A high-performance titanium alloy material promoting spheroidization and a preparation method thereof

Abstract

The application discloses a high-performance titanium alloy material for promoting spheroidization and a preparation method thereof, and belongs to the field of high-strength and high-toughness titanium-based alloy materials, and comprises the following steps: high-purity raw materials are smelted into titanium-based alloy button ingots containing different tin element contents by using a vacuum induction smelting furnace; after homogenization treatment of the titanium-based alloy button ingots, a high-performance titanium alloy material is obtained by adopting a sectional hot rolling process; and the high-performance titanium alloy material is subjected to mechanical property testing, and the longitudinal mechanical test results are as follows: yield strength is 880-1080 MPa, tensile strength is 1020-1220 MPa, and elongation is 12.5-23%; and the transverse tensile test results are as follows: yield strength is 920-1100 MPa, tensile strength is 1050-1290 MPa, and elongation is 11-20%. The Ti80 zirconium element is replaced by doping of the tin element, and the rolling process is controlled to promote spheroidization of the structure, so that the strength and ductility of the titanium-based alloy are improved.

Description

Technical Field

[0001] This invention relates to the field of high-strength and high-toughness titanium-based alloy materials technology, and in particular to a high-performance titanium alloy material that promotes spheroidization and its preparation method. Background Technology

[0002] Titanium and titanium alloys, with their high strength, excellent corrosion resistance, and good biocompatibility, have become key structural materials in high-end fields such as aerospace, marine engineering, and biomedicine. Their performance advantages directly support technological upgrades and product iterations in these fields. As modern industry expands into extreme working conditions (such as high temperature, high pressure, and highly corrosive environments), the shortcomings of traditional titanium alloys in high-temperature creep resistance, comprehensive ductility and toughness, and process adaptability are becoming increasingly apparent. They cannot meet the more stringent performance requirements of high-end equipment for structural materials. Therefore, it is urgent to explore effective strengthening and toughening technologies for titanium alloys to overcome the performance bottlenecks of existing materials.

[0003] Currently, combining elemental doping substitution alloying with hot rolling process control is widely recognized as an effective technical direction for improving the overall performance of titanium alloys. In the elemental alloying system, different types of elements play specific functions: Firstly, α-stabilizing elements are the core strengthening components. Among them, aluminum (Al) enhances the high-temperature strength, creep resistance, and creep resistance of titanium alloys through solid solution strengthening or precipitation phase strengthening; oxygen (O), nitrogen (N), and carbon (C), as interstitial α-stabilizing elements, significantly improve the hardness and strength of the α phase with their extremely strong interstitial solid solution strengthening effect; silicon (Si), as an auxiliary α-stabilizing element, can refine grains and promote the precipitation of high-temperature resistant Ti5Si3 silicides, especially improving high-temperature creep resistance in the 600-800℃ range. Secondly, β-stabilizing elements (vanadium V, niobium Nb, molybdenum Mo, tantalum Ta, chromium Cr, iron Fe, etc.) effectively improve the machinability and toughness of titanium alloys by expanding the β phase region.

[0004] Although existing elemental alloying technologies can improve some properties of titanium alloys, significant drawbacks remain, primarily in the limitations of key alloying elements. On the one hand, while β-stabilizing elements (V, Nb, Mo, Ta, Cr, Fe, etc.) can improve processability and toughness, their disadvantages are extremely prominent, including high risk of embrittlement (easily leading to sudden fracture under stress), high raw material costs (e.g., the high price of rare metals like Nb and Ta increases alloy preparation costs), significant toxicity of some elements (e.g., Cr and V may pose safety risks in the biomedical field), a tendency to produce compositional segregation (leading to uneven alloy microstructure and large performance fluctuations), poor corrosion resistance (some elements reduce the stability of the alloy in corrosive environments), and low process compatibility (insufficient compatibility with existing hot rolling and other processing techniques, easily resulting in processing defects). On the other hand, some α-stabilizing elements... While stabilizing elements (such as O, N, and C) offer strong solid solution strengthening effects, excessive addition can lead to a sharp decline in the ductility and toughness of titanium alloys, making it difficult to balance the synergistic improvement in strength and toughness. To ensure the synergistic effect of strength and ductility in the strengthening process of titanium alloys, tin (Sn), as an important alloying element, with its low melting point of 231.9℃, good ductility, chemical stability, and metallic compatibility, can regulate the mechanical, physical, and chemical properties of alloys, imparting machinability and weldability, controlling recrystallization processes and grain boundary behavior, promoting the transformation of irregular grains into low-surface-energy spherical shapes, hindering grain growth, and refining grains. It improves ductility and toughness while maintaining strength, making it an important candidate element in alloying design. However, even with its many advantages, the current technology for the synergistic effect of Sn with other elements is still imperfect, failing to fully realize its potential in performance regulation and process optimization. Overall, existing alloying technologies struggle to balance the strength, toughness, corrosion resistance, processability, and cost control of titanium alloys, and cannot fully meet the application requirements under extreme conditions. Summary of the Invention

