes the recovery and rearrangement of high-density dislocations and subgrain boundaries introduced by deformation, reduces residual stress inside the material, and stabilizes the microstructure and phase boundary structure. It also helps improve the material's plasticity and thermal stability.

[0018] This invention also provides a Ta-containing high-temperature titanium alloy prepared by the above-described method, comprising the following components by mass percentage: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 2.0-6.0%, with the balance being Ti and unavoidable impurities. Further, the Ta content includes, but is not limited to: 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8%, 4.0%, 4.2%, 4.4%, 4.6%, 4.8%, 5.0%, 5.2%, 5.4%, 5.6%, 5.8%, and 6.0%.

[0019] This invention, through precise control of the Ta element in the alloy (maintaining its mass percentage of 2.0–6.0%) and the synergistic effect of multi-stage hot deformation and heat treatment processes, effectively promotes the uniform solid solution of Ta and the formation of a stable strengthening phase. This results in a series of titanium alloys exhibiting high service strength while maintaining good plasticity under high-temperature operating conditions. Specifically: This invention achieves a comprehensive balance between material properties and manufacturing performance by rationally selecting and precisely controlling the types and contents of high-temperature strengthening elements, synergistically optimizing the phase composition, microstructure, and thermal stability of the alloy, while simultaneously considering engineering formability and adaptability to complex service environments. This is a fundamental principle in the design of high-temperature titanium alloys. Existing high-temperature titanium alloys typically improve the thermal stability of the α phase in the mid-to-high temperature range through α-stabilizing elements such as Al and Sn, and achieve high-temperature solid solution strengthening through refractory β-stabilizing elements such as Ta, W, and Mo, thereby enhancing the alloy's high-temperature strength and creep resistance.

[0020] Under precise compositional control, the Ti-Al-Sn ternary system can form ordered phase compounds represented by Ti3(Al,Sn) and Ti4(Al,Sn). This ordered structure significantly increases the phase transformation temperature of the alloy, providing a material basis for extending the service temperature range of titanium alloys. Simultaneously, the formation of the ordered phase and the favorable thermodynamic combination between Ti-Al-Sn atoms enable the alloy's solid solution structure and microstructure to exhibit good thermal stability under medium- and high-temperature conditions, which helps to suppress microstructure coarsening and phase instability evolution.

[0021] Building upon this foundation, further enhancing the matrix strength and achieving synergy between ordered phase strengthening and matrix strengthening is key to obtaining excellent high-temperature comprehensive performance. The refractory high-temperature element Ta is one of the effective ways to improve the high-temperature service capability of alloys. Ta possesses characteristics such as a high melting point, low atomic diffusion rate, and high high-temperature solid solution strengthening efficiency. It can maintain a stable solid solution state in a titanium matrix over a wide temperature range, thereby significantly improving the service temperature and high-temperature strength of the alloy. As a typical β-stabilizing element, the addition of Ta can effectively regulate the α / β phase ratio in the alloy, suppress microstructure coarsening and unstable phase evolution behavior under high-temperature conditions, improve the stability of the microstructure during long-term high-temperature service, and help maintain the overall plasticity and fracture toughness of the alloy while ensuring high-temperature strength.

[0022] This invention also provides an application of a Ta-containing high-temperature titanium alloy in the manufacture of high-temperature components for aerospace engines.

[0023] Compared with the prior art, the present invention has the following advantages and technical effects: (1) This invention precisely controls the Ti-Al-Sn ratio through uniform hot deformation and setting solid solution parameters, introducing equiaxed structures of Ti3(Al,Sn) and Ti4(Al,Sn) ordered structures, and promoting their uniform distribution in the matrix with fine size. At the same time, the solid solution strengthening effect of the higher Sn content in the matrix significantly improves the high-temperature strength of the alloy. More importantly, it obtains a high phase transformation temperature titanium alloy with a significantly improved β phase transformation temperature, effectively breaking through the design limitations of existing high-temperature titanium alloys in terms of phase transformation temperature and microstructure stability.

[0024] (2) This invention introduces Ta, which has a large atomic radius and low diffusion rate, to dissolve in the titanium alloy matrix and significantly introduce lattice distortion, thereby forming a stable local stress field in the matrix, effectively hindering dislocation movement and achieving a significant solid solution strengthening effect. Simultaneously, Ta has a high melting point and excellent thermal stability, effectively suppressing dislocation thermal activation and microstructure softening under high-temperature service conditions, playing a crucial role in maintaining the high-temperature strength of the alloy. Furthermore, as a β-phase stabilizing element in titanium alloys, Ta is beneficial for controlling the β-phase volume fraction and improving the α / β phase interface bonding state, playing a key role in enhancing phase boundary stability.

[0025] (3) The Ta and Sn atoms introduced in this invention both have significant solid solution strengthening effects. By matching multiple hot deformation and heat treatment processes, a high-temperature stable ordered phase rich in Sn elements is formed in the equiaxed structure, which effectively improves the phase transformation temperature and high-temperature structural stability of the alloy. At the same time, in the β structure, the initial β crystal of Ta elements is solidly dissolved and plays a stabilizing and high-temperature strengthening role of the β phase, inhibiting high-temperature softening and structural coarsening, thereby achieving synergistic strengthening of the equiaxed α ordered phase and the β matrix, significantly improving the comprehensive mechanical properties of the alloy under medium and high temperature conditions. The effect characteristics of Ta-Sn elements on the α and β phases in titanium alloys synergistically improve the high-temperature strength of the equiaxed structure and the matrix, make up for the short-plate effect, and improve the overall high-temperature stability of the alloy. Attached Figure Description

[0026] The accompanying drawings, which form part of this invention, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an undue limitation of the invention. In the drawings: Figure 1 Metallographic image of the high-temperature titanium alloy obtained in Example 1; Figure 2 Metallographic image of the high-temperature titanium alloy obtained in Example 2; Figure 3 Metallographic image of the high-temperature titanium alloy obtained in Example 3; Figure 4 Metallographic image of the high-temperature titanium alloy prepared in Comparative Example 1. Figure 5 Metallographic image of the high-temperature titanium alloy prepared in Comparative Example 2; Figure 6 Metallographic image of the high-temperature titanium alloy prepared in Comparative Example 3; Figure 7 Metallographic image of the high-temperature titanium alloy prepared in Comparative Example 4. Figure 8 Metallographic image of the high-temperature titanium alloy prepared in Comparative Example 5. Figure 9 The image shows the metallographic structure of the high-temperature titanium alloy prepared in Comparative Example 6. Detailed Implementation

[0027] Various exemplary embodiments of the present invention will now be described in detail. This detailed description should not be considered as a limitation of the present invention, but rather as a more detailed description of certain aspects, features, and embodiments of the present invention.

