High-strength alloy material and preparation method thereof

Abstract

The invention provides a high-strength alloy material and a preparation method thereof.The high-strength alloy material comprises, by atomic percent, 52.5 at%-57.5 at% of nickel, 5.0 at%-10.0 at% of hafnium, not larger than 1.0 at% of carbon, not larger than 0.5 at% of inevitable inclusions and the balance titanium. The prepared high-strength alloy material has the advantages of high hardness, high wear resistance, high corrosion resistance, superelasticity and higher strength.

Description

TECHNICAL FIELD

[0001] The present application relates to the technical field of alloy materials, in particular to a high-strength alloy material and a preparation method thereof. BACKGROUND

[0002] NiTi alloy has been widely researched and applied due to its excellent shape memory effect, but At present, the strength, wear resistance and corrosion resistance of NiTi alloy are poor, and the density is low, which is difficult to be applied in the field with high requirements on material performance. SUMMARY

[0003] Therefore, the purpose of the present application is to provide a high-strength alloy material and a preparation method thereof.

[0004] To achieve the above purpose, the present application provides a high-strength alloy material, in atomic percentage, the composition of the high-strength alloy material comprises: 52.5at%-57.5at% of nickel, 5.0at%-10.0at% of hafnium, not more than 1.0at% of carbon, not more than 0.5at% of unavoidable inclusions, and the rest is titanium.

[0005] Optionally, the composition of the high-strength alloy material comprises: 53.5at%-56.5at% of nickel, 6.5at%-8.5at% of hafnium, not more than 1.0at% of carbon, not more than 0.5at% of unavoidable inclusions, and the rest is titanium.

[0006] Optionally, the composition of the high-strength alloy material comprises: 54.0at%-56.0at% of nickel, 7.0at%-8.0at% of hafnium, not more than 1.0at% of carbon, not more than 0.5at% of unavoidable inclusions, and the rest is titanium.

[0007] Based on the same inventive concept, the present application also provides a preparation method of a high-strength alloy material, comprising the following steps: The alloy raw material is pretreated to obtain a pretreated alloy raw material; The pretreated alloy raw material is mixed and melted to obtain a molten metal liquid; The molten metal liquid is poured into a red copper mold to cool, and an alloy ingot is obtained; The alloy ingot is subjected to vacuum homogenization treatment to obtain a homogenized alloy ingot; The homogenized alloy is subjected to solid solution treatment and oil quenching to obtain an alloy ingot after solid solution treatment; The alloy ingot after solid solution treatment is subjected to aging treatment and oil quenching to obtain a high-strength alloy material.

[0008] Optionally, the nickel raw material, titanium raw material and hafnium raw material are polished, then immersed in an acetone solution and ultrasonically cleaned for 10-20 min, and then dried at 100-150℃ to obtain the pretreated alloy raw material.

[0009] Optionally, the pretreated alloy raw material is mixed and smelted to obtain a molten metal liquid, which comprises: The pretreated alloy raw material is smelted at a temperature of 1000-1100℃ under a vacuum of 3×10 -3 -5×10 -3 Pa for 20-25 h, and the pretreated alloy raw material is turned over multiple times during the smelting process to obtain the molten metal liquid.

[0010] Optionally, the molten metal liquid is poured into a red copper mold to cool to obtain an alloy ingot, which comprises: the molten metal liquid is poured into a red copper mold to cool at a cooling rate of 9-11℃ / min to obtain the alloy ingot.

[0011] Optionally, the homogenized alloy is subjected to solid solution treatment and oil quenching to obtain a solid solution treated alloy ingot, which comprises: The homogenized alloy is subjected to solid solution treatment at a temperature of 1045-1055℃ for 2-6 hours and oil quenching to obtain the solid solution treated alloy ingot.

[0012] Optionally, the homogenized alloy is subjected to solid solution treatment and oil quenching to obtain a solid solution treated alloy ingot, which comprises: The homogenized alloy is subjected to solid solution treatment at a temperature of 1050℃ for 4 hours and oil quenching to obtain the solid solution treated alloy ingot.

[0013] Optionally, the solid solution treated alloy ingot is subjected to aging treatment and oil quenching to obtain a high-strength alloy material, which comprises: The solid solution treated alloy ingot is subjected to aging treatment at a temperature of 395-405℃ for 2-6 hours and oil quenching to obtain the high-strength alloy material.

