Method for improving the stability of the lamellar structure of a deformed titanium-aluminum-manganese-molybdenum-based intermetallic compound

Abstract

The application discloses a method for improving the stability of a sheet structure of a deformed titanium-aluminum-manganese-molybdenum-based intermetallic compound, and belongs to the technical field of titanium-aluminum alloys. The method comprises the following steps: smelting a titanium-aluminum-manganese-molybdenum-based alloy ingot; performing hot working deformation on the titanium-aluminum-manganese-molybdenum-based alloy ingot to obtain a deformed alloy; performing heat treatment on the deformed alloy to obtain a heat-treated alloy; and under a heat exposure system of 750 DEG C or 800 DEG C, the longest heat exposure time of the heat-treated alloy is greater than or equal to 3000 h. The method realizes the technical effect of improving the stability of the sheet structure of the deformed titanium-aluminum-manganese-molybdenum-based intermetallic compound.

Description

Technical Field

[0001] This invention relates to the field of titanium-aluminum alloy technology, and in particular to a method for improving the stability of the lamellar structure of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds. Background Technology

[0002] TiAl-based intermetallic compounds are a new type of intermetallic compound structural material with low density (~4 g / cm³). 3 With its advantages such as high specific strength and good oxidation resistance, it has great advantages in improving the thrust-to-weight ratio of aerospace engines, improving the fuel combustion efficiency of internal combustion engines, and reducing greenhouse gas emissions. It has important engineering application value in aerospace, weaponry and civilian industries.

[0003] Ti-Al-Mn based intermetallic compounds, such as Ti-42Al-5Mn (at.%), have become an important development direction for low-cost TiAl alloys in recent years due to their combination of good hot deformation ability and low raw material cost. However, the presence of Mn significantly reduces the high-temperature resistance of the alloy. Related technologies have proposed a method to improve the temperature resistance of Ti-Al-Mn based intermetallic compounds by adding trace amounts of Mo. Because Mo has a very strong β-stabilizing effect, its large presence can suppress β at the lamellar interface. o The precipitation of the Laves phase in phase (B2) and α2 lamellars is observed, but at near-service temperatures (e.g., 750°C), the α2+γ→β transition at the lamellar interface can also be induced. o +γ cellular response and α2→β in lamellar tissue o The transformation still results in the alloy exhibiting high-temperature structural instability. Summary of the Invention

[0004] The main objective of this invention is to provide a method for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds, aiming to solve the technical problem of poor lamellar structure stability in current titanium-aluminum-based intermetallic compounds.

[0005] To achieve the above objectives, the present invention provides a method for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds, comprising: Titanium-aluminum-manganese-molybdenum based alloy ingots were obtained through smelting. The titanium-aluminum-manganese-molybdenum based alloy ingot is subjected to hot working deformation to obtain a deformed alloy; The deformed alloy is heat-treated to obtain a heat-treated alloy; Under a heat exposure regime of 750°C or 800°C, the maximum heat exposure time of the heat-treated alloy is greater than or equal to 3000 hours.

[0006] In one embodiment, the heat-treated alloy comprises a titanium-aluminum-manganese-molybdenum-based intermetallic compound, which, by atomic percentage, comprises 40% to 48% Al, 1.0% to 5.0% Mn, 0.5% to 2.0% Mo, and the remainder being Ti.

[0007] In one embodiment, the content of Mo in the titanium-aluminum-manganese-molybdenum-based intermetallic compound is reduced by introducing W in the titanium-aluminum-manganese-molybdenum-based alloy ingot in an amount equal to the reduction in Mo content.

[0008] In one embodiment, the reduction in the Mo content is 0.5% to 1.0% in atomic percentage.

[0009] In one embodiment, the step of hot-working and deforming the titanium-aluminum-manganese-molybdenum-based alloy ingot to obtain a deformed alloy includes: The titanium-aluminum-manganese-molybdenum based alloy ingot is forged and rolled under uncoated processing conditions to obtain a deformed alloy.

[0010] In one embodiment, the forging is a multi-heat deformation process, with a forging heating temperature of 1300℃~1380℃, a forging holding time of 1h~3h, a final forging temperature higher than 1100℃, and air cooling after forging.

[0011] In one embodiment, the rolling is a single-fire hot deformation, with an initial rolling temperature of 1300℃~1350℃ and a post-rolling cooling method of air cooling.

[0012] In one embodiment, the rolling is performed at 1300℃~1380℃ for 1h~3h followed by holding.

[0013] In one embodiment, the heat treatment process is as follows: heat treatment at a temperature of 1250℃~1280℃ for 0.2h-1h, and air cooling is used.

[0014] In one embodiment, the heat treatment further includes: aging treatment at 760℃~850℃ for 3h~6h after air cooling, followed by furnace cooling.

[0015] This invention provides a method for improving the stability of lamellar microstructures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds. Addressing the problem of insufficient high-temperature microstructure stability in Ti-Al-Mn-Mo alloys, this method provides a method of replacing a portion of Mo with an equal amount of W. On one hand, reducing the Mo content in the alloy and controlling it within a reasonable range can suppress the precipitation of brittle Laves phases. On the other hand, while ensuring that the alloy can undergo hot working deformation without cladding, the relatively weaker β-stabilizing effect of W compared to Mo can reduce the α2+γ→β transition at the lamellar interface during thermal exposure. o +γ cellular response and α2→β in lamellar tissue oThe transformation enhances the stability of the lamellar microstructure, thereby improving the heat resistance of the deformed Ti-Al-Mn-Mo alloy. Attached Figure Description

[0016] To more clearly illustrate the technical solutions in the embodiments or related technologies of this drawing, the drawings used in the description of the embodiments or related technologies will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this drawing. For those skilled in the art, other drawings can be obtained based on the structures shown in these drawings without creative effort.

[0017] Figure 1 The image shows a hot-rolled bar of the alloy used in the example. Figure 2 Here is a photograph of the hot-rolled bar of the comparative alloy; Figure 3 The image shows the microstructure of the alloy after heat treatment in the example. Figure 4 The image shows the microstructure of the comparative alloy after heat treatment. Figure 5 The image shows the microstructure of the alloy in the example after being exposed to heat at 750°C for 3000 hours. Figure 6 The microstructure of the comparative alloy after heat exposure at 750℃ for 3000 hours is shown. Figure 7 The image shows the microstructure of the alloy in the example after being exposed to heat at 800°C for 3000 hours. Figure 8 The image shows the microstructure of the comparative alloy after being exposed to heat at 800℃ for 3000 hours.

[0018] 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

[0019] It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.

[0020] The following detailed description, with appropriate reference to the accompanying drawings, specifically discloses embodiments of the present invention for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds. However, unnecessary detailed descriptions may be omitted. For example, detailed descriptions of well-known matters and repetitive descriptions of practically identical structures may be omitted. This is to avoid unnecessarily lengthy descriptions and to facilitate understanding by those skilled in the art. Furthermore, the accompanying drawings and the following description are provided to enable those skilled in the art to fully understand the invention and are not intended to limit the subject matter of the claims.

[0021] The "range" disclosed in this invention is defined by a lower limit and an upper limit. A given range is defined by selecting a lower limit and an upper limit, which define the boundaries of the particular range. Ranges defined in this way can include or exclude endpoints and can be arbitrarily combined; that is, any lower limit can be combined with any upper limit to form a range. For example, if ranges of 60-120 and 80-110 are listed for a specific parameter, it is understood that ranges of 60-110 and 80-120 are also expected. Furthermore, if minimum range values ​​1 and 2 are listed, and if maximum range values ​​3, 4, and 5 are listed, then the following ranges are all expected: 1-3, 1-4, 1-5, 2-3, 2-4, and 2-5. In this invention, unless otherwise stated, the numerical range "ab" represents a shortened representation of any combination of real numbers between a and b, where a and b are real numbers. For example, the numerical range "0-5" indicates that all real numbers between "0-5" have been listed in this article; "0-5" is simply a shortened representation of these numerical combinations. Furthermore, when a parameter is stated as an integer ≥2, it is equivalent to disclosing that the parameter is, for example, an integer such as 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, etc.

[0022] To make the above-mentioned objects, features, and advantages of the present invention more apparent and understandable, the technical solutions of the present invention will be further described below in conjunction with the accompanying drawings and embodiments. However, the present invention is not limited to the listed embodiments, but should also include any other known modifications within the scope of the claims of the present invention.

[0023] Ti-Al-Mn based intermetallic compounds, such as Ti-42Al-5Mn (at.%), have become an important development direction for low-cost TiAl alloys in recent years due to their combination of good hot deformation capability and low raw material cost. However, the presence of Mn significantly reduces the high-temperature resistance of the alloy. For example, at 800℃, a large amount of brittle Laves phase ((Ti,Al)Mn2) precipitates in the microstructure of Ti-42Al-5Mn alloy, causing structural instability; at the same time, Mn in the alloy preferentially oxidizes, forming granular Mn2O3 in the outermost TiO2 oxide film, destroying the compactness of the oxide film. Related technologies have proposed a deformed Ti-Al-Mn-Mo based intermetallic compound, which uses the addition of trace amounts of Mo (0.5-1.0 at.%) to suppress the precipitation of the Laves phase, thereby improving the temperature resistance of Ti-Al-Mn alloys to a certain extent.

[0024] However, in the study of the high-temperature structural stability of this type of alloy, it was found that, due to the extremely strong β-stabilizing effect of Mo, its large presence can suppress the β-stabilizing effect at the lamellar interface. oThe precipitation of the Laves phase in phase (B2) and α2 lamellars is observed, but at near-service temperatures (e.g., 750°C), the α2+γ→β transition at the lamellar interface can also be induced. o +γ cellular response and α2→β in lamellar tissue o The transformation still results in high-temperature structural instability in the alloy. Therefore, in order to utilize the advantages of Ti-Al-Mn-Mo alloys, such as easy deformation and low cost, it is necessary to find suitable control methods to overcome the above-mentioned problems, improve their temperature resistance, and promote their application.

[0025] This invention provides a method for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds. In this embodiment, the method for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds includes: Step S10: Smelting to obtain titanium-aluminum-manganese-molybdenum based alloy ingots; This embodiment uses vacuum induction melting to obtain titanium-aluminum-manganese-molybdenum-based alloy ingots. It is understood that the ingot contains at least four elements: Ti, Al, Mn, and Mo. By introducing W (with the same amount as the reduction in Mo content) into the titanium-aluminum-manganese-molybdenum-based alloy ingot, the Mo content in the titanium-aluminum-manganese-molybdenum-based intermetallic compound is reduced; therefore, the ingot also contains W. Before obtaining the ingot, the reduction in Mo content and the total amount are determined. Subtracting the reduction in Mo content from the total amount of Mo yields the final amount of Mo added, which is the amount of W added. In some feasible implementations, the reduction in Mo content, expressed as an atomic percentage, is 0.5% to 1.0%, for example, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, etc. Mo itself is a trace element in titanium-aluminum alloys; excessively high Mo content can easily induce the α2+γ→β transition at the lamellar interface. o +γ cellular response and α2→β in lamellar tissue o The transformation results in the alloy still exhibiting high-temperature structural instability.

[0026] In some feasible ways, the ingot may also include other non-metallic elements to improve the properties of the intermetallic compound, such as element B and element C.

[0027] In some feasible methods, the main raw materials used in smelting include sponge titanium, high-purity aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, graphite, etc.

[0028] Step S20: The titanium-aluminum-manganese-molybdenum based alloy ingot is subjected to hot working deformation to obtain a deformed alloy; The hot working deformation in this embodiment can include forging and rolling deformation. In this embodiment, the titanium-aluminum-manganese-molybdenum-based alloy ingot is forged and rolled under uncoated processing conditions to obtain a deformed alloy.

[0029] In some feasible embodiments, the forging is a multi-heat deformation process, with the forging heating temperature being 1300℃~1380℃, for example, 1300℃, 1320℃, 1340℃, 1360℃, 1380℃, etc., the forging holding time being 1h~3h, for example, 1h, 1.5h, 2h, 2.5h, 3h, etc., the final forging temperature being higher than 1100℃, for example, 1110℃, 1115℃, 1120℃, etc., and the cooling method after forging being air cooling.

[0030] In some feasible methods, the rolling is a single-fire, two-stage hot deformation, with an initial rolling temperature of 1300℃~1350℃, for example, 1300℃, 1310℃, 1320℃, 1330℃, 1340℃, 1350℃, etc., and air cooling after rolling. It is understood that rolling can also be performed at 1300℃~1380℃, for example, 1300℃, 1320℃, 1340℃, 1360℃, 1380℃, etc., followed by holding at that temperature for 1h~3h, for example, 1h, 1.5h, 2h, 2.5h, 3h, etc.

[0031] Step S30: The deformed alloy is heat-treated to obtain a heat-treated alloy; In this embodiment, the heat treatment process can be: heat treatment at a temperature of 1250℃~1280℃ for 0.2h-1h, with air cooling as the cooling method. The heat treatment temperature can be 1250℃, 1260℃, 1270℃, 1280℃, etc. The heat treatment time can be 0.2h, 0.4h, 0.6h, 0.8h, 1h, etc. In some feasible embodiments, the heat treatment further includes: aging treatment at 760℃~850℃ for 3h-6h after air cooling, followed by furnace cooling. The aging treatment temperature can be 760℃, 780℃, 800℃, 820℃, 850℃, etc. The aging treatment time can be 3h, 4h, 5h, 6h, etc.

[0032] After obtaining the heat-treated alloy, a heat exposure test was conducted to examine the stability of the lamellar structure of the intermetallic compound. The titanium-aluminum-manganese-molybdenum based intermetallic compound obtained by the method in this embodiment exhibited a maximum heat exposure time of 3000 hours or more under a heat exposure regime of 750°C or 800°C.

[0033] In some feasible embodiments, the heat-treated alloy comprises a titanium-aluminum-manganese-molybdenum-based intermetallic compound, which, by atomic percentage, comprises 40%–48% Al, 1.0%–5.0% Mn, 0.5%–2.0% Mo, and the remainder Ti.

[0034] In terms of atomic percentage, the content of Al can be 40%, 42%, 44%, 46%, 48%, etc.; the content of Mn can be 1.0%, 2.0%, 3.0%, 4.0%, 5.0%, etc.; and the content of Mo can be 0.5%, 0.8%, 1.0%, 1.2%, 1.5%, 1.8%, 2.0%, etc.

[0035] In this embodiment, to address the problem of insufficient microstructural stability of Ti-Al-Mn-Mo alloys at high temperatures, a method is provided to replace a portion of Mo with an equal amount of W. On the one hand, reducing the Mo content in the alloy and controlling it within a reasonable range can suppress the precipitation of brittle Laves phase. On the other hand, while ensuring that the alloy can undergo hot working deformation without cladding, the relatively weaker β-stabilizing effect of W compared to Mo can reduce the cellular reaction of α2+γ→βo+γ at the lamellar interface and the α2→β reaction in the lamellar microstructure during heat exposure. o The transformation enhances the stability of the lamellar microstructure, thereby improving the heat resistance of the deformed Ti-Al-Mn-Mo alloy.

[0036] The following detailed description of the method for improving the stability of the lamellar structure of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds according to the present invention, with reference to specific embodiments and comparative examples, is provided in detail.

[0037] Example The alloy composition of the example, by atomic percentage, is: Ti-43.97Al-3.1Mn-0.39Mo-0.40W-0.1B-0.12C.

[0038] The preparation method includes: the main raw materials for alloy preparation are sponge titanium, high-purity aluminum, purified manganese, aluminum-molybdenum master alloy, aluminum-tungsten master alloy, TiB2 powder, and graphite. Four Ø50 mm × 700 mm casting rods are melted in a vacuum induction melting furnace, with a total ingot weight of 20 kg. The alloy casting rods are then directly rolled into 13 mm diameter bars in a single pass using a Y-type rolling mill at a rolling heating temperature of 1360℃.

[0039] The hot-rolled bars were heat-treated at 1270℃ for 30 minutes and then air-cooled to room temperature. They were then aged at 850℃ for 3 hours and then furnace-cooled to room temperature.

[0040] The heat-treated bars were subjected to long-term heat exposure at 750℃ and 800℃ for up to 3000h. The polished microstructure of the above-mentioned series of treated samples was observed using a JXA-8530F electron probe microanalysis (EPMA) in backscattered electron mode (BSE). Sub-backscattered diffraction (EBSD) was used to analyze the phase composition characteristics of the alloy microstructure after heat treatment. The lamellar structure characteristics in the microstructure were analyzed using a Talos F200X field emission transmission electron microscope, and quantitative data of the lamellar structure were obtained by combining image analysis software.

[0041] Comparative Example The comparative alloy composition, by atomic percentage, is: Ti-43.88Al-3.11Mn-0.79Mo-0.09B-0.12C.

[0042] The preparation method includes: the main raw materials for alloy preparation are sponge titanium, high-purity aluminum, purified manganese, aluminum-molybdenum master alloy, TiB2 powder, and graphite. Four Ø50 mm × 700 mm casting rods are melted in a vacuum induction melting furnace, with a total ingot weight of 20 kg. The alloy casting rods are then directly rolled into bars with a diameter of 13 mm in one pass using a Y-type rolling mill, with a rolling heating temperature of 1360℃.

[0043] The hot-rolled bars were heat-treated at 1270℃ for 30 minutes and then air-cooled to room temperature. They were then aged at 850℃ for 3 hours and then furnace-cooled to room temperature.

[0044] The heat-treated bars were subjected to long-term heat exposure at 750℃ and 800℃ for up to 3000h. The polished microstructure of the above-mentioned series of treated samples was observed using a JXA-8530F electron probe microanalysis (EPMA) in backscattered electron mode (BSE). Sub-backscattered diffraction (EBSD) was used to analyze the phase composition characteristics of the alloy microstructure after heat treatment. The lamellar structure characteristics in the microstructure were analyzed using a Talos F200X field emission transmission electron microscope, and quantitative data of the lamellar structure were obtained by combining image analysis software.

[0045] The test results and analysis of the examples and comparative examples are as follows.

[0046] Figure 1 The image shows a hot-rolled bar of the alloy used in the example. Figure 2 This is a photograph of a hot-rolled bar of a comparative alloy. From... Figure 1 and Figure 2 It can be seen that both alloys in the examples and comparative examples can achieve hot rolling deformation without cladding.

[0047] Figure 3 The image shows the microstructure of the alloy after heat treatment, as shown in the example. Figure 4 The image shows the microstructure of the comparative alloy after heat treatment. From... Figure 3 and Figure 4 It can be seen that both alloys in the examples and comparative examples have a near-lamellar structure, that is, mainly composed of α2 / γ lamellae, with a certain amount of β lamellae around the lamellae. o A mixed microstructure of (white) and γ (black). EBSD analysis revealed that the two alloys corresponding to the examples and comparative examples have α2 and β... o The fractions of the three phases β, γ, and H were as follows: 7.07%, 3.71%, and 89.22% in the alloy of the Example; and 2.32%, 5.96%, and 91.72% in the alloy of the Comparative Example. This indicates that, after using the method of the present invention, the β phase in the alloy under the same treatment conditions... o The content of the α2 phase decreased, while the content of the β phase increased. This is because the α2 phase is mainly located in lamellar tissue, while the β phase... o The phase is mainly located around the lamellar structure. Therefore, after using the method of the present invention, the lamellar structure content of the alloy under the same treatment conditions is increased from 67.6% in the comparative example to 80.7%.

[0048] Figure 5 The image shows the microstructure of the alloy in the example after being exposed to heat at 750°C for 3000 hours. Figure 6 This is a microstructure image of the comparative alloy after heat exposure at 750℃ for 3000 hours. From... Figure 5 and Figure 6 It can be seen that the two alloys corresponding to the examples and comparative examples still have a near-lamellar structure after being exposed to heat at 750°C for 3000 hours, and no significant changes have occurred.

[0049] Table 1 shows the interlamellar spacing dimensions of the alloys in the examples and comparative examples during 750°C heat exposure. The quantitative statistical results in Table 1 show that the interlamellar spacing of the comparative alloys is generally higher than that of the example alloys. Furthermore, after 1000 hours of heat exposure at 750°C, the interlamellar spacing of the comparative alloys did not increase significantly, but after 3000 hours of heat exposure, the interlamellar spacing of the comparative alloys increased significantly, by 51%. Using the method of this invention, after 3000 hours of heat exposure at 750°C, the interlamellar spacing of the example alloys remained within the range of 42-45 nm, maintaining high thermal stability.

[0050] Table 1

[0051] Table 2 shows the α2 lamellar precipitation β during the 750°C heat exposure process of the alloys in the examples and comparative examples. o Phase content. Table 2 further reveals that during heat exposure at 750℃, the α2 layers in the lamellar structure precipitate β... o The phase content of the alloys in the examples and the comparative examples also differs to some extent. Specifically, in the comparative example alloy, as the heat exposure at 750°C continued, the β phase precipitated in the α2 lamellar layers increased. oThe phase content is significantly higher than that of the alloy in the examples. This indicates that, after using the method of the present invention and exposing the alloy at 750°C for 3000 hours, the stability of the lamellar phase is improved.

[0052] Table 2

[0053] Figure 7 The image shows the microstructure of the alloy in this example after being exposed to heat at 800°C for 3000 hours. Figure 8 The image shows the microstructure of the comparative alloy after being exposed to heat at 800℃ for 3000 hours. From... Figure 7 and Figure 8 It can be seen that after heat exposure at 800℃ for 3000 hours, there are significant differences in the microstructure of the alloys in the examples and the comparative examples. Specifically, the lamellar content of the alloy in the comparative example is significantly reduced, and lamellar structures appear around the lamellar structures. Figure 8 The yellow dashed line indicates the degradation structure, which is an α2+γ→β transition induced at the lamellar interface after long-term high-temperature thermal exposure of the alloy. o +γ-cellular reaction products. Conversely, using the method of the present invention, the lamellar content of the alloy in the examples remains at a high level, with no obvious cellular reaction products; only γ-grain growth occurs around the lamellar structure. In fact, these relatively large γ-grains are beneficial to the plastic deformation of the alloy. In summary, using the method of the present invention can significantly improve the heat resistance of deformed Ti-Al-Mn-Mo based intermetallic compounds; in this example, the 800°C heat exposure time of the alloy can be extended to at least 3000 hours.

[0054] 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 method for improving the stability of lamellar structures in deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds, characterized in that, The method includes: Titanium-aluminum-manganese-molybdenum based alloy ingots were obtained through smelting. The titanium-aluminum-manganese-molybdenum based alloy ingot is subjected to hot working deformation to obtain a deformed alloy; The deformed alloy is heat-treated to obtain a heat-treated alloy; Under a heat exposure regime of 750°C or 800°C, the maximum heat exposure time of the heat-treated alloy is greater than or equal to 3000 h, wherein the heat-treated alloy comprises a titanium-aluminum-manganese-molybdenum-based intermetallic compound, and by atomic percentage, the titanium-aluminum-manganese-molybdenum-based intermetallic compound comprises 43.97Al-3.1Mn-0.39Mo-0.40W-0.1B-0.12C, with the balance being Ti.

2. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 1, characterized in that, The content of Mo in the titanium-aluminum-manganese-molybdenum-based intermetallic compound is reduced by introducing W in the titanium-aluminum-manganese-molybdenum-based alloy ingot in the same amount as the reduction in Mo content.

3. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 1, characterized in that, The step of hot-working and deforming the titanium-aluminum-manganese-molybdenum-based alloy ingot to obtain the deformed alloy includes: The titanium-aluminum-manganese-molybdenum based alloy ingot is forged and rolled under uncoated processing conditions to obtain a deformed alloy.

4. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 3, characterized in that, The forging process is a multi-heat deformation process, with a forging heating temperature of 1300℃~1380℃, a forging holding time of 1h~3h, a final forging temperature higher than 1100℃, and air cooling after forging.

5. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 3, characterized in that, The rolling process is a single-fire hot deformation, with an initial rolling temperature of 1300℃~1350℃ and a post-rolling cooling method of air cooling.

6. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 5, characterized in that, The rolling process is carried out at 1300℃~1380℃, followed by holding at that temperature for 1h~3h.

7. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 1, characterized in that, The heat treatment process is as follows: heat treatment at a temperature of 1250℃~1280℃ for 0.2h-1h, and air cooling is used.

8. The method for improving the stability of lamellar structures of deformed titanium-aluminum-manganese-molybdenum-based intermetallic compounds as described in claim 7, characterized in that, The heat treatment also includes: aging treatment at 760℃~850℃ for 3h~6h after air cooling, followed by furnace cooling.

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