[0028] It should be understood that the terminology used in this invention is merely for describing particular embodiments and is not intended to limit the invention. Furthermore, with respect to numerical ranges in this invention, it should be understood that each intermediate value between the upper and lower limits of the range is also specifically disclosed. Every smaller range between any stated value or intermediate value within a stated range, and any other stated value or intermediate value within said range, is also included in this invention. The upper and lower limits of these smaller ranges may be independently included or excluded from the range.

[0029] Unless otherwise stated, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. While only preferred methods and materials have been described herein, any methods and materials similar or equivalent to those described herein may be used in the implementation or testing of this invention. All references to this specification are incorporated by way of citation to disclose and describe methods and / or materials associated with those references. In the event of any conflict with any incorporated reference, the content of this specification shall prevail.

[0030] Various modifications and variations can be made to the specific embodiments described in this specification without departing from the scope or spirit of the invention, as will be apparent to those skilled in the art. Other embodiments derived from this specification will also be apparent to those skilled in the art. This specification and embodiments are merely exemplary.

[0031] The terms “include,” “including,” “have,” “contain,” etc., used in this article are all open-ended terms, meaning that they include but are not limited to.

[0032] This invention provides a method for preparing a Ta-containing high-temperature titanium alloy, comprising the following steps: S1. Preparation of consumable electrode: The raw materials Ti, Al, W, Si, C, Sn and Ta are mixed in proportion, pressed into electrode blocks, and welded into consumable electrodes. S2, Vacuum self-consuming arc melting: Vacuum self-consuming arc melting is performed on the self-consuming electrode to obtain an ingot; S3. Hot Deformation Process: The ingot is sequentially subjected to two-stage forging in the single-phase region, two-stage hot deformation forging in the two-phase region, and three-stage hot rolling in the two-phase region, including: First-stage single-phase forging: heating the ingot to T β1 (e.g., T) β1 =1020℃, 1040℃ or 1060℃) + (120~150℃, "+" indicates a temperature higher than T) β1The ingot is forged at a temperature of 120-150℃ (e.g., 1140℃, 1175℃, or 1210℃) and held at this temperature for 120-150 minutes (e.g., 120 minutes, 135 minutes, or 150 minutes). A high-speed forging machine is used to perform a "one-upset-one-drawing" forging process. During the upsetting stage, the compressive deformation is 50-60% (e.g., 50%, 55%, or 60%), with a corresponding deformation rate of 50-60 mm / min (e.g., 50 mm / min, 55 mm / min, or 60 mm / min). During the drawing stage, the tensile deformation is 45-55% (e.g., 45%, 50%, or 55%), with a corresponding deformation rate of 30-40 mm / min (e.g., 30 mm / min, 35 mm / min, or 40 mm / min). The final forging temperature during the forging process is maintained at ≥T. β1 After forging, the temperature is increased by 20℃ (e.g., 1040℃, 1060℃ or 1080℃), then cooled to room temperature by air cooling and the surface is ground. Second-stage single-phase forging: The forging obtained from the first-stage single-phase forging is heated to T. β1 + (80~100℃) (e.g., 1100℃, 1130℃, or 1160℃), and hold at this temperature for 120~150min (e.g., 120min, 135min, or 150min). Use a high-speed forging machine to perform a "one-upset-one-drawing" forging process on the ingot. During the upsetting stage, the compressive deformation is 45~55% (e.g., 45%, 50%, or 55%), corresponding to a deformation rate of 45~55mm / min (e.g., 45mm / min, 50mm / min, or 55mm / min). During the drawing stage, the tensile deformation is 40~50% (e.g., 40%, 45%, or 50%), corresponding to a deformation rate of 25~35mm / min (e.g., 25mm / min, 30mm / min, or 35mm / min). The final forging temperature during the forging process is maintained at ≥T. β1 After forging, the temperature is increased by 20℃ (e.g., 1040℃, 1060℃ or 1080℃), then cooled to room temperature by air cooling and the surface is ground. Third-stage two-phase zone hot deformation forging: The forging blank obtained from the second-stage single-phase zone forging is heated to T. β1 - (20~40℃, "-" indicates temperature higher than T) β1The workpiece is subjected to a "drawing" forging process using a high-speed forging mill. The temperature is set 20–40°C lower (e.g., 1000°C, 1010°C, or 1020°C) and held at this temperature for 150–180 minutes (e.g., 150 minutes, 165 minutes, or 180 minutes). During the drawing stage, the tensile deformation is 40–50% (e.g., 40%, 45%, or 50%), with a corresponding deformation rate of 30–35 mm / min (e.g., 30 mm / min, 32 mm / min, or 35 mm / min). The single feed rate is 200–220 mm (e.g., 200 mm, 210 mm, or 220 mm), and the high-speed forging mill frequency is 3 seconds per pass. The final forging temperature during the forging process is maintained at ≥T. β1 After forging, the temperature is reduced to -100℃ (e.g., 920℃, 940℃ or 960℃), then cooled to room temperature by air cooling, and the surface is ground. Fourth-stage two-phase zone hot deformation forging: The forging billet obtained after the third-stage two-phase zone hot deformation forging is heated to T. β1 - (30~50℃) (e.g., 990℃, 1000℃, or 1010℃), and hold at this temperature for 150~180min (e.g., 150min, 165min, or 180min), using a high-speed forging mill to perform a "drawing" forging process on the workpiece. During the drawing stage, the tensile deformation is 35~40% (e.g., 35%, 37%, or 40%), with a corresponding deformation rate of 25~30mm / min (e.g., 25mm / min, 27mm / min, or 30mm / min), a single feed rate of 200~220mm (e.g., 200mm, 210mm, or 220mm), and a high-speed forging mill frequency of 3s / cycle; the final forging temperature during the forging process is ≥T. β1 -120℃ (such as 900℃, 920℃ or 940℃), after forging, air-cool to room temperature, and then grind the surface. Fifth-stage two-phase zone hot rolling: The forging billet obtained from the fourth-stage two-phase zone hot deformation forging is heated to T. β1 - (10~30℃) (e.g., 1010℃, 1020℃, or 1030℃), and hold at this temperature for 150~180min (e.g., 150min, 165min, or 180min), using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece, wherein the total deformation per hot pass is 35~40% (e.g., 35%, 37%, or 40%), the bite rate is 0.5~0.8m / s (e.g., 0.5m / s, 0.65m / s, or 0.8m / s), the feed rate is 2.5~3.5m / s (e.g., 2.5m / s, 3.0m / s, or 3.5m / s), and the final forging temperature during the rolling process is maintained at ≥T β1 After forging, the temperature is reduced to -100℃ (e.g., 920℃, 940℃ or 960℃), then cooled to room temperature by air cooling, and the surface is ground. Sixth-stage two-phase zone hot rolling: The workpiece obtained after the fifth-stage two-phase zone hot rolling is heated to T. β1 - (20~40℃) (e.g., 1000℃, 1010℃, or 1020℃), and hold at this temperature for 150~180min (e.g., 150min, 165min, or 180min), using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece. The total deformation per pass is 30~35% (e.g., 30%, 32%, or 35%), the bite rate is 0.8~1.0m / s (e.g., 0.8m / s, 0.9m / s, or 1.0m / s), the feed rate is 3.0~4.0m / s (e.g., 3.0m / s, 3.5m / s, or 4.0m / s), and the final forging temperature during the rolling process is ≥T. β1 After forging, the temperature is reduced to -100℃ (e.g., 920℃, 940℃ or 960℃), then cooled to room temperature by air cooling, and the surface is ground. Seventh-stage two-phase zone hot rolling: The workpiece obtained after the sixth-stage two-phase zone hot rolling is heated to T. β1 - (30~50℃) (e.g., 990℃, 1000℃ or 1010℃), and hold at this temperature for 150~180min (e.g., 150min, 165min or 180min), using a rolling mill to perform a "unidirectional rolling" hot deformation process on the workpiece, wherein the total deformation per hot pass is 25~30% (e.g., 25%, 27% or 30%), the bite rate is 1.0m / s, the feed rate is 4.0m / s, and the final forging temperature during the rolling process is ≥T β1 -120℃ (such as 900℃, 920℃ or 940℃), after forging, air-cool to room temperature, and then grind the surface. S4. The workpiece obtained after the seventh hot rolling in the two-phase zone is subjected to solution treatment and aging treatment. S5. Perform the eighth hot rolling in the two-phase zone on the workpiece that has undergone aging treatment. S6. Anneal the workpiece obtained after the eighth hot rolling in the two-phase region to obtain a high-temperature titanium alloy containing Ta.