[0005] The technical problem to be solved by the present invention is to provide a high-performance titanium alloy material that promotes spheroidization and its preparation method. By adding tin to the titanium-based alloy and controlling the hot rolling process, the microstructure transformation of the titanium-based alloy is promoted, the microstructure is spheroidized, the comprehensive mechanical properties of the titanium-based alloy are improved in multiple dimensions, the production efficiency is increased, and the industrialization of high-performance titanium-based alloys is promoted.

[0006] To solve the above-mentioned technical problems, the technical solution adopted by the present invention is as follows:

[0007] A method for preparing a high-performance titanium alloy material that promotes spheroidization includes the following steps:

[0008] Step 1: Prepare a titanium-based alloy matrix and tin particles to obtain Ti-6Al-3Nb-1Mo-XSn raw material;

[0009] Step 2: Place the raw materials prepared in Step 1 into the vacuum melting furnace chamber, put Zr blocks into the chamber, draw a vacuum, and pass an electric arc to melt the raw material particles to form an ingot block. Turn the ingot block over and add magnetic stirring to mix the raw materials evenly. After cooling, Ti-6Al-3Nb-1Mo-XSn silver-white button ingot block is obtained.

[0010] Step 3: Place the silver-white button ingot block obtained in Step 2 into a tube furnace. After the tube furnace is cleaned, it is heated, kept at that temperature, and then water-cooled to obtain a uniformly composed Ti-6Al-3Nb-1Mo-XSn button ingot.

[0011] Step 4: The button ingot after the composition homogenization treatment in Step 3 is first rolled in the unidirectional zone to obtain the first plate. Then, the first plate is rolled and deformed in the two-phase zone and water-cooled to obtain the high-performance titanium alloy plate.

[0012] A further improvement of the technical solution of the present invention is that: in step 1, the value of X in the Ti-6Al-3Nb-1Mo-XSn raw material is 2-6, that is, the amount of Sn particles added is 2wt%-6wt%.

[0013] A further improvement of the technical solution of the present invention is that: in step 2, when the raw material is placed in the vacuum melting furnace chamber, the Al element is placed at the bottom of the melting crucible, the Sn element is placed at the center above the Al element, and then the Ti, Nb and Mo elements are covered from bottom to top.

[0014] A further improvement to the technical solution of the present invention is that, in step 2, the vacuum is maintained for 10... -3 Pa, apply an arc current of 2A and a magnetic stirring current of 5A, and flip the mixture 5-8 times until there are no particle protrusions on the molten surface.

[0015] A further improvement of the technical solution of the present invention is that: in step 3, after the tubular furnace is purged, the temperature is raised to 1050℃-1150℃ at a heating rate of 10℃ / min, and held for 1.5-2.5h.

[0016] A further improvement of the technical solution of the present invention is that: in step 4, when the ingot is initially rolled in the unidirectional zone, the rolling temperature is 100℃-150℃ above the phase transformation point of the Ti80 alloy, and the rolling temperature is controlled at 1040℃-1060℃.

[0017] A further improvement of the technical solution of the present invention is that: in step 4, when the button ingot is initially rolled in the unidirectional zone, the button ingot is first placed in a muffle furnace and kept warm for 20-40 minutes before rolling, and the deformation amount is 45%-50% of the thickness before deformation.

[0018] A further improvement to the technical solution of the present invention is that: in step 4, the first plate is rolled in the two-phase region.

[0019] During manufacturing, the rolling temperature is 50℃-100℃ below the phase transformation point of the Ti80 alloy, and the rolling temperature is controlled between 940℃ and 960℃.