[0014] It can be seen from the above that the composition of the high-strength alloy material provided by the application includes: 52.5at%-57.5at% of nickel, 5.0at%-10.0at% of hafnium, not more than 1.0at% of carbon, not more than 0.5at% of inevitable inclusions, and the rest is titanium. Among them, the nickel content is limited in the reasonable range of 52.5at%-57.5at%, which not only avoids the problem of instability of austenite caused by too low nickel content, easy martensite phase change under high temperature stress and reduction of strength, but also avoids the defect of alloy brittleness and forming difficulty caused by too high nickel content. The hafnium content is limited in the range of 5.0at%-10.0at%, which further strengthens the mechanical properties of the alloy, significantly improves the strength and hardness of the alloy on the basis of retaining the original excellent properties. At the same time, the alloy strictly controls the carbon content to be not more than 1.0at%, and the inevitable inclusions content to be not more than 0.5at%, effectively reduces the adverse effects of impurities on performance, guarantees the stability of alloy organization and the reliability of performance, and finally forms an alloy with the comprehensive advantages of high hardness, high wear resistance, high corrosion resistance, super elasticity and higher strength, which lays a solid foundation for its application in high-end bearing and other fields with strict requirements on material performance. BRIEF DESCRIPTION OF DRAWINGS

[0015] In order to more clearly illustrate the technical solutions in the application or related art, the drawings needed to be used in the embodiments or related art description will be briefly introduced. Obviously, the drawings in the following description are only embodiments of the application, and other drawings can be obtained by those skilled in the art without creating laborious work.

[0016] Figure 1 (a) is the alloy morphology diagram of the embodiment of the application after vacuum non-consumable arc melting and natural cooling; Figure 1 (b) is the alloy morphology diagram of the embodiment of the application after vacuum non-consumable arc melting and copper mold suction casting preparation; Figure 2 The hardness diagram of the alloy ingot after vacuum non-consumable arc melting and natural cooling, the alloy ingot after vacuum non-consumable arc melting and copper mold suction casting preparation after solid solution treatment and aging treatment is shown in the embodiment of the application; Figure 3 The strength diagram of the alloy ingot after vacuum non-consumable arc melting and natural cooling, the alloy ingot after vacuum non-consumable arc melting and copper mold suction casting preparation after solid solution treatment and aging treatment is shown in the embodiment of the application. DETAILED DESCRIPTION

[0017] In order to make the purpose, technical solutions and advantages of the application more clear and obvious, the application will be further described in detail below in combination with specific embodiments and with reference to the drawings.

[0018] It should be noted that, unless otherwise defined, the technical or scientific terms used in the embodiments of this application should have the ordinary meaning understood by one of ordinary skill in the art to which this application pertains. The terms "first," "second," and similar terms used in the embodiments of this application do not indicate any order, quantity, or importance, but are merely used to distinguish different components. Terms such as "comprising" or "including" mean that the element or object preceding the word encompasses the elements or objects listed after the word and their equivalents, without excluding other elements or objects. Terms such as "connected" or "linked" are not limited to physical or mechanical connections, but can include electrical connections, whether direct or indirect. Terms such as "upper," "lower," "left," and "right" are only used to indicate relative positional relationships; when the absolute position of the described object changes, the relative positional relationship may also change accordingly.

[0019] As mentioned in the background, NiTi alloys, with their unique shape memory effect and superelasticity, have been widely researched and applied in fields such as biomedicine, aerospace, and intelligent equipment, becoming a functional material with great development potential. However, as high-end applications increasingly demand higher comprehensive performance from materials, the inherent shortcomings of traditional NiTi alloys are becoming more apparent, making it difficult to meet the requirements of harsh working conditions: their strength and wear resistance are insufficient, making them prone to deformation, wear, and even failure in scenarios subjected to dynamic loads and frictional wear (such as high-frequency drive components and mechanical transmission structures), limiting their expansion in heavy-duty and high-wear-resistant fields; their corrosion resistance is limited, and in complex media environments (such as acidic and alkaline media in industrial environments), long-term use may lead to surface corrosion and ion precipitation; at the same time, although low density is an advantage in some lightweight scenarios, in precision structural components that require both high rigidity and impact resistance, the lower density leads to insufficient component stability, making it difficult to meet the comprehensive material requirements of high-end equipment.

[0020] To address the aforementioned problems, this application provides a high-strength alloy material and its preparation method.

[0021] The following is in conjunction with the appendix Figures 1-3 The embodiments of this application will be described in detail below.