[0033] In some optional embodiments of the present invention, in step S1, the mass ratio of Ti, Al, W, Si, C, Sn and Ta is (77.25~81.25)∶5.8∶2.5∶0.4∶0.05∶8∶(2~6), such as 81.25∶5.8∶2.5∶0.4∶0.05∶8∶2, 79.25∶5.8∶2.5∶0.4∶0.05∶8∶4 or 77.25∶5.8∶2.5∶0.4∶0.05∶8∶6. The specific preparation steps of the consumable electrode are as follows: Ti, Al, W, Si, C, Sn and Ta are mixed, and after thorough stirring, they are pressed into electrode blocks of Ф150mm×(200~300)mm (such as Ф150mm×200mm, Ф150mm×250mm or Ф150mm×300mm). Four to six electrode blocks are then welded together to form a consumable electrode with dimensions of Ф150mm×(1100~1300)mm (such as Ф150mm×1200mm, Ф150mm×300mm). The stirring size is 1250mm or Ф150mm×1200mm; the stirring speed is 20-30 rpm (e.g., 20 rpm, 25 rpm or 30 rpm), and the stirring time is 3-6 h (e.g., 3 h, 4.5 h or 6 h); Al, W, and Si elements can be added as single-element powders or master alloys; Sn element needs to be added as an Al-Sn alloy; Ta element needs to be added as single-element powders; Ti element is added as 0-1 grade sponge titanium (complies with grade 0A in GB / T 2524 standard, particle size of 0.84-12.6mm) powder; C element is added in the form of carbon powder.

[0034] In some optional embodiments of the present invention, in step S2, the vacuum consumable arc melting is performed three times in a vacuum environment and a 99.99% argon atmosphere (volume concentration) to obtain a uniformly composed Ta-containing titanium alloy ingot; the vacuum degree of the vacuum environment is 0.15-0.20 Pa (e.g., 0.15 Pa); the surface oxide layer of the Ta-containing titanium alloy ingot should be removed; the specific parameters of the three consumable arc meltings are as follows: First vacuum self-consuming arc melting: current 30-32kA (e.g. 30kA, 31kA or 32kA), voltage 42-44V (e.g. 42V, 43V or 44V), speed 300-400mm / min (e.g. 300mm / min, 350mm / min or 400mm / min). Second vacuum self-consuming arc melting: current is 32-34kA (e.g., 32kA, 33kA or 34kV), voltage is 44-46V (e.g., 44V, 45V or 46V), speed is 275-375mm / min (e.g., 275mm / min, 325mm / min or 375mm / min); The third vacuum self-consuming arc melting process: the current is 34-36kA (e.g., 34kA, 35kA or 36kA), the voltage is 46-48V (e.g., 46V, 47V or 48V), and the speed is 250-350mm / min (e.g., 250mm / min, 300mm / min or 350mm / min).

[0035] In some optional embodiments of the present invention, in step S3, the thickness of the titanium alloy plate can be increased by adding hot rolling passes according to the required plate thickness, and the process of the added passes is the same as that of the seventh pass two-phase zone hot rolling.

[0036] In some optional embodiments of the present invention, the specific operation steps of solution treatment in step S4 are as follows: heating the workpiece obtained by the seventh hot rolling in the two-phase region to T β2 - (20~30℃) (e.g., T) β2 If the temperature is 1090℃, 1110℃, or 1130℃, then heat the workpiece to 1070℃, 1085℃, or 1100℃, hold for 180–240 min (e.g., 180 min, 210 min, or 240 min), and then air-cool to room temperature. The specific steps for aging treatment are as follows: Heat the workpiece obtained after solution treatment to 700±10℃ (e.g., 690℃, 700℃, or 710℃), with a heating rate of 15℃ / min, hold for 180–240 min (e.g., 180 min, 210 min, or 240 min), and then air-cool to room temperature.

[0037] In some optional embodiments of the present invention, the specific operation steps of the eighth hot rolling in the two-phase region in step S5 are as follows: heating the workpiece obtained after aging treatment to T β2 - (80~100℃) (e.g., 1010℃, 1020℃ or 1030℃), hold for 120~150min (e.g., 120min, 135min or 150min), employ a hot deformation process of "unidirectional rolling" on the workpiece using a rolling mill, wherein the total deformation per hot pass is 5~8% (5%, 6% or 8%), the bite rate is 0.4~0.6m / s (0.4m / s, 0.5m / s or 0.6m / s), the feed rate is 2.0~3.0m / s (2.0m / s, 2.5m / s or 3.0m / s), and the final forging temperature during the rolling process is ≥T β2 After forging, the temperature is reduced to -150℃ (e.g., 940℃, 960℃ or 980℃), then cooled to room temperature by air cooling, and the surface is ground.

[0038] In some optional embodiments of the present invention, the specific operation steps of the annealing process in step S6 are as follows: heating the workpiece obtained by the eighth hot rolling in the two-phase zone to 700±10℃ (e.g., 690℃, 700℃ or 710℃) and holding it for 180 to 240 min (e.g., 180 min, 210 min or 240 min).

[0039] The Ta high-temperature titanium alloy prepared by the above method contains the following components by mass percentage: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 2.0-6.0%, with the balance being Ti and unavoidable impurities. Preferably, the Ta content includes, but is not limited to: 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8%, 4.0%, 4.2%, 4.4%, 4.6%, 4.8%, 5.0%, 5.2%, 5.4%, 5.6%, 5.8%, and 6.0%.

[0040] The aforementioned Ta high-temperature titanium alloy can be used in the manufacture of high-temperature components for aerospace engines.

[0041] Unless otherwise specified, "room temperature" in this invention refers to 25±2℃.

[0042] All raw materials used in this invention were purchased from the market.

[0043] The technical solution of the present invention will be further illustrated by the following embodiments.

[0044] Example 1 A method for preparing a Ta-containing high-temperature titanium alloy includes the following steps: (a) Ingredients Grade 0-1 sponge titanium was selected as the Ti raw material (complying with grade 0A in GB / T 2524 standard, with a particle size of 0.84-12.6mm); alloying elements Al, W, and Si were added as single-element powders and master alloys; C was added in the form of carbon powder; Sn was added as an Al-Sn master alloy; and Ta was added as a single-element powder. The final Ta-containing titanium alloy powder was composed of the following mass percentages: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 2.0%, with the balance being Ti and unavoidable impurities. (II) Preparation of consumable electrode The ingredients in step (1) are mixed evenly using a mixer at a speed of 30 rpm for 3 hours. After thorough mixing, the mixture is pressed into electrode blocks of Ф150mm×200mm and the six electrode blocks are welded together to form a consumable electrode with a size of Ф150mm×1200mm. (III) Vacuum self-consuming arc melting The consumable electrode prepared in step (II) was placed in a vacuum environment with a vacuum degree of 0.15 Pa and an atmosphere of 99.99% argon (volume concentration) for three consumable arc melting processes to obtain a uniformly composed Ta-containing titanium alloy ingot, and the surface oxide layer was removed. The parameters for the first vacuum arc melting process were: current 30kA, voltage 42V, and speed 300mm / min; the parameters for the second vacuum arc melting process were: current 32kA, voltage 44V, and speed 275mm / min; and the parameters for the third vacuum arc melting process were: current 34kA, voltage 46V, and speed 250mm / min. (iv) Hot deformation process The β-phase transformation temperature T of titanium alloy ingots was determined by metallographic method. β1 Measurements were performed to obtain the ingot T under this ratio. β1 =1020℃; The Ta-containing titanium alloy ingot is subjected to two-stage forging in the single-phase region, two-stage hot deformation forging in the two-phase region, and three-stage hot rolling in the two-phase region. The specific process parameters are as follows: First-stage single-phase forging: The ingot is heated to 1140℃ and held at this temperature for 120 minutes. A high-speed forging machine is used to carry out a "one-upset-one-drawing" forging process on the ingot. In the upsetting stage, the compression deformation is 50%, and the corresponding deformation rate is 50 mm / min. In the drawing stage, the tensile deformation is 45%, and the corresponding deformation rate is 30 mm / min. The final forging temperature is maintained at ≥1040℃ during the forging process. After forging, the ingot is cooled to room temperature by air cooling and the surface is ground. Second-stage single-phase forging: The forging billet obtained from the first-stage single-phase forging is heated to 1100℃ and held at this temperature for 120 minutes. The workpiece is then subjected to a "one-upset-one-drawing" forging process using a high-speed forging machine. In the upsetting stage, the compressive deformation is 45%, corresponding to a deformation rate of 45 mm / min; in the drawing stage, the tensile deformation is 40%, corresponding to a deformation rate of 25 mm / min. The final forging temperature is maintained at ≥1040℃ during the forging process. After forging, the workpiece is air-cooled to room temperature and its surface is ground. The third stage of two-phase zone hot deformation forging: The forging billet obtained from the second stage of single-phase zone forging is heated to 1000℃ and held at this temperature for 150 min. The workpiece is then subjected to a "drawing" forging process using a high-speed forging machine. During the drawing stage, the tensile deformation is 40%, the corresponding deformation rate is 30 mm / min, the single feed is 200 mm, and the high-speed forging machine frequency is 3 s / time. The final forging temperature is maintained at ≥920℃ during the forging process. After forging, the workpiece is air-cooled to room temperature and its surface is ground. Fourth-stage two-phase zone hot deformation forging: The forging billet obtained from the third-stage two-phase zone hot deformation forging is heated to 990℃ and held at this temperature for 150 min. The workpiece is then subjected to a "drawing" forging process using a high-speed forging machine. During the drawing stage, the tensile deformation is 35%, the corresponding deformation rate is 25 mm / min, the single feed is 200 mm, and the high-speed forging machine frequency is 3 s / cycle. The final forging temperature during the forging process is ≥900℃. After forging, the workpiece is air-cooled to room temperature and its surface is ground. Fifth-stage two-phase zone hot rolling: The forging billet obtained from the fourth-stage two-phase zone hot deformation forging is heated to 1010℃ and held at this temperature for 150 minutes. The workpiece is then subjected to a "unidirectional rolling" hot deformation process using a rolling mill. The total deformation in a single-stage process is 35%, the bite rate is 0.5 m / s, the feed rate is 2.5 m / s, and the final forging temperature during the rolling process is maintained at ≥920℃. After forging, the workpiece is cooled to room temperature by air cooling and its surface is then ground. Sixth hot rolling in the two-phase zone: The workpiece obtained from the fifth hot rolling in the two-phase zone is heated to 1000℃ and held at this temperature for 150 minutes. The workpiece is then subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 30%, the bite rate is 0.8 m / s, the feed rate is 3.0 m / s, and the final forging temperature during the rolling process is ≥920℃. After forging, the workpiece is cooled to room temperature by air cooling and its surface is then ground. Seventh hot rolling in the two-phase zone: The workpiece obtained from the sixth hot rolling in the two-phase zone is heated to 990℃ and held at this temperature for 150 minutes. The workpiece is then subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 25%, the bite rate is 1.0 m / s, the feed rate is 4.0 m / s, and the final forging temperature during the rolling process is ≥900℃. After forging, the workpiece is cooled to room temperature by air cooling and its surface is then ground. (v) Heat treatment The β-phase transformation temperature T of the heat-treated Ta-containing titanium alloy workpiece was determined by metallographic method. β2 Measurements were performed to obtain workpiece T under this mix ratio. β2 =1090℃; The titanium alloy workpiece containing Ta, after undergoing hot deformation, is heated to 1070℃ and held for 180 min. The furnace temperature is then raised to 700℃, and the workpiece is placed in the furnace and heated to 1070℃ at a rate of 15℃ / min. After solution treatment, it is cooled to room temperature by air cooling. Subsequently, the solution-treated workpiece is heated to 700℃ and held for 180 min for aging treatment, and then air-cooled to room temperature. (vi) Secondary thermal deformation The heat-treated sheet metal is subjected to the eighth hot rolling in the two-phase region: the heat-treated titanium alloy workpiece containing Ta is heated to 1010℃ and held for 120 min. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 5%, the bite rate is 0.4 m / s, the feed rate is 2.0 m / s, and the final forging temperature during the rolling process is kept not lower than 940℃. After forging, the workpiece is cooled by air and its surface is ground. (vii) Annealing The titanium alloy workpiece containing Ta, which has undergone a secondary hot deformation process, is heated to 700℃ and held for 180 minutes to obtain a high-temperature titanium alloy containing Ta.

[0045] Performance Test 1 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Example 1. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 1.

[0046] Table 1. Tensile property test results of the high-temperature titanium alloy in Example 1

[0047] Example 2 A method for preparing a Ta-containing high-temperature titanium alloy includes the following steps: (a) Ingredients Grade 0-1 sponge titanium was selected as the Ti raw material (complying with grade 0A in GB / T 2524 standard, with a particle size of 0.84-12.6mm). Alloying elements Al, W, and Si were added as single-element powders and master alloys; C was added as carbon powder; Sn was added as an Al-Sn master alloy; and Ta was added as single-element powder. The final Ta-containing titanium alloy powder, by mass percentage, was: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 4.0%, with the balance being Ti and unavoidable impurities.

[0048] (II) Preparation of consumable electrode The ingredients were mixed evenly using a mixer at a speed of 25 rpm for 4.5 hours. After thorough mixing, the mixture was pressed into electrode blocks of Ф150mm×250mm and five electrode blocks were welded together to form a consumable electrode with a size of Ф150mm×1250mm. (III) Vacuum self-consuming arc melting The consumable electrode was placed in a vacuum environment with a vacuum degree of 0.20 Pa and an atmosphere of 99.99% argon (volume concentration) for three consumable arc melting processes to obtain a uniformly composed Ta-containing titanium alloy ingot, and the surface oxide layer was removed. The parameters for the first vacuum arc melting process were: current 31kA, voltage 43V, and speed 350mm / min; the parameters for the second vacuum arc melting process were: current 33kA, voltage 45V, and speed 325mm / min; and the parameters for the third vacuum arc melting process were: current 35kA, voltage 47V, and speed 300mm / min. (iv) Heat deformation The β-phase transformation temperature T of titanium alloy ingots was determined by metallographic method. β1 Measurements were performed to obtain the ingot T under this ratio. β1 =1040℃; The Ta-containing titanium alloy ingot undergoes two hot forging processes in the single-phase region, two hot deformation forging processes in the two-phase region, and three hot rolling processes. The specific process parameters are as follows: First-stage single-phase forging: The titanium alloy ingot containing Ta is heated to 1175℃ and held at this temperature for 135 min. Then, a high-speed forging machine is used to perform a "one-upset-one-drawing" forging process. During the upsetting stage, the compressive deformation is controlled at 55%, corresponding to a deformation rate of 55 mm / min; during the drawing stage, the tensile deformation is controlled at 50%, with a deformation rate of 35 mm / min. The final forging temperature is maintained at no less than 1060℃. After forging, the workpiece is air-cooled and its surface is ground. Second-stage single-phase forging: The titanium alloy workpiece containing Ta, after the first-stage forging, is heated to 1130℃ and held at this temperature for 135 minutes. Then, a high-speed forging machine is used to perform a "one-upset-one-drawing" forging process. During the upsetting stage, the compressive deformation is controlled at 50%, corresponding to a deformation rate of 45 mm / min; during the drawing stage, the tensile deformation is controlled at 45%, with a deformation rate of 30 mm / min. The final forging temperature is maintained at no less than 1060℃. After forging, the workpiece is air-cooled and its surface is ground. The third two-phase zone hot deformation forging: The titanium alloy workpiece containing Ta that has been forged in the second single-phase zone is heated to 1010℃ and held at this temperature for 165 min. Then, the workpiece is subjected to a "drawing" forging process using a high-speed forging machine. The drawing stretching deformation is controlled at 45%, the deformation rate is 32 mm / min, the single feed is 210 mm, the high-speed forging machine frequency is 3 s / time, and the final forging temperature during the forging process is kept not lower than 940℃. After forging, the workpiece is cooled by air and its surface is ground. Fourth-stage two-phase zone hot deformation forging: The titanium alloy workpiece containing Ta, which has been forged in the third-stage two-phase zone, is heated to 1000℃ and held at this temperature for 165 minutes. Then, the workpiece is subjected to a "drawing" forging process using a high-speed forging machine. The drawing stretching deformation is controlled at 37%, the deformation rate is 27 mm / min, the single feed is 210 mm, the high-speed forging machine frequency is 3 seconds / time, and the final forging temperature during the forging process is kept not lower than 920℃. After forging, the workpiece is cooled by air and its surface is ground. Fifth-stage two-phase zone hot rolling: The titanium alloy workpiece containing Ta, after being forged in the fourth stage of the two-phase zone, is heated to 1020℃ and held at this temperature for 165 minutes. Subsequently, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single stage is 37%, the bite rate is 0.65 m / s, the feed rate is 3.0 m / s, and the final forging temperature during the rolling process is maintained at no less than 940℃. After forging, the workpiece is air-cooled and its surface is ground. Sixth hot rolling in the two-phase zone: The titanium alloy workpiece containing Ta that has been hot rolled in the five-phase zone is heated to 1010℃ and held at this temperature for 165 min. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 32%, the bite rate is 0.9 m / s, the feed rate is 3.5 m / s, and the final forging temperature during the rolling process is kept not lower than 940℃. After forging, the workpiece is cooled by air and its surface is ground. Seventh hot rolling in the two-phase zone: The titanium alloy workpiece containing Ta, after the sixth hot rolling in the two-phase zone, is heated to 1000℃ and held at this temperature for 165 minutes. Subsequently, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 27%, the bite rate is 1.0 m / s, the feed rate is 4.0 m / s, and the final forging temperature during the rolling process is maintained at no less than 920℃. After forging, the workpiece is air-cooled and its surface is ground. (v) Heat treatment The β-phase transformation temperature T of the heat-treated Ta-containing titanium alloy workpiece was determined by metallographic method. β2 Measurements were performed to obtain workpiece T under this mix ratio. β2 =1110℃; The titanium alloy workpiece containing Ta, after undergoing hot deformation, is heated to 1085℃ and held for 210 min. The furnace temperature is then raised to 690℃, and the workpiece is placed in the furnace and heated to 1085℃ at a rate of 15℃ / min. After solution treatment, it is cooled to room temperature by air cooling. The solution-treated workpiece is then heated to 690℃ and held for 180 min for aging treatment, and then air-cooled to room temperature. (vi) Secondary thermal deformation The heat-treated sheet metal was subjected to an eighth hot rolling in the two-phase region: the Ta-containing titanium alloy workpiece was heated to 1020℃ and held for 135 minutes. Subsequently, the workpiece was subjected to a hot deformation process of "unidirectional rolling" using a rolling mill, with a total deformation of 6% per hot rolling pass, a bite rate of 0.5 m / s, a feed rate of 2.5 m / s, and a final forging temperature of not less than 960℃ during the rolling process. After forging, the workpiece was air-cooled and its surface was ground. (vii) Annealing The titanium alloy workpiece containing Ta, after undergoing a secondary hot deformation process, is heated to 690℃ and held for 180 minutes.