[0020] A further improvement of the technical solution of the present invention is that: in step 4, when rolling the first plate in the two-phase region, the first plate is first placed in a muffle furnace and kept warm for 20-40 minutes before rolling, and the deformation is 65%-70% of the thickness of the first plate.

[0021] A high-performance titanium alloy material that promotes spheroidization is disclosed. The mechanical properties of the high-performance titanium alloy material are tested. The longitudinal mechanical test results are: yield strength 880MPa-1080MPa, tensile strength 1020MPa-1220MPa, elongation 12.5%-23%; the transverse tensile test results are: yield strength 920MPa-1100MPa, tensile strength 1050MPa-1290MPa, elongation 11%-20%.

[0022] The technological advancements achieved by this invention due to the adoption of the above technical solutions are as follows:

[0023] 1. This invention effectively overcomes the processing difficulties of Sn element's low melting point and easy volatility by optimizing the melting current and stirring intensity during vacuum melting and making reasonable material distribution in the early stage of melting. In the obtained titanium-based alloy material ingot, Sn atoms preferentially replace Ti atoms in the α-Ti lattice to form Ti-Sn solid solution. Since the Sn atomic radius (0.158nm) is larger than that of Ti (0.147nm), the lattice distortion is significant and the dislocation slip resistance is increased, thereby improving the alloy strength.

[0024] 2. This invention first rolls the grains in the β single-phase region to obtain a large amount of deformation and break the grains, and then hot rolls them in the two-phase region to suppress the coarsening of the microstructure, fully refine the grains and improve the microstructure. Furthermore, it refines the grains and strengthens them through tin alloying. The combined effect of multiple strengthening mechanisms achieves a synergistic improvement in strength and plasticity.

[0025] 3. The preparation method provided by this invention has strong process compatibility, is suitable for large-scale industrial production, has high cost-effectiveness, does not require expensive equipment investment, has a short technology transformation path, is easy to implement, and is applicable to the industrial production of aerospace parts, engine blades, etc. Attached Figure Description

[0026] To more clearly illustrate the technical solutions in the embodiments of the present invention or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0027] Figure 1 Metallographic microstructure of the Sn-enhanced and hot-rolled process-controlled titanium-based alloy prepared in Example 1 of this invention;

[0028] Among them, (a) and (b) are metallographic images under a 50µm scale, and (c) and (d) are metallographic images under a 20µm scale;

[0029] Figure 2 The image shows the metallographic microstructure of the Sn-enhanced and hot-rolled process-controlled titanium-based alloy prepared in Example 2 of this invention.

[0030] Among them, (a) and (b) are metallographic images under a 50µm scale, and (c) and (d) are metallographic images under a 20µm scale;

[0031] Figure 3 The image shows the metallographic microstructure of the Sn-enhanced and hot-rolled process-controlled titanium-based alloy prepared in Example 3 of this invention.

[0032] Among them, (a) and (b) are metallographic images under a 50µm scale, and (c) and (d) are metallographic images under a 20µm scale;

[0033] Figure 4 The image shows the metallographic microstructure of the Sn-enhanced and hot-rolled process-controlled titanium-based alloy prepared in Example 4 of this invention.

[0034] Among them, (a) and (b) are metallographic images under a 50µm scale, and (c) and (d) are metallographic images under a 20µm scale;

[0035] Figure 5 The image shows the metallographic microstructure of the Sn-enhanced and hot-rolled process-controlled titanium-based alloy prepared in Example 5 of this invention.

[0036] Among them, (a) and (b) are metallographic images under a 50µm scale, and (c) and (d) are metallographic images under a 20µm scale;

[0037] Figure 6 This is a comparison of the longitudinal tensile curves of Ti-6Al-3Nb-1Mo-3Sn prepared in Example 2 and Ti-6Al-3Nb-1Mo-5Sn prepared in Example 4 of this invention.

[0038] Figure 7 This is a comparison of the transverse tensile curves of Ti-6Al-3Nb-1Mo-3Sn prepared in Example 2 and Ti-6Al-3Nb-1Mo-5Sn prepared in Example 4 of this invention.