[0022] A high-strength alloy material, by atomic percentage, comprises: 52.5 at%-57.5 at% nickel, 5.0 at%-10.0 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder being titanium.

[0023] In this embodiment, the high-strength alloy material comprises: 52.5 at%-57.5 at% nickel, 5.0 at%-10.0 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder being titanium. The nickel content is limited to the reasonable range of 52.5 at%-57.5 at% to avoid the problems of austenitic instability and easy martensitic transformation under high-temperature stress, which reduces strength, caused by excessively low nickel content. It also avoids the defects of brittleness and difficulty in forming caused by excessively high nickel content. The hafnium content is limited to the range of 5.0 at%-10.0 at% to further enhance the mechanical properties of the alloy, significantly improving its strength and hardness while retaining its original excellent characteristics. Meanwhile, the carbon content of the alloy is strictly controlled to be no more than 1.0 at%, and the unavoidable inclusion content is no more than 0.5 at, which effectively reduces the adverse effects of impurities on performance, ensures the stability of the alloy structure and the reliability of its performance. The resulting alloy has the comprehensive advantages of high hardness, high wear resistance, high corrosion resistance, super elasticity and higher strength, laying a solid foundation for its application in fields with stringent material performance requirements, such as high-end bearings.

[0024] In some embodiments, the high-strength alloy material comprises: 53.5 at%-56.5 at% nickel, 6.5 at%-8.5 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder being titanium.

[0025] In addition, the composition of the high-strength alloy material includes: 54.0 at%-56.0 at% nickel, 7.0 at%-8.0 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder is titanium.

[0026] In this embodiment, the high-strength alloy material with the above-mentioned content has its composition ratio optimized and adjusted, which can give full play to the synergistic effect of each element. Compared with other composition ratios, its comprehensive performance is more outstanding.

[0027] Based on the same inventive concept, this application proposes a method for preparing a high-strength alloy material, comprising the following steps: The alloy raw materials are pretreated to obtain pretreated alloy raw materials; The pretreated alloy raw materials are mixed and smelted to obtain molten metal. The molten metal is poured into a copper mold and cooled to obtain an alloy ingot; The alloy ingot is subjected to vacuum homogenization treatment to obtain a homogenized alloy ingot; The homogenized alloy is subjected to solution treatment and oil quenching to obtain a solution-treated alloy ingot. The alloy ingot after solution treatment is subjected to aging treatment and oil quenching to obtain a high-strength alloy material.

[0028] In this embodiment, the high-strength alloy material prepared by the above method includes: 53.5at%-56.5at% nickel, 6.5at%-8.5at% hafnium, no more than 1.0at% carbon, no more than 0.5at% unavoidable inclusions, and the remainder is titanium. This specific composition ratio enables the alloy to achieve synergistic optimization in terms of corrosion resistance, mechanical strength, elastic properties and lightweight, resulting in strong comprehensive performance.

[0029] In some embodiments, the pretreatment of the alloy raw materials to obtain pretreated alloy raw materials includes: After grinding, the nickel, titanium, and hafnium raw materials are immersed in acetone solution and ultrasonically cleaned for 10-20 minutes. After cleaning, they are dried at 100-150℃ to obtain pretreated alloy raw materials.

[0030] In this embodiment, grinding removes impurities such as oxide scale and oil from the surface of the raw materials, followed by ultrasonic cleaning with acetone for 10-20 minutes. This efficiently removes trace contaminants and residual impurities adhering to the surface of the raw materials, preventing these impurities from forming harmful inclusions or defects during the smelting process. Drying at 100-150℃ thoroughly removes moisture and acetone residue from the surface of the raw materials, preventing gas inclusion problems caused by moisture during smelting and ensuring that the raw materials can fully react and uniformly fuse during the mixing and smelting stage. This step effectively reduces the negative impact of impurities on alloy properties, ensures the stability of the subsequent smelting process, and provides the prerequisite for obtaining alloy ingots with uniform composition and dense structure, indirectly improving the mechanical properties and reliability of the final alloy.

[0031] In some embodiments, the step of mixing and melting the pretreated alloy raw materials to obtain molten metal includes: The pretreated alloy raw material was subjected to 3×10 -3 -5×10 -3 Melting at a vacuum of Pa and a temperature of 1000-1100℃ for 20-25 hours, the pretreated alloy raw material is turned over multiple times during the melting process to obtain molten metal.

[0032] In this embodiment, by precisely controlling the vacuum level, temperature, time, and operating method, the homogenization of the alloy composition and the improvement of its purity were achieved. 3×10 -3 -5×10 -3The high vacuum environment of Pa effectively isolates air, preventing the oxidation of active metals such as Ni, Ti, and Hf at high temperatures, while also reducing the entrainment of gaseous impurities. A melting temperature of 1000-1100℃ and a holding time of 20-25 hours ensure thorough melting of all raw materials and uniform atomic diffusion, preventing localized component segregation. Multiple turning operations during the melting process further promote the homogeneity of the molten metal, eliminating performance limitations caused by compositional inhomogeneity. This process ultimately yields a molten metal with precise composition, uniform microstructure, and extremely low impurity content, providing a high-quality material guarantee for subsequent alloy ingot forming and final performance optimization, allowing the alloy's high strength and high hardness to be fully realized.

[0033] In some embodiments, the step of pouring the molten metal into a copper mold for cooling to obtain an alloy ingot includes: pouring the molten metal into a copper mold and cooling it at a cooling rate of 9-11°C / min to obtain an alloy ingot.

[0034] In this embodiment, by selecting a copper mold and precisely controlling the cooling rate, high-quality forming and microstructure optimization of the alloy ingot were achieved. The copper mold possesses excellent thermal conductivity, and combined with a cooling rate of 9-11℃ / min, it can quickly remove the heat from the molten metal, preventing excessive grain growth, and suppressing the precipitation of harmful phases, thus refining the alloy grains. This step ultimately yields a dense, fine-grained, and well-formed alloy ingot, providing a good matrix for subsequent homogenization and solution aging treatments, and laying the microstructure foundation for the alloy to ultimately achieve its performance goals of high hardness, high wear resistance, and high strength.

[0035] In some embodiments, the step of solution treating the homogenized alloy and oil quenching it to obtain a solution-treated alloy ingot includes: The homogenized alloy is solution treated at 1045-1055℃ for 2-6 hours, followed by oil quenching to obtain the solution-treated alloy ingot.

[0036] In addition, the process of solution treating and oil quenching the homogenized alloy to obtain a solution-treated alloy ingot includes: The homogenized alloy was solution treated at 1050°C for 4 hours, followed by oil quenching to obtain the solution-treated alloy ingot.

[0037] In this embodiment, the solution treatment process, through precise control of temperature and holding time combined with oil quenching, creates key conditions for improving alloy performance. A solution temperature of 1045-1055℃ allows solute atoms such as Hf to fully dissolve into the NiTi matrix, forming a supersaturated solid solution, while simultaneously eliminating internal stress and structural defects that may have arisen in previous processes. A holding time of 2-6 hours ensures sufficient atomic diffusion, avoiding the retention of undissolved phases. Rapid oil quenching effectively suppresses solute atom precipitation, stabilizing the supersaturated solid solution at room temperature, laying the foundation for the strengthening effect of subsequent aging treatment. This process not only improves the uniformity and purity of the alloy microstructure but also provides the structural prerequisites for enhancing the alloy's strength and hardness, enabling the alloy to fully leverage the synergistic effect of solution strengthening and precipitation strengthening after subsequent aging treatment.

[0038] In addition, the optimal solution temperature of 1050℃ and the optimal holding time of 4h make the alloy microstructure more stable, making the precipitation strengthening effect of subsequent aging treatment more significant, and ultimately giving the alloy more uniform mechanical properties, ensuring that its advantages of high strength and high hardness are stably presented.

[0039] In some embodiments, the step of aging the solution-treated alloy ingot and oil quenching it to obtain a high-strength alloy material includes: The solution-treated alloy ingot is aged at 395-405℃ for 2-6 hours and then oil-quenched to obtain a high-strength alloy material.

[0040] In this embodiment, the aging treatment process achieves precise strengthening of the alloy's mechanical properties by rationally controlling the temperature and holding time. An aging temperature of 395-405℃ is the optimal range for solute atom precipitation in a supersaturated solid solution. This range promotes the uniform precipitation of fine, dispersed second-phase particles, significantly improving the alloy's strength and hardness through precipitation strengthening, while avoiding the problems of coarsening of second-phase particles due to excessively high temperatures or insufficient precipitation due to excessively low temperatures. A holding time of 2-6 hours ensures that the quantity and size of the precipitated phases reach the optimal state, and oil quenching further solidifies the strengthened microstructure. This process, in synergy with the previous solution treatment, further enhances the alloy's strength and hardness while inheriting its advantages of high wear resistance, high corrosion resistance, and superelasticity, ensuring that the final alloy material fully meets the performance requirements of next-generation advanced bearing materials.

[0041] The present application is described below with reference to specific embodiments.

[0042] Example 1 The alloy raw materials used are high-purity nickel, high-purity titanium, and high-purity hafnium particles, with a purity of not less than 99.99 at%. First, the alloy raw materials undergo pretreatment to obtain clean pretreated alloy raw materials. Before melting, the furnace cavity is evacuated step-by-step using mechanical and molecular pumps to achieve a vacuum level of 3 × 10⁻⁶. -3 -5×10 -3 Pa, then high-purity argon gas was introduced to create an inert protective atmosphere. The furnace cavity vacuum was then stabilized at 5 × 10⁻⁶ Pa. -3 After Pa, the temperature is increased, and the pretreated alloy raw material is subjected to vacuum homogenization treatment. This treatment preferably adopts a process of holding at 1050℃ for 24 hours. In order to obtain a molten metal with uniform composition and microstructure, the pretreated alloy raw material needs to be turned over multiple times during the melting process. After the homogenization treatment is completed, the molten metal is cooled to room temperature with the furnace to obtain an alloy ingot. The alloy ingot is then subjected to solution treatment, which is carried out at 1050℃ for 4 hours. After treatment, it is oil quenched to obtain a solution-treated alloy ingot. Finally, the solution-treated alloy ingot is subjected to aging treatment, which is carried out at 400℃ for 4 hours. After treatment, it is oil quenched again to obtain the target high-strength alloy material.

[0043] Figure 1 The morphology of high-strength alloys prepared by two different processes is shown: (a) The alloy after vacuum non-consumable arc melting and natural cooling (from Example 1) has a radius of approximately 100 mm and a thickness of approximately 22 mm; (b) The alloy prepared by copper mold casting after vacuum non-consumable arc melting (only the copper mold casting cooling step replaces the natural cooling step in Example 1, the other steps are the same), the sample length is approximately 50-65 mm and the radius is approximately 4 mm. The comparison shows that the alloy in Figure (b) prepared by copper mold casting has no obvious defects in appearance, and its forming quality is better than that of the alloy in Figure (a) which was naturally cooled. This indicates that copper mold casting allows for rapid cooling of the alloy, which can quickly remove the heat from the molten metal, avoid excessive grain growth, and inhibit the precipitation of harmful phases, thus refining the alloy grains. This step ultimately yields an alloy with a dense structure, fine grains, and good forming.

[0044] Figure 2The images show the hardness of alloy ingots prepared by vacuum non-consumable arc melting followed by natural cooling (from Example 1) and alloy ingots prepared by vacuum non-consumable arc melting followed by copper mold casting (only the copper mold casting cooling step replaces the natural cooling step in Example 1, with a cooling rate of 10℃ / min, and the other steps are the same), after solution treatment (holding at 1050℃ for 4 hours) and aging treatment (holding at 400℃ for 4 hours). The alloy ingot prepared by vacuum non-consumable arc melting followed by natural cooling reaches a hardness of 765.0 HV after solution treatment and 775.0 HV after aging treatment. The alloy ingot prepared by vacuum non-consumable arc melting followed by copper mold casting reaches a hardness of 795.6 HV after solution treatment, representing an increase of 30.6 HV (4.0%) compared to the alloy ingot prepared by vacuum non-consumable arc melting followed by natural cooling. The alloy ingot prepared by copper mold suction casting achieved a hardness of 806.2 HV after aging treatment, which is 31.2 HV higher than that of the sample prepared by natural cooling, representing an increase of 4.0%.

[0045] Figure 3 The strength diagrams show the results of solution treatment (holding at 1050℃ for 4 hours) and aging treatment (holding at 400℃ for 4 hours) on alloy ingots that were naturally cooled after vacuum non-consumable arc melting (from Example 1) and alloy ingots prepared by copper mold casting after vacuum non-consumable arc melting (only the copper mold casting cooling step was used instead of the natural cooling step in Example 1, with a cooling rate of 10℃ / min, and the other steps were the same). Figure 3 The results show that the alloy prepared by copper mold suction casting has a significantly higher strength than that prepared by natural cooling. The alloy ingot prepared by natural cooling in a vacuum non-consumable arc furnace achieved a strength of 2830 MPa after solution treatment and 2968 MPa after aging treatment. The alloy ingot prepared by copper mold suction casting achieved a strength of 3012 MPa after solution treatment, an increase of 182 MPa (6.4%) compared to the sample prepared by the vacuum non-consumable arc furnace. The alloy ingot prepared by copper mold suction casting achieved a strength of 3136 MPa after aging treatment, an increase of 168 MPa (5.7%) compared to the sample prepared by the vacuum non-consumable arc furnace. Figure 2 and Figure 3 This indicates that the alloy prepared by copper mold suction casting has high hardness and strength.