[0049] Performance Test 2 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Example 2. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Room temperature test method" and GB / T 4338-2006 "Metallic materials - High temperature tensile test method". The test was conducted no less than three times at each temperature. The results are shown in Table 2.

[0050] Table 2. Tensile property test results of the high-temperature titanium alloy in Example 2.

[0051] Example 3 A method for preparing a Ta-containing high-temperature titanium alloy includes the following steps: (a) Ingredients Grade 0-1 sponge titanium was selected as the Ti raw material (compliant with grade 0A in GB / T 2524 standard, particle size 0.84-12.6mm); alloying elements Al, W, and Si were added as single-element powders and master alloys; C was added in the form of carbon powder; Sn was added as an Al-Sn master alloy; and Ta was added as a single-element powder. The final Ta-containing titanium alloy powder was composed of the following mass percentages: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 6.0%, with the balance being Ti and unavoidable impurities. (II) Preparation of consumable electrode The ingredients were mixed evenly using a mixer at a speed of 20 rpm for 6 hours. After thorough mixing, the mixture was pressed into electrode blocks of Ф150mm×300mm and four electrode blocks were welded together to form a consumable electrode with a size of Ф150mm×1200mm. (III) Vacuum self-consuming arc melting The consumable electrode was placed in a vacuum environment with a vacuum degree of 0.15 Pa and an atmosphere of 99.99% argon (volume concentration) for three consumable arc melting processes to obtain a uniformly composed Ta-containing titanium alloy ingot, and the surface oxide layer was removed. The parameters for the first vacuum arc melting process were: current 32kA, voltage 44V, and speed 400mm / min; the parameters for the second vacuum arc melting process were: current 34kA, voltage 46V, and speed 375mm / min; and the parameters for the third vacuum arc melting process were: current 36kA, voltage 48V, and speed 350mm / min. (iv) Heat deformation The β-phase transformation temperature T of titanium alloy ingots was determined by metallographic method. βMeasurements were performed to obtain the ingot T under this ratio. β1 =1060℃, The Ta-containing titanium alloy ingot undergoes two hot forging processes in the single-phase region, two hot deformation forging processes in the two-phase region, and three hot rolling processes. Additionally, additional hot rolling processes can be added depending on the required plate thickness. The processes for these additional processes are the same as the final hot rolling process in the two-phase region. Specific process parameters are as follows: First-stage single-phase forging: The titanium alloy ingot containing Ta is heated to 1210℃ and held at this temperature for 150 min. Then, the ingot is subjected to a "one-upset-one-drawing" forging process using a high-speed forging equipment. During the upsetting stage, the compressive deformation is controlled at 60%, with a corresponding deformation rate of 60 mm / min. During the drawing stage, the tensile deformation is controlled at 55%, with a deformation rate of 40 mm / min. The final forging temperature is maintained at no less than 1080℃. After forging, the workpiece is air-cooled and its surface is ground. Second-stage single-phase forging: The titanium alloy workpiece containing Ta, after the first-stage forging, is heated to 1160℃ and held at this temperature for 150 min. Then, a high-speed forging equipment is used to carry out a "one-upset-one-drawing" forging process. In the upsetting stage, the compressive deformation is controlled at 55%, and the corresponding deformation rate is 55 mm / min. In the drawing stage, the tensile deformation is controlled at 50%, and the deformation rate is 35 mm / min. The final forging temperature during the forging process is kept not lower than 1080℃. After forging, the workpiece is air-cooled and its surface is ground. The third two-phase zone hot deformation forging: The titanium alloy workpiece containing Ta that has been forged in the second single-phase zone is heated to 1020℃ and held at this temperature for 180min. Then, the workpiece is subjected to a "drawing" forging process using a high-speed forging machine. The drawing stretching deformation is controlled at 50%, the deformation rate is 35mm / min, the single feed is 220mm, the high-speed forging machine frequency is 3s / time, and the final forging temperature during the forging process is kept not lower than 960℃. After forging, the workpiece is cooled by air and its surface is ground. Fourth-stage two-phase zone hot deformation forging: The titanium alloy workpiece containing Ta, which has been forged in the third-stage two-phase zone, is heated to 1010℃ and held at this temperature for 180 min. Then, the workpiece is subjected to a "drawing" forging process using a high-speed forging machine. The drawing stretching deformation is controlled at 45%, the deformation rate is 30 mm / min, the single feed is 220 mm, the high-speed forging machine frequency is 3 s / time, and the final forging temperature during the forging process is kept not lower than 940℃. After forging, the workpiece is cooled by air and its surface is ground. Fifth-stage two-phase zone hot rolling: The titanium alloy workpiece containing Ta, after being forged in the fourth-stage two-phase zone, is heated to 1030℃ and held at this temperature for 180 minutes. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single-stage process is 40%, the bite rate is 0.8 m / s, and the feed rate is 3.5 m / s. The final forging temperature during the rolling process is kept not lower than 960℃. After forging, the workpiece is cooled by air and its surface is ground. Sixth hot rolling in the two-phase zone: The titanium alloy workpiece containing Ta that has been hot rolled in the five-phase zone is heated to 1020℃ and held at this temperature for 180 min. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 35%, the bite rate is 1.0 m / s, the feed rate is 4.0 m / s, and the final forging temperature during the rolling process is kept not lower than 960℃. After forging, the workpiece is cooled by air and its surface is ground. Seventh hot rolling in the two-phase zone: The titanium alloy workpiece containing Ta that has been hot rolled in the two-phase zone after the sixth hot rolling is heated to 1010℃ and held at this temperature for 180 min. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single hot rolling is 30%, the bite rate is 1.0 m / s, the feed rate is 4.0 m / s, and the final forging temperature during the rolling process is kept not lower than 940℃. After forging, the workpiece is cooled by air and its surface is ground. (v) Heat treatment The β-phase transformation temperature T of the heat-treated Ta-containing titanium alloy workpiece was determined by metallographic method. β2 Measurements were performed to obtain workpiece T under this mix ratio. β2 =1130℃; The titanium alloy workpiece containing Ta, after undergoing hot deformation, is heated to 1100℃ and held for 240 minutes. Specifically, after heating the furnace to 710℃, the titanium alloy workpiece containing Ta, after undergoing hot deformation, is placed in the furnace and heated to 1100℃ at a heating rate of 15℃ / min. After solution treatment, it is cooled to room temperature by air cooling. Then, the solution-treated workpiece is heated to 710℃ and held for 240 minutes for aging treatment, and then air-cooled to room temperature. (vi) Secondary thermal deformation The heat-treated sheet metal is subjected to an eighth two-phase hot rolling process: the heat-treated titanium alloy workpiece containing Ta is heated to 1030℃ and held for 150 min. Then, the workpiece is subjected to a hot deformation process of "unidirectional rolling" using a rolling mill. The total deformation in a single heat is 8%, the bite rate is 0.6 m / s, the feed rate is 3.0 m / s, and the final forging temperature during the rolling process is kept not lower than 980℃. After forging, the workpiece is cooled by air and its surface is ground. (vii) Annealing The titanium alloy workpiece containing Ta, after undergoing a secondary hot deformation process, is heated to 710℃ and held for 240 minutes.

[0052] Performance Test 3 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Example 3. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 3.

[0053] Table 3. Tensile property test results of the high-temperature titanium alloy in Example 3.

[0054] Comparative Example 1 Similar to Example 1, the difference is that in the batching step (a), the mass percentage of Ta is 0%, so that the powder containing Ta titanium alloy is as follows by mass percentage: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, with the balance being Ti and unavoidable impurities.

[0055] Performance Test 4 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 1. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 4.

[0056] Table 4. Tensile property test results of the high-temperature titanium alloy in Comparative Example 1

[0057] Comparative Example 2 Similar to Example 1, the difference is that in the batching step (a), the mass percentage of Ta is 7%, resulting in the following mass percentage of the Ta-containing titanium alloy powder: Al: 5.8±0.1%, W: 2.5±0.05%, Si: 0.4±0.05%, C: 0.05±0.01%, Sn: 8.0±0.1%, Ta: 7.0%, with the balance being Ti and unavoidable impurities.

[0058] Performance Test 5 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 2. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 5.

[0059] Table 5. Tensile property test results of the high-temperature titanium alloy in Comparative Example 2

[0060] Comparative Example 3 Similar to Example 1, the difference is that water cooling is used in all three steps: step (iv) hot deformation, step (v) heat treatment, and step (vi) secondary hot deformation.

[0061] Performance Test 6 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 3. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 6.

[0062] Table 6. Tensile property test results of the high-temperature titanium alloy in Comparative Example 3

[0063] Comparative Example 4 Similar to Example 1, the difference is that air cooling is used in all three steps: step (iv) hot deformation, step (v) heat treatment, and step (vi) secondary hot deformation.

[0064] Performance Test 7 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 4. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 7.

[0065] Table 7. Tensile property test results of the high-temperature titanium alloy in Comparative Example 4

[0066] Comparative Example 5 Same as Example 1, except that in step (v) heat treatment, the workpiece is heated to a temperature below the β phase transformation point T of the forging.β2 Solution treatment is carried out at 60–80℃, as follows: (v) Heat treatment The β-phase transformation temperature T of the heat-treated Ta-containing titanium alloy workpiece was determined by metallographic method. β2 Measurements were performed to obtain workpiece T under this mix ratio. β2 =1090℃; The titanium alloy workpiece containing Ta, after undergoing hot deformation, is heated to 1030℃ and held for 180 minutes. The furnace temperature is then raised to 700℃, and the workpiece is placed in the furnace and heated to the specified temperature at a rate of 15℃ / min. After solution treatment, it is cooled to room temperature by air cooling. Then, the solution-treated workpiece is heated to 700℃ and held for 180 minutes for aging treatment, and then air-cooled to room temperature.

[0067] Performance Test 8 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 5. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 8.

[0068] Table 8. Tensile property test results of the high-temperature titanium alloy in Comparative Example 5

[0069] Comparative Example 6 Same as Example 1, except that step (vi) secondary hot deformation and step (vii) annealing are omitted.

[0070] Performance Test 9 Samples were taken along the ND direction from the high-temperature titanium alloy sheet prepared in Comparative Example 6. Tensile properties were tested at room temperature and high temperature (700℃) according to the national standards GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature" and GB / T 4338-2006 "Metallic materials - Tensile testing method at high temperature". The test was conducted no less than three times at each temperature. The results are shown in Table 9.

[0071] Table 9. Tensile property test results of the high-temperature titanium alloy in Comparative Example 6

[0072] Comparing the data in Tables 1-9, it can be seen that, with other preparation processes remaining the same, the yield strength and tensile strength of the alloy at room temperature and 700℃ increase with increasing Ta content, while the elongation decreases slightly. With the same Sn content, changing the cooling method of the solution treatment from air cooling to water cooling significantly increases the yield strength and tensile strength of the alloy at room temperature and 700℃, but the elongation decreases significantly, far exceeding service requirements. Changing the cooling method of the solution treatment from air cooling to dry cooling significantly decreases the yield strength and tensile strength of the alloy at room temperature and 700℃, but the elongation increases slightly, resulting in a decrease in the overall material performance. Without adding Ta, the yield strength and tensile strength of the material decrease slightly, while the elongation increases slightly (this is based on existing processes). When the Ta content exceeds the composition design range of this invention or the solution temperature is low, the solid solution strengthening effect of the alloy becomes more significant, and the pinning phenomenon caused by lattice distortion due to Ta atoms becomes more prevalent. Simultaneously, the total proportion of Ta and the ordered phase of the (Ti,Al)3Sn structure increases, exceeding the critical threshold, resulting in a significant decrease in the material elongation, exceeding the material service standard.

[0073] The second hot deformation and annealing process is protected by this invention, but it can be omitted in actual processes. The difference lies in the degree of requirement for material strength or plasticity in actual needs. However, regardless of whether this process is performed, it should be within the scope of protection of this invention.

[0074] Figures 1-9 Metallographic images of Ta-containing high-temperature titanium alloys prepared in Examples 1-3 and Comparative Examples 1-6 are shown below. Figures 1-9 It can be observed that, under the condition of maintaining a consistent preparation process, as the Ta content gradually increases, the volume fraction of the equiaxed α phase in the typical bimodal microstructure of the alloy decreases significantly, while the proportion of the microstructure formed by the β phase transformation increases accordingly. If the Ta content of the alloy remains unchanged, and only the cooling method after solution treatment is adjusted from air cooling to air cooling or water cooling, the microstructure morphology changes significantly: the equiaxed α phase formed under water cooling is the smallest, the equiaxed α phase under air cooling is relatively coarse, and the air-cooled microstructure is in between. When the alloy does not contain Ta, a continuous and interconnected network structure easily forms in the grain boundary region, the original lamellar groups are significantly fragmented, and the grain boundary characteristics are more prominent. This microstructure characteristic may weaken the bonding stability of the internal interfaces of the material. Furthermore, when the Ta content is too high or the solution temperature is too low, the microstructure evolution tends to be unbalanced, manifested as the simultaneous growth of the lamellar groups and the original β grains, insufficient lamellar refinement, and enhanced lamellar orientation consistency, ultimately forming a relatively coarse overall transformed lamellar microstructure. In contrast, after secondary hot deformation combined with annealing, the material grains are effectively refined and the number of subgrain boundaries increases significantly.

[0075] The above are merely preferred embodiments of the present invention, but the scope of protection of the present invention is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in the present invention should be included within the scope of protection of the present invention. Therefore, the scope of protection of the present invention should be determined by the scope of the claims.

Claims

1. A method for improving the mechanical properties of Ta-containing high-temperature titanium alloys, characterized in that, Includes the following steps: S1. Mix the raw materials Ti, Al, W, Si, C, Sn and Ta in the specified ratio, press them into electrode blocks, and weld them into consumable electrodes; S2. Vacuum consumable electrode is subjected to consumable arc melting to obtain ingot; S3. The ingot is sequentially subjected to two-stage forging in the single-phase region, two-stage hot deformation forging in the two-phase region, and three-stage hot rolling in the two-phase region, wherein the temperature for the two-stage forging in the single-phase region is T. β1 + (80~150℃); the temperature for two-stage hot deformation forging in the two-phase region is up to T. β1 - (20~50℃); The temperature for the three-stage hot rolling in the two-phase region is T. β1 - (10~40℃); T β1 The β phase transformation temperature of the titanium alloy ingot; S4. Perform solution treatment and aging treatment on the workpiece obtained in step S3. S5. Perform an eighth hot rolling in the two-phase zone on the workpiece that has undergone the aging treatment. S6. The workpiece obtained by hot rolling in the second phase region after the eighth heat treatment is annealed to obtain a high-temperature titanium alloy containing Ta.

2. The method according to claim 1, characterized in that, Step S3 includes the following specific steps: First-stage single-phase forging: heating the ingot to T β1 + (120~150℃), hold for 120~150min, and perform one upsetting and one drawing using a high-speed forging machine. During the upsetting stage, the compressive deformation is 50~60%, corresponding to a deformation rate of 50~60mm / min; during the drawing stage, the tensile deformation is 45~55%, corresponding to a deformation rate of 30~40mm / min; the final forging temperature during the forging process is maintained at ≥T. β1 +20℃, then air-cooled to room temperature; Second-stage single-phase forging: The forging obtained from the first-stage single-phase forging is heated to T. β1 + (80~100℃), hold for 120~150min, and perform one upsetting and one drawing using a high-speed forging machine. During the upsetting stage, the compressive deformation is 45~55%, corresponding to a deformation rate of 45~55mm / min; during the drawing stage, the tensile deformation is 40~50%, corresponding to a deformation rate of 25~35mm / min; the final forging temperature during the forging process is maintained at ≥T. β1 +20℃, then air-cooled to room temperature; Third-stage two-phase zone hot deformation forging: The forging blank obtained from the second-stage single-phase zone forging is heated to T. β1 - (20~40℃), hold for 150~180min, and use a high-speed forging mill for drawing. During the drawing stage, the tensile deformation is 40~50%, the corresponding deformation rate is 30~35mm / min, the single feed is 200~220mm, and the high-speed forging mill frequency is 3s / cycle; the final forging temperature during the forging process is maintained at ≥T. β1 -100℃, cooled to room temperature by air cooling; Fourth-stage two-phase zone hot deformation forging: The forging billet obtained after the third-stage two-phase zone hot deformation forging is heated to T. β1 - (30~50℃), hold for 150~180min, and use a high-speed forging mill for drawing. During the drawing stage, the tensile deformation is 35~40%, the corresponding deformation rate is 25~30mm / min, the single feed is 200~220mm, and the high-speed forging mill frequency is 3s / cycle; the final forging temperature during the forging process is ≥T β1 -120℃, cooled to room temperature by air cooling; Fifth-stage two-phase zone hot rolling: The forging billet obtained from the fourth-stage two-phase zone hot deformation forging is heated to T. β1 - (10~30℃), hold for 150~180min, unidirectional rolling using a rolling mill, wherein the total deformation per pass is 35~40%, the bite rate is 0.5~0.8m / s, the feed rate is 2.5~3.5m / s, and the final forging temperature during the rolling process is maintained at ≥T β1 -100℃, cooled to room temperature by air cooling; Sixth-stage two-phase zone hot rolling: The workpiece obtained after the fifth-stage two-phase zone hot rolling is heated to T. β1 - (20~40℃), hold for 150~180min, unidirectional rolling using a rolling mill, wherein the total deformation per pass is 30~35%, the bite rate is 0.8~1.0m / s, the feed rate is 3.0~4.0m / s, and the final forging temperature during the rolling process is ≥T β1 -100℃, cooled to room temperature by air cooling; Seventh-stage two-phase zone hot rolling: The workpiece obtained after the sixth-stage two-phase zone hot rolling is heated to T. β1 - (30~50℃), hold for 150~180min, unidirectional rolling using a rolling mill, wherein the total deformation per pass is 25~30%, the bite rate is 1.0m / s, the feed rate is 4.0m / s, and the final forging temperature during the rolling process is ≥T β1 -120℃, cooled to room temperature by air cooling.

3. The method according to claim 1, characterized in that, In step S1, the mass ratio of Ti, Al, W, Si, C, Sn and Ta is (77.25~81.25)∶5.8∶2.5∶0.4∶0.05∶8∶(2~6); the vacuum consumable arc melting is carried out three times in an argon atmosphere and a vacuum degree of 0.15~0.20 Pa.

4. The method according to claim 3, characterized in that, The specific parameters for the three self-consuming arc melting processes are as follows: First vacuum self-consuming arc melting: current 30-32kA, voltage 42-44V, speed 300-400mm / min; Second vacuum self-consuming arc melting: current 32-34kA, voltage 44-46V, speed 275-375mm / min; The third vacuum self-consuming arc melting process: current 34-36kA, voltage 46-48V, speed 250-350mm / min.

5. The method according to claim 1, characterized in that, In step S4, the specific steps of the solution treatment are as follows: heating the workpiece obtained after the seventh hot rolling in the two-phase region to T. β2 - (20~30℃), keep warm for 180~240 minutes, then air cool to room temperature.

6. The method according to claim 1, characterized in that, In step S4, the specific steps of the aging treatment are as follows: heat the workpiece obtained after solution treatment to 700±10℃, keep it at that temperature for 180~240min, and then air cool it to room temperature.

7. The method according to claim 1, characterized in that, In step S5, the specific operation steps of the eighth hot rolling in the two-phase region are as follows: heating the workpiece obtained after aging treatment to T β2 - (80~100℃), hold for 120~150min, unidirectional rolling using a rolling mill, wherein the total deformation per pass is 5~8%, the bite rate is 0.4~0.6m / s, the feed rate is 2.0~3.0m / s, and the final forging temperature during the rolling process is ≥T β2 -150℃, cooled to room temperature by air cooling.

8. The method according to claim 1, characterized in that, In step S6, the specific operation steps of the annealing treatment are as follows: heat the workpiece obtained by the eighth hot rolling in the two-phase region to 700±10℃ and hold it for 180~240min.

9. A high-temperature titanium alloy containing Ta, characterized in that, It is prepared using the method described in any one of claims 1-8.

10. The application of the Ta-containing high-temperature titanium alloy as described in claim 9 in the manufacture of high-temperature components for aerospace engines.

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