[0039] Figure 8Comparison of longitudinal tensile curves of Ti-6Al-3Nb-1Mo-2Sn prepared in Example 1, Ti-6Al-3Nb-1Mo-4Sn prepared in Example 3, and Ti-6Al-3Nb-1Mo-6Sn prepared in Example 5 of this invention;

[0040] Figure 9 The image shows a comparison of the transverse tensile curves of Ti-6Al-3Nb-1Mo-2Sn prepared in Example 1, Ti-6Al-3Nb-1Mo-4Sn prepared in Example 3, and Ti-6Al-3Nb-1Mo-6Sn prepared in Example 5 of this invention. Detailed Implementation

[0041] It should be noted that the terms "comprising" and "having" and any variations thereof in the specification, claims and accompanying drawings of this invention are intended to cover non-exclusive inclusion. For example, a process, method, system, product or device that includes a series of steps or units is not necessarily limited to those steps or units that are explicitly listed, but may include other steps or units that are not explicitly listed or that are inherent to such processes, methods, products or devices.

[0042] The present invention will be further described in detail below with reference to the accompanying drawings and embodiments:

[0043] like Figure 1 As shown, a method for preparing a high-performance titanium alloy material that promotes spheroidization includes the following steps:

[0044] Step 1: Prepare a titanium-based alloy matrix and tin particles to obtain Ti-6Al-3Nb-1Mo-XSn raw material;

[0045] Before mixing, the Ti, Al, Nb, Mo and Sn particles used in the Ti-6Al-3Nb-1Mo-XSn raw material were ultrasonically cleaned in anhydrous ethanol for 20 minutes, and then acid washed.

[0046] The value of X in the Ti-6Al-3Nb-1Mo-XSn raw material ranges from 2 to 6, which means that the Sn particle addition amount is 2wt%-6wt%.

[0047] Step 2: Place the Ti-6Al-3Nb-1Mo-XSn raw material prepared in Step 1 into the vacuum melting furnace chamber, place Zr blocks inside the chamber, and maintain a vacuum of 10°C. -3 Pa, an electric arc (2A) is passed through to melt the raw material particles, the ingot block is turned over and magnetic stirring (5A) is added to mix the raw material evenly, and it is turned over 5-8 times until there are no particles protruding on the molten surface. After cooling, a Ti-6Al-3Nb-1Mo-XSn silver-white button ingot block is obtained.

[0048] The arrangement of materials when placing the prepared Ti-6Al-3Nb-1Mo-XSn raw material into the vacuum melting furnace chamber is as follows: Due to the extremely low melting point of Sn, strong volatilization often occurs during the melting process. Utilizing the differences in melting points among the elements, Al, which has a lower melting point, is placed at the bottom of the melting crucible, and Sn, which has the lowest melting point, is placed above and in the center of the Al element, placing it in the core position of the raw material. Then, Ti, Nb, and Mo, which have slightly higher melting points, are sequentially covered on the surface of the raw material from bottom to top. This arrangement of the raw material according to the distribution of element melting points allows the elements with higher melting points to melt to the maximum extent and be evenly distributed within the limited melting current and temperature, while Sn, which has the lowest melting point, melts and is evenly distributed in the core through heat transfer, reducing the volatilization of Sn and the resulting compositional deviations.

[0049] Step 3: Place the silver-white button ingot obtained in Step 2 into a tube furnace. After cleaning the tube furnace, heat it to 1050℃-1150℃ at a heating rate of 10℃ / min, hold it at that temperature for 1.5-2.5h, and then water cool it to obtain a uniformly composed Ti-6Al-3Nb-1Mo-XSn button ingot.

[0050] Step 4: The ingot after the composition homogenization treatment in Step 3 is first rolled in the unidirectional zone to obtain the first plate. Then, the first plate is rolled and deformed in the two-phase zone and water-cooled to obtain the high-performance titanium alloy plate.

[0051] When the ingot is initially rolled in the unidirectional zone, the rolling temperature is 100℃-150℃ above the phase transformation point of the Ti80 alloy, and the rolling temperature is controlled at 1040℃-1060℃.

[0052] When the ingot is initially rolled in the unidirectional zone, the button ingot is first placed in a muffle furnace and held for 20-40 minutes, then rolled 15-20 times, with a deformation amount of 45%-50% of the original thickness. When the first plate is rolled in the two-phase zone, the rolling temperature is 50℃-100℃ below the phase transformation point of the Ti80 alloy, and the rolling temperature is controlled at 940℃-960℃.

[0053] When rolling the first plate in the two-phase region, first place the first plate in a muffle furnace and hold it for 20-40 minutes, then roll it 8-20 times, with the deformation amount being 65%-70% of the thickness of the first plate.

[0054] The high-performance titanium alloy material with spheroidization promotion obtained by the above preparation method was subjected to mechanical property tests. The longitudinal mechanical test results were: yield strength 880MPa-1080MPa, tensile strength 1020MPa-1220MPa, and elongation 12.5%-23%; the transverse tensile test results were: yield strength 920MPa-1100MPa, tensile strength 1050MPa-1290MPa, and elongation 11%-20%.

[0055] In the following embodiments, the weight of the melted button ingot is 80g, and the titanium-based alloy consists of titanium (Ti), aluminum (Al), niobium (Nb), molybdenum (Mo), and tin (Sn) particles with a purity ≥99.99%.

[0056] Example 1

[0057] A method for preparing a high-performance titanium alloy material that promotes spheroidization is disclosed in this embodiment. The titanium-based alloy matrix involved is Ti80. Microstructural transformation of the titanium-based alloy is promoted by replacing Zr with tin doping and by controlling the hot rolling process, thereby promoting spheroidization and achieving strength and toughness of the titanium alloy. The composition mass ratio is Ti-6Al-3Nb-1Mo-2Sn, and the preparation method includes the following steps:

[0058] Step 1: Preparation of the titanium-based alloy matrix and tin (Sn) particles: The Ti, Al, Nb, Mo, and Sn particles used were ultrasonically cleaned in anhydrous ethanol for 20 min, followed by acid washing. After cleaning and drying, the following proportions were prepared: Al: 4.8006 g, Nb: 2.4002 g, Mo: 0.8010 g, Sn: 1.6004 g, with the remainder being Ti: 70.3998 g. The resulting material was Ti-6Al-3Nb-1Mo-2Sn.

[0059] Step 2, Melting: Place the raw materials into the vacuum melting furnace chamber, and simultaneously place Zr blocks inside the chamber to prevent the influence of oxygen during the melting process. Maintain a vacuum of 10°C. -3 A 2A electric arc is applied to melt the raw material particles. The ingot is then turned over and a magnetic stirrer (5A) is used to mix the raw materials evenly. This process is repeated 5-8 times until there are no protruding particles on the molten surface. After cooling, a silver-white button-shaped Ti-6Al-3Nb-1Mo-2Sn ingot is obtained. The dimensions of the silver-white button-shaped ingot are: diameter 45.78 mm and thickness 13.39 mm.

[0060] Step 3, homogenization of composition: The silver-white button ingot block obtained in step 2 is placed into a tube furnace. After the tube furnace is purged, the temperature is raised to 1100℃ at a heating rate of 10℃ / min and held for 2 hours to allow the components to diffuse fully. Water cooling is then performed to obtain a Ti-6Al-3Nb-1Mo-2Sn button ingot with homogeneous composition.

[0061] Step 4, Hot rolling:

[0062] The muffle furnace is heated to 1050℃ at a heating rate of 10℃ / min and held. The button ingot is placed in the muffle furnace and held for 30 minutes. After holding, it is rolled by a hot rolling mill at a rate of 0.4mm each time. After each rolling, it is held at 1050℃ for 1 minute. The plate thickness is rolled to 7mm and then water-cooled.

[0063] The muffle furnace is kept at 950℃. The plate after the first rolling step is placed into the muffle furnace and held for 30 minutes. Then, it is rolled at a rate of 0.4 mm per roll in the hot rolling mill. After each roll, it is held at 950℃ for 1 minute. The plate thickness is rolled to 2 mm and then water cooled.

[0064] The microstructure of the Ti-6Al-3Nb-1Mo-2Sn plate containing 2wt% Sn prepared by the above steps after wire cutting, polishing, and etching is as follows: Figure 1 As shown, Figure 1 Images (a) and (b) are metallographic images at a 50µm scale, and (c) and (d) are at a 20µm scale. The metallographic microstructure shows that the titanium alloy of this composition consists of relatively long lath α-phase and a small amount of spheroidized equiaxed crystals, but these are large and uneven in size. However, the lath structure and the small amount of spheroidized structure in the alloy improve its longitudinal elongation and strength, enhancing both its strength and ductility. The mechanical properties of the prepared tensile samples were determined using a universal testing machine. The longitudinal tensile test results were: yield strength 920MPa, tensile strength 1150MPa, and elongation 19%; the transverse tensile test results were: yield strength 980MPa, tensile strength 1120MPa, and elongation 16%. Figure 8 , Figure 9 As shown.

[0065] Example 2

[0066] A method for preparing a high-performance titanium alloy material that promotes spheroidization is disclosed in this embodiment. The titanium-based alloy matrix involved is Ti80, and the alloy is strengthened and toughened by replacing Zr with Sn and controlling the rolling process. The composition mass ratio is Ti-6Al-3Nb-1Mo-3Sn, and the preparation method includes the following steps:

[0067] Step 1: Preparation of the titanium-based alloy matrix and Sn particles: The Ti, Al, Nb, Sn, and Mo particles used were ultrasonically cleaned in anhydrous ethanol for 20 minutes, followed by acid washing. After cleaning and drying, the following proportions were prepared: Al: 4.8004 g, Nb: 2.4005 g, Sn: 2.4005 g, Mo: 0.8002 g, with the remainder being Ti: 69.5998 g. The raw materials were obtained after the proportions were prepared.

[0068] Step 2, Melting: Place the raw materials into the vacuum melting furnace chamber, and simultaneously place zirconium blocks inside the chamber to prevent the influence of oxygen during the melting process. Evacuate to 10... -3 A 2A electric arc is applied to melt the raw material particles. The ingot is then turned over and a magnetic stirrer (5A) is used to mix the raw materials evenly. This process is repeated 5-8 times until there are no protruding particles on the molten surface. After cooling, a silver-white button-shaped Ti-6Al-3Nb-1Mo-3Sn ingot is obtained. The dimensions of the silver-white button-shaped ingot are: diameter 46.68mm and thickness 13.52mm.

[0069] Step 3, composition homogenization: The ingot block obtained in step 2 is placed in a tube furnace. After three gas washings in the tube furnace, the temperature is raised to 1100℃ at a heating rate of 10℃ / min and held for 2 hours to allow the components to fully diffuse. Water cooling is then performed to obtain a Ti-6Al-3Nb-1Mo-3Sn button ingot with a homogeneous composition.

[0070] Step 4, Hot rolling:

[0071] The muffle furnace is heated to 1050℃ at a heating rate of 10℃ / min and held. The button ingot is placed in the muffle furnace and held for 30 minutes. Then, it is rolled by a hot rolling mill at a rate of 0.4mm each time. After each rolling, it is held at 1050℃ for 1 minute. The plate thickness is rolled to 7mm and then water-cooled.

[0072] The sheet material is held at 950℃ in a muffle furnace. After the first rolling step, the sheet material is placed in the muffle furnace and held for 30 minutes. Then, it is rolled at a rate of 0.4 mm per roll in a hot rolling mill. After each roll, the sheet material is held at 950℃ for 1 minute. The sheet material is then water-cooled after the thickness is reduced to 2 mm.

[0073] The microstructure of the Ti-6Al-3Nb-1Mo-3Sn plate containing 3wt% Sn prepared by the above steps after wire cutting, polishing, and etching is as follows: Figure 2 As shown, Figure 2 (a) and (b) are metallographic images at a 50µm scale, and (c) and (d) are metallographic images at a 20µm scale. The metallographic microstructure shows that this titanium alloy mainly consists of lath structures and a small amount of spheroidized equiaxed grains. The lath lengths are uneven, and the grains are slightly refined, but the distribution of the lath structure and spheroidized grains is uneven. However, due to the grain refinement, the alloy exhibits improved tensile strength in both the transverse and longitudinal directions without sacrificing ductility. The mechanical properties of the prepared tensile samples were determined using a universal testing machine. The longitudinal tensile yield strength was 1050MPa, the tensile strength was 1200MPa, and the elongation was 12.5%; the transverse tensile yield strength was 1080MPa, the tensile strength was 1280MPa, and the elongation was 11%. Figure 6 , Figure 7 As shown.

[0074] Example 3

[0075] A method for preparing a high-performance titanium alloy material that promotes spheroidization is disclosed in this embodiment. The titanium-based alloy matrix involved is Ti80. Microstructural transformation of the titanium-based alloy is promoted by replacing Zr with tin doping and by controlling the hot rolling process, thereby promoting spheroidization and achieving strength and toughness of the titanium alloy. The composition mass ratio is Ti-6Al-3Nb-1Mo-4Sn, and the preparation method includes the following steps:

[0076] Step 1: Preparation of the titanium-based alloy matrix and Sn particles: The Ti, Al, Nb, Sn, and Mo particles used were ultrasonically cleaned in anhydrous ethanol for 20 minutes, followed by acid washing. After cleaning and drying, the following proportions were prepared: Al: 4.8004 g, Nb: 2.4005 g, Sn: 3.2005 g, Mo: 0.8002 g, with the remainder being Ti: 68.7994 g. The resulting material was Ti-6Al-3Nb-1Mo-4Sn.

[0077] Step 2, Melting: Place the raw materials into the vacuum melting furnace chamber, and simultaneously place zirconium blocks inside the chamber to prevent the influence of oxygen during the melting process. Evacuate to 10... -3 A 2A electric arc is applied to melt the raw material particles. The ingot is then turned over and a magnetic stirrer (5A) is used to mix the raw materials evenly. This process is repeated 5-8 times until there are no protruding particles on the molten surface. After cooling, a silver-white button-shaped Ti-6Al-3Nb-1Mo-4Sn ingot is obtained. The dimensions of the silver-white button-shaped ingot are: diameter 46.68mm and thickness 13.52mm.

[0078] Step 3, homogenization of composition: The silver-white button ingot block obtained in step 2 is placed into a tube furnace. After three gas washings in the tube furnace, the temperature is raised to 1100℃ at a heating rate of 10℃ / min and held for 2 hours to allow the components to fully diffuse. Water cooling is then performed to obtain a Ti-6Al-3Nb-1Mo-4Sn button ingot with homogeneous composition.

[0079] Step 4, Hot rolling:

[0080] The muffle furnace is heated to 1050℃ at a heating rate of 10℃ / min and held. The button ingot is placed in the muffle furnace and held for 30 minutes. Then, it is rolled by a hot rolling mill at a rate of 0.4mm each time. After each rolling, it is held at 1050℃ for 1 minute. The plate thickness is rolled to 7mm and then water-cooled.

[0081] The sheet material is held at 950℃ in a muffle furnace. After the first rolling step, the sheet material is placed in the muffle furnace and held for 30 minutes. Then, it is rolled at a rate of 0.4 mm per roll in a hot rolling mill. After each roll, the sheet material is held at 950℃ for 1 minute. The sheet material is then water-cooled after the thickness is reduced to 2 mm.

[0082] The microstructure of the Ti-6Al-3Nb-1Mo-4Sn plate containing 4wt% Sn prepared by the above steps after wire cutting, polishing, and etching is as follows: Figure 3 As shown, Figure 3Images (a) and (b) are metallographic images at a 50µm scale, and images (c) and (d) are metallographic images at a 20µm scale. The metallographic microstructure shows that the titanium alloy of this composition consists of short rod-shaped α-phase and dispersed spheroidized equiaxed grains, with significantly refined and uniformly distributed grains. Based on the significant grain refinement and the uniformly dispersed distribution of spheroidal structure and short rod-shaped α-phase, the alloy exhibits a significant synergistic improvement in strength and plasticity, making it the optimal composition design. The prepared tensile samples were tested for mechanical properties using a universal testing machine. The longitudinal tensile yield strength reached 1080MPa, the tensile strength increased to 1180MPa, and the elongation reached 19%; the transverse tensile yield strength was 1100MPa, the tensile strength was 1290MPa, and the elongation was 20%. Figure 8 , Figure 9 As shown.

[0083] Example 4

[0084] A method for preparing a high-performance titanium alloy material that promotes spheroidization is disclosed in this embodiment. The titanium-based alloy matrix involved is Ti80. Tin doping is used to alloy and replace zirconium, and the hot rolling process is controlled to promote the microstructure transformation of the titanium-based alloy, thereby promoting spheroidization and achieving strength and toughness of the titanium alloy. The composition mass ratio is Ti-6Al-3N-1Mo-5Sn, and the preparation method includes the following steps:

[0085] Step 1: Preparation of the titanium-based alloy matrix and tin (Sