Multi-component β-solidified γ-TiAl alloy and its preparation method

Abstract

This invention discloses a multi-component β-solidified γ-TiAl alloy and its preparation method, belonging to the field of alloy materials technology. By atomic percentage, it comprises 44.0%-46.0% Al, 1.0%-4.0% Mn, 0.5%-1.5% Mo, and 0.1%-1.0% W, with the remainder being Ti and unavoidable impurity elements. This invention, by adding appropriate amounts of Mn, Mo, and W to the TiAl alloy, ensures that the alloy meets the requirements for forging and rolling deformation under conventional conditions, and possesses good microstructural stability and oxidation resistance.

Description

Technical Field

[0001] This invention relates to the field of alloy materials technology, and in particular to a multi-component β-solidified γ-TiAl alloy and its preparation method. Background Technology

[0002] β-solidified γ-TiAl alloys combine the advantages of low density, high specific strength, and high elastic modulus of γ-TiAl alloys. At the same time, these alloys do not undergo peritectic transformation, have small principal component segregation, and can be hot-worked and deformed, making them a new generation of lightweight and high-temperature resistant structural materials with great application potential.

[0003] Currently, a complete series of β-solidified γ-TiAl alloys has not yet been formed. Common examples include Ti-Al-Nb, Ti-Al-Nb-Mo, Ti-Al-Mn, and Ti-Al-V. Among these systems, Ti-Al-Mn alloys have attracted widespread attention from scholars both domestically and internationally due to their good hot deformability and low material cost. However, high-temperature tests have revealed that these Ti-Al-Mn alloys often suffer from severe deficiencies in high-temperature oxidation resistance and microstructural stability. For instance, the Ti-42Al-5Mn alloy developed by NIMS in Japan, hailed as the world's first β-solidified γ-TiAl alloy capable of cladding-free hot forging deformation, exhibits significant problems during high-temperature service. Mn reacts with other elements to form granular Mn2O3, which adheres to the outermost TiO2 film, making the oxide film prone to detachment and exacerbating oxidation and corrosion of the alloy matrix. Furthermore, brittle Laves phases precipitate, accelerating alloy embrittlement. Summary of the Invention

[0004] The main objective of this invention is to provide a multi-component β-solidified γ-TiAl alloy and its preparation method, aiming to solve the problems of Ti-Al-Mn alloys being prone to precipitating brittle Laves phase and having insufficient high-temperature oxidation resistance.

[0005] To achieve the above objectives, the present invention provides a multi-component β-solidified γ-TiAl alloy, comprising, by atomic percentage, 44.0%-46.0% Al, 1.0%-4.0% Mn, 0.5%-1.5% Mo, 0.1%-1.0% W, with the remainder being Ti and unavoidable impurity elements.

[0006] Optionally, the ratio between the content of Mo and the content of W is greater than 1.0.

[0007] Optionally, the multi-component β-solidified γ-TiAl alloy further comprises 0.05%-0.2% B and 0.1%-0.3% C by atomic percentage.

[0008] Optionally, the impurity elements include O, N, and H, wherein the content of O is less than 0.08 wt.%, the content of N is less than 0.008 wt.%, and the content of H is less than 0.004 wt.%.

[0009] Furthermore, to achieve the above objectives, the present invention also provides a method for preparing a multi-component β-solidified γ-TiAl alloy, used to prepare the multi-component β-solidified γ-TiAl alloy as described above, the preparation method comprising the following steps:

[0010] Raw materials containing Ti, Al, Mn, Mo, W, B, and C elements are selected based on atomic percentage and smelted to obtain ingots;

[0011] The ingot is subjected to heating and heat preservation treatment;

[0012] Multi-component β-solidified γ-TiAl alloy material is obtained by forging and rolling deformation of the ingot after heating and heat preservation in an atmospheric environment.

[0013] Optionally, the temperature of the heating and heat preservation treatment is determined according to the composition of the multi-component β-solidified γ-TiAl alloy, and is the temperature of the α+β two-phase region.

[0014] Optionally, the method of obtaining ingots through smelting includes vacuum induction, a combination of vacuum induction and vacuum self-consumption process, and plasma arc.

[0015] Optionally, the raw materials include sponge titanium, industrial pure aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite.

[0016] Optionally, during the rolling deformation process, a Y-type rolling mill is used for multi-pass rolling in one heat.

[0017] Optionally, the multi-component β-solidified γ-TiAl alloy material is fully oxidation-resistant at 800℃ and has an elongation greater than 15%.