[0046] Those skilled in the art should understand that the discussion of any of the above embodiments is merely exemplary and is not intended to imply that the scope of this application is limited to these examples; under the concept of this application, the technical features of the above embodiments or different embodiments can also be combined, the steps can be implemented in any order, and there are many other variations of different aspects of the embodiments of this application as described above, which are not provided in detail for the sake of brevity.

[0047] Although this application has been described in conjunction with specific embodiments thereof, many substitutions, modifications, and variations of these embodiments will be apparent to those skilled in the art from the foregoing description. For example, other memory architectures (e.g., dynamic RAM (DRAM)) may be used with the embodiments discussed.

[0048] The embodiments of this application are intended to cover all such substitutions, modifications, and variations that fall within the broad scope of the claims of this application. Therefore, any omissions, modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the embodiments of this application should be included within the protection scope of this application.

Claims

1. A high-strength alloy material, characterized in that, The high-strength alloy material comprises, by atomic percentage, 52.5 at%-57.5 at% nickel, 5.0 at%-10.0 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder being titanium.

2. The high-strength alloy material according to claim 1, characterized in that, The high-strength alloy material comprises: 53.5 at%-56.5 at% nickel, 6.5 at%-8.5 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder being titanium.

3. The high-strength alloy material according to claim 2, characterized in that, The composition of the high-strength alloy material includes: 54.0 at%-56.0 at% nickel, 7.0 at%-8.0 at% hafnium, no more than 1.0 at% carbon, no more than 0.5 at% unavoidable inclusions, and the remainder is titanium.

4. A method for preparing a high-strength alloy material as described in any one of claims 1-3, characterized in that, Includes the following steps: The alloy raw materials are pretreated to obtain pretreated alloy raw materials; The pretreated alloy raw materials are mixed and smelted to obtain molten metal. The molten metal is poured into a copper mold and cooled to obtain an alloy ingot; The alloy ingot is subjected to vacuum homogenization treatment to obtain a homogenized alloy ingot; The homogenized alloy is subjected to solution treatment and oil quenching to obtain a solution-treated alloy ingot. The alloy ingot after solution treatment is subjected to aging treatment and oil quenching to obtain a high-strength alloy material.

5. The preparation method according to claim 4, characterized in that, The process of pretreating the alloy raw materials to obtain pretreated alloy raw materials includes: After grinding, the nickel, titanium, and hafnium raw materials are immersed in acetone solution and ultrasonically cleaned for 10-20 minutes. After cleaning, they are dried at 100-150℃ to obtain pretreated alloy raw materials.

6. The preparation method according to claim 4, characterized in that, The step of mixing and melting the pretreated alloy raw materials to obtain molten metal includes: The pretreated alloy raw material was subjected to 3×10 -3 -5×10 -3 Melting at a vacuum of Pa and a temperature of 1000-1100℃ for 20-25 hours, the pretreated alloy raw material is turned over multiple times during the melting process to obtain molten metal.

7. The preparation method according to claim 4, characterized in that, The step of pouring the molten metal into a copper mold and cooling it to obtain an alloy ingot includes: pouring the molten metal into a copper mold and cooling it at a cooling rate of 9-11℃ / min to obtain an alloy ingot.

8. The preparation method according to claim 4, characterized in that, The process of solution treating the homogenized alloy and oil quenching it to obtain a solution-treated alloy ingot includes: The homogenized alloy is solution treated at 1045-1055℃ for 2-6 hours, followed by oil quenching to obtain the solution-treated alloy ingot.

9. The preparation method according to claim 4, characterized in that, The process of solution treating the homogenized alloy and oil quenching it to obtain a solution-treated alloy ingot includes: The homogenized alloy was solution treated at 1050°C for 4 hours, followed by oil quenching to obtain the solution-treated alloy ingot.

10. The preparation method according to claim 4, characterized in that, The process of aging the solution-treated alloy ingot and oil quenching it to obtain a high-strength alloy material includes: The solution-treated alloy ingot is aged at 395-405℃ for 2-6 hours and then oil-quenched to obtain a high-strength alloy material.

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