[0018] The multi-component β-solidified γ-TiAl alloy and its preparation method provided by this invention stabilize the β phase with Mn element and use strong β-forming elements such as Mo and W for multi-component micro-alloying. The amount of W, which is prone to segregation, is less than that of Mo element, ensuring that the alloy meets the requirements for forging and rolling deformation under conventional conditions. At the same time, under the condition of simultaneous addition of Mo and W, the alloy can also be controlled to have a high Al content, further ensuring that the alloy has good microstructure stability and oxidation resistance, and is not prone to precipitation of brittle Laves phase. This allows the multi-component β-solidified γ-TiAl alloy material to have both high-temperature oxidation resistance and good hot workability. Attached Figure Description

[0019] Figure 1This is a schematic flowchart of an embodiment of the preparation method of the multi-component β-solidified γ-TiAl alloy of the present invention;

[0020] Figure 2a This is a macroscopic morphology image of the sample surface after 100 oxidation cycles in Comparative Example 1 of this invention.

[0021] Figure 2b This is a macroscopic morphology image of the sample surface after 100 oxidation cycles in Example 1 of the present invention.

[0022] The realization of the objective, functional features and advantages of the present invention will be further explained in conjunction with the embodiments and with reference to the accompanying drawings. Detailed Implementation

[0023] It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.

[0024] β-solidified γ-TiAl alloys combine the advantages of low density, high specific strength, and high elastic modulus of γ-TiAl alloys. Furthermore, these alloys do not undergo peritectic transformation, exhibit minimal principal component segregation, and are hot-workable, making them a promising new generation of lightweight, high-temperature resistant structural materials. Currently, a complete series of β-solidified γ-TiAl alloys has not yet been established. The most commonly reported internationally are Ti-Al-Nb, Ti-Al-Nb-Mo, Ti-Al-Mn, and Ti-Al-V. Due to the high solid solubility of Nb in the γ phase and the strong solid solution strengthening effect, Ti-Al-Nb alloys have high high-temperature strength. However, as the Nb content increases to 4 at.% or above, such as Ti-45Al-9Nb and Ti-43Al-4Nb-1Mo-0.1B (TNM), brittle ω phases are easily precipitated in these β-solidified γ-TiAl alloys. In addition, Ti-Al-Nb alloys have poor hot workability. Even if high-temperature hot working can be achieved, it often needs to be carried out under harsh conditions such as cladding or isothermal treatment, which makes the processing steps complex and expensive.

[0025] Compared to Nb, Mn and V have stronger β-phase stabilizing effects and play a crucial role in the composition design of deformed TiAl alloys. For example, the Ti-42Al-5Mn and Ti-42Al-10V developed in Japan can achieve forging deformation under conventional conditions. In comparison, the material cost of Mn is almost 1 / 150th that of V. Therefore, Ti-Al-Mn β-solidified γ-TiAl alloys have the dual advantages of good hot deformability and low cost, making them an important alternative system for developing low-cost TiAl alloys. However, in high-temperature oxidizing environments, Mn will also undergo preferential selective oxidation along with Ti and Al, forming Mn2O3 oxides that are doped into the outer TiO2 layer. This leads to easy peeling of the oxide film, accelerating the oxidation and erosion of the TiAl matrix. Therefore, Ti-Al-Mn alloys often have poor oxidation resistance. Furthermore, similar to Nb, for some alloys with high Mn content, such as Ti-42Al-5Mn, β-phase stabilization is also affected under near-service temperature conditions. o Both the (B2) phase and the α2 lamellae can lead to localized enrichment of Mn and precipitation of the brittle Laves phase. In order to take advantage of the easy deformation and low cost of Ti-Al-Mn alloys, it is necessary to find suitable composition control methods to overcome the above-mentioned problems of this type of alloy, improve its temperature resistance, and broaden its application fields.

[0026] This invention provides a multi-component β-solidified γ-TiAl alloy, comprising, by atomic percentage, 44.0%-46.0% Al, 1.0%-4.0% Mn, 0.5%-1.5% Mo, 0.1%-1.0% W, with the remainder being Ti and unavoidable impurity elements.

[0027] TiAl alloys primarily consist of Ti and Al. By adding appropriate amounts of Mn, Mo, and W to Ti and Al, a multi-component β-solidified γ-TiAl alloy with Ti-Al-Mn as the main component is formed. Mn stabilizes the β phase, reducing the preparation cost of the alloy material. The addition of strong β-forming elements Mo and W ensures that the alloy can undergo hot deformation under normal conditions. Furthermore, the Al content in the alloy can be increased, improving its oxidation resistance and enabling the alloy material to have complete oxidation resistance at 800℃.

[0028] The microstructure of γ-TiAl alloys is dominated by the γ phase. The Al content is the main factor determining the solidification path under conventional cooling rates; different solidification paths result in different room-temperature microstructures. The atomic percentage of Al in the alloy ranges from 44.0% to 46.0%, for example, 44.0%, 45.0%, or 46.0%. The control of Al content is related to the addition of Mo and W. Within the above range, the alloy can undergo β-solidification and exhibit good high-temperature oxidation resistance.

[0029] The atomic percentage content of Mn is in the range of 1.0%-4.0%, for example, it can be 1.0%, 2.5% or 4.0%. Mn has a β-phase stabilizing effect, and the stabilizing effect is stronger than that of Nb, while the preparation cost is lower than that of V. β-solidified γ-TiAl alloys of the Ti-Al-Mn system have the dual advantages of good hot deformability and low cost.

[0030] The atomic percentage content of Mo is in the range of 0.5%-1.5%, for example, 0.5%, 1.0%, or 1.5%. The atomic percentage content of W is in the range of 0.1%-1.0%, for example, 0.1%, 0.5%, or 1.0%. Mo and W are strong β-forming elements and can also play a role in stabilizing the β phase. However, W undergoes a rapid eutectoid reaction in the β phase and is prone to segregation; therefore, the amount of W added should be less than that of Mo.

[0031] In some feasible implementations, the ratio of Mo to W content can be controlled to be greater than 1.0. This maximizes the individual effects of Mo and W, as well as their interaction, while reducing the amount of W, a component prone to segregation, and ensuring that the alloy can be forged and rolled under normal conditions.

[0032] In some feasible implementations, 0.05%-0.2% B and 0.1%-0.3% C atomic percentages can also be added to the alloy. The addition of trace amounts of B and C can refine the alloy microstructure and improve the high-temperature strength of the alloy.

[0033] In some feasible implementations, the contents of impurity elements O, N, and H can be controlled to ensure that the O content is less than 0.08 wt.%, the N content is less than 0.008 wt.%, and the H content is less than 0.004 wt.%. The introduction of impurity elements can be due to multiple factors, such as impurities in the raw materials or impurities introduced from the air during alloy preparation. The contents of impurity elements can be controlled through various purification methods. Maintaining impurity element contents at extremely low levels ensures the purity of the alloy composition and contributes to the stability of the alloy's properties.

[0034] This invention provides a method for preparing a multi-component β-solidified γ-TiAl alloy, referring to... Figure 1 , Figure 1 This is a schematic flowchart of an embodiment of a method for preparing a multi-component β-solidified γ-TiAl alloy according to the present invention.

[0035] In this embodiment, the preparation method of the multi-component β-solidified γ-TiAl alloy includes:

[0036] Step S10: Take raw materials containing Ti, Al, Mn, Mo, W, B, and C elements according to atomic percentage, and smelt them to obtain ingots;

[0037] The raw materials used in the smelting process can include sponge titanium, industrially pure aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite. Sponge titanium provides titanium (Ti), industrially pure aluminum provides aluminum (Al), purified manganese provides manganese (Mn), the aluminum-molybdenum master alloy provides aluminum and molybdenum (Mo), the aluminum-tungsten master alloy provides aluminum and w (W), TiB2 powder provides titanium (Ti) and boron (B), and graphite provides carbon (C). The amount of each raw material used can be determined by the purity and atomic percentage of each element.

[0038] Smelting refers to the process of melting solid metal into a liquid state, and ingot casting is the product of smelting. In this embodiment, the smelting process can include vacuum induction, a combined vacuum induction and vacuum consumable process, and plasma arc. Different smelting methods can be selected according to actual needs.

[0039] Step S20: The ingot is heated and kept warm.

[0040] After obtaining the ingot, it can be heated and held at a specific temperature to control its microstructure. The heating and holding temperature can be determined based on the composition of the multi-component β-solidified γ-TiAl alloy, specifically the temperature of the α+β two-phase region. Since the types and contents of elements added to the alloy material can vary within a certain range, the temperature of the α+β two-phase region will also change with the alloy composition. Therefore, the temperature of the α+β two-phase region needs to be determined based on the alloy composition. For example, the temperature of the α+β two-phase region is above 1200℃.

[0041] Step S30: The heated and heat-preserved ingot is forged and rolled under atmospheric conditions to obtain a multi-component β-solidified γ-TiAl alloy material.

[0042] The alloy prepared in this embodiment exhibits excellent oxidation resistance, thus allowing for direct, crack-free forging and rolling deformation of the ingot in an uncoated, non-isothermal atmospheric environment. During the forging process, the ingot can be upset or drawn multiple times. Forging can eliminate defects such as casting porosity in metallic materials, optimize the microstructure, and generally results in forgings with superior mechanical properties compared to castings of the same material.

[0043] During the rolling deformation process, a Y-type rolling mill can be used for multi-pass rolling in a single heat. Rolling deformation can reduce the cross-section and increase the length of the material, making it suitable for manufacturing profiles, plates, bars, and other material parts. The multi-component β-solidified γ-TiAl alloy material prepared by the method in this embodiment possesses both hot deformability and high oxidation resistance, exhibiting complete oxidation resistance at 800℃, and showing an elongation greater than 15% after aging treatment at 800℃ for 3000 hours.

[0044] In this embodiment, a multi-component β-solidified γ-TiAl alloy with Ti-Al-Mn as the main component is prepared. This method results in low material cost and employs a multi-component microalloying method using strong β-forming elements such as Mo and W. By controlling the Mo / W ratio to be greater than 1.0, the individual and interactive effects of each element can be maximized, reducing the amount of W, a component prone to segregation, and ensuring the alloy meets the requirements for forging and rolling deformation under conventional conditions. Furthermore, the simultaneous addition of Mo and W allows for control of a high Al content, further ensuring good microstructural stability and oxidation resistance. This multi-component β-solidified γ-TiAl alloy is a lightweight, high-strength, and high-temperature resistant structural material with complete oxidation resistance at 800℃. It holds promise for applications in aerospace, weaponry, and automotive industries, improving the thrust-to-weight ratio of power systems and fuel combustion efficiency.

[0045] Example 1

[0046] This embodiment is a Ti-Al-Mn alloy with both Mo and W added. Its chemical composition, in atomic percentage, is Ti-44.8Al-3.57Mn-0.6Mo-0.4W-0.1B-0.12C, with a Mo / W ratio of 1.5.

[0047] The preparation and testing methods of Example 1 include:

[0048] (1) The main raw materials for alloy preparation are sponge titanium, industrial pure aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite. 20 kg of alloy material was melted in a vacuum induction melting furnace and cast into four pieces with dimensions of [missing information]. The alloy ingots were directly rolled into 12mm diameter bars in one pass using a Y-type rolling mill, with an initial deformation temperature of 1380℃ (i.e., the temperature of the α+β two-phase region). The hot-rolled bars were then subjected to a high-temperature treatment at 1270℃ for 30 minutes, followed by air cooling, and then treated at 850℃ for 3 hours, with furnace cooling.

[0049] (2) The heat-treated rolled bars were aged at 800℃ for 3000h to evaluate the stability of the alloy's long-term aging microstructure and properties. Samples were taken from the heat-treated and long-term aged rolled bars and processed into standard tensile specimens. Tensile tests were conducted on the tensile tester at room temperature and 800℃ to evaluate its comprehensive mechanical properties (the room temperature and high temperature tensile properties were performed according to GB / T228.1-2010 and GB / T228.2-2015 standards, respectively).

[0050] (3) The oxidation resistance of hot-rolled bars at 800℃ was evaluated by cyclic oxidation test. The evaluation method was as follows: a series of 10mm×10mm×5mm test samples were prepared and oxidized at 800℃ under atmospheric conditions. After holding at the temperature for 1 hour, the samples were cooled to room temperature and cyclicated multiple times. According to the Aviation Industry Standard - Test Method for Oxidation Resistance of Steel and High Temperature Alloys (HB52580-2000), the total number of oxidation cycles was 100 times (100h). After cooling, the weight gain due to oxidation and the weight of oxide film peeling off were measured. The instrument was an electronic balance with an accuracy of 0.1mg.

[0051] Comparative Example 1

[0052] This comparative example is a Ti-Al-Mn alloy with Mo added alone, mainly used as a control experiment. Its chemical composition, in atomic percentage, is Ti-43.5Al-3.1Mn-0.8Mo-0.09B-0.11C.

[0053] The preparation and testing methods of Comparative Example 1 include:

[0054] (1) The main raw materials for alloy preparation are sponge titanium, industrial pure aluminum, purified manganese, aluminum-molybdenum master alloy, TiB2 powder, and graphite. 20 kg of alloy material was melted in a vacuum induction melting furnace and cast into four pieces with dimensions of [missing information]. The alloy ingots are directly rolled into bars with a diameter of 12mm in one pass using a Y-type rolling mill, with an initial heating temperature of 1380℃.

[0055] (2) The oxidation resistance of hot-rolled bars at 800℃ was evaluated by cyclic oxidation test. The evaluation method was as follows: a series of 10mm×10mm×5mm test samples were prepared and oxidized at 800℃ under atmospheric conditions. After holding at the temperature for 1 hour, the samples were cooled to room temperature and cyclicated multiple times. According to the Aviation Industry Standard - Test Method for Oxidation Resistance of Steel and High-Temperature Alloys (HB52580-2000), the total number of oxidation cycles was 100 times (100h). After cooling, the weight gain due to oxidation and the weight of oxide film peeling off were measured. The instrument was an electronic balance with an accuracy of 0.1mg.

[0056] Comparative Example 2

[0057] This comparative example is a Ti-Al-Mn alloy with both Mo and W added. Its chemical composition, in atomic percentage, is Ti-42.07Al-2.57Mn-0.24Mo-0.80W-0.4B-0.32C, with a Mo / W ratio of 0.3.

[0058] The preparation and testing methods for Comparative Example 2 include:

[0059] (1) The main raw materials for alloy preparation are sponge titanium, industrial pure aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite. 20 kg of alloy material was melted in a vacuum induction melting furnace and cast into four pieces with dimensions of [missing information]. The alloy ingots were directly rolled into 12mm diameter bars in one pass using a Y-type rolling mill, with an initial deformation temperature of 1380℃. The hot-rolled bars were then subjected to a high-temperature treatment at 1270℃ for 30 minutes, followed by air cooling, and then further treated at 850℃ for 3 hours, with furnace cooling.

[0060] (2) The heat-treated rolled bars were aged at 800℃ for 500h to evaluate the stability of the alloy's long-term aging microstructure and properties. Samples were taken from the heat-treated and long-term aged rolled bars and processed into standard tensile specimens. Tensile tests were conducted on the tensile tester at room temperature and 800℃ to evaluate its comprehensive mechanical properties (the room temperature and high temperature tensile properties were performed according to GB / T228.1-2010 and GB / T228.2-2015 standards, respectively).

[0061] Test Results and Analysis

[0062] Table 1 shows the average oxidation rate and antioxidant level of the samples obtained from Comparative Example 1 and Example 1 after 100 cycles at 800℃ / 1h. The antioxidant level is classified according to the HB 5258-2000 standard. Figure 2a The image shows the macroscopic surface morphology of the sample after 100 oxidation cycles in Comparative Example 1. Figure 2b The image shows the macroscopic surface morphology of the sample after 100 oxidation cycles in Example 1. It can be seen that the average oxidation rate of Comparative Example 1 is 0.115 g·m⁻¹. -2 ·h -1 It exceeded 0.1 g·m -2 ·h -1 This indicates that the alloy is at an oxidation resistance level at 800℃. Further analysis of its macroscopic morphology reveals that after 100 cycles at 800℃ / 1h, the alloy oxide film showed significant peeling. In comparison, the average oxidation rate of Example 1 was only 0.063 g·m⁻¹. -2 ·h -1 It is significantly lower than 0.1 g·m -2 ·h -1 The results indicate that the alloy is at a fully oxidation-resistant level at 800℃, and the oxide film did not peel off under these conditions, as observed from its macroscopic morphology. These results demonstrate that the alloy's oxidation resistance at 800℃ is relatively poor when Mo is added alone, while the combined addition of Mo and W significantly improves its oxidation resistance at 800℃.

[0063] Table 1

[0064]

[0065] Table 2 shows the tensile properties of the samples obtained after heat treatment in Example 1 and Comparative Example 2 at room temperature and 800°C. As can be seen from Table 2, although the difference in tensile properties between the two alloys at room temperature and 800°C is not very significant, the alloy of Example 1 exhibits relatively higher strength and elongation, with a room temperature elongation reaching 1.5%.

[0066] Table 2

[0067]

[0068] Table 3 shows the room temperature and 800°C tensile properties of the samples obtained in Example 1 and Comparative Example 2 after long-term aging at 800°C. It can be seen that for Example 1, even after aging at 800°C for 3000 hours, the room temperature elongation of the alloy remained at 1.5%, and the alloy strength did not show a significant decrease; the elongation at 800°C reached 22.0%. In contrast, for Comparative Example 2, after aging at 800°C for 500 hours, the alloy exhibited brittle fracture at room temperature, and no elongation was detected.

[0069] Table 3

[0070]

[0071] The test results in Tables 2 and 3 show that the alloy obtained in Example 1 not only has better elongation at room temperature, but also higher performance stability after long-term aging at 800℃. This indicates that the effect of the combined addition of Mo and W on the long-term performance stability of Ti-Al-Mn alloys at 800℃ is related to their content ratio; that is, when the Mo / W ratio is greater than 1.0, the alloy exhibits higher performance stability at 800℃. Comparing the Al content of the alloys obtained in Example 1 and Comparative Example 2 also reveals that for a Mo / W ratio greater than 1.0 (1.5 in Example 1), appropriately increasing the Al content (44.8%) still allows for uncoated, non-isothermal rolling deformation. A higher Al content not only improves the alloy's oxidation resistance but also increases the content of the γ phase and reduces the content of the metastable α2 phase, thereby contributing to improved microstructural stability.

[0072] It should be noted that, in this document, the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a process, method, article, or system that comprises a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such a process, method, article, or system. Unless otherwise specified, an element defined by the phrase "comprising one..." does not exclude the presence of other identical elements in the process, method, article, or system that includes that element.

[0073] The sequence numbers of the above embodiments of the present invention are for descriptive purposes only and do not represent the superiority or inferiority of the embodiments.

[0074] The above are merely preferred embodiments of the present invention and do not limit the scope of the patent. Any equivalent structural or procedural transformations made based on the description and drawings of the present invention, or direct or indirect applications in other related technical fields, are similarly included within the scope of patent protection of the present invention.

Claims

1. A multi-component β-solidified γ-TiAl alloy, characterized in that, On an atomic percentage basis, it comprises 45.0%-46.0% Al, 1.0%-4.0% Mn, 0.5%-1.5% Mo, 0.1%-1.0% W, with the remainder being Ti and unavoidable impurity elements, wherein the Mo / W ratio is greater than 1.

0.

2. The multi-component β-solidified γ-TiAl alloy as described in claim 1, characterized in that, The multi-component β-solidified γ-TiAl alloy further comprises 0.05%-0.2% B and 0.1%-0.3% C by atomic percentage.

3. The multi-component β-solidified γ-TiAl alloy as described in claim 2, characterized in that, The impurity elements include O, N and H, wherein the content of O is less than 0.08 wt.%, the content of N is less than 0.008 wt.%, and the content of H is less than 0.004 wt.%.

4. A method for preparing a multi-component β-solidified γ-TiAl alloy, characterized in that, The method for preparing a multi-component β-solidified γ-TiAl alloy as described in any one of claims 1-3 comprises the following steps: Raw materials containing Ti, Al, Mn, Mo, W, B, and C elements are selected based on atomic percentage and smelted to obtain ingots; The ingot is subjected to heating and heat preservation treatment; Multi-component β-solidified γ-TiAl alloy material is obtained by forging and rolling deformation of the ingot after heating and heat preservation in an atmospheric environment.

5. The method for preparing the multi-component β-solidified γ-TiAl alloy as described in claim 4, characterized in that, The temperature of the heating and heat preservation treatment is determined according to the composition of the multi-component β-solidified γ-TiAl alloy, and is the temperature of the α+β two-phase region.

6. The method for preparing the multi-component β-solidified γ-TiAl alloy as described in claim 4, characterized in that, The methods for obtaining ingots through smelting include vacuum induction, a combination of vacuum induction and vacuum self-consumption process, or plasma arc.

7. The method for preparing the multi-component β-solidified γ-TiAl alloy as described in claim 4, characterized in that, The raw materials include sponge titanium, industrial pure aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite.

8. The method for preparing the multi-component β-solidified γ-TiAl alloy as described in claim 4, characterized in that, During the rolling deformation process, a Y-type rolling mill is used for multi-pass rolling in one heat.

9. The method for preparing the multi-component β-solidified γ-TiAl alloy as described in any one of claims 4-8, characterized in that, The multi-component β-solidified γ-TiAl alloy material is fully oxidation-resistant at 800℃, and its elongation is greater than 15% after aging treatment at 800℃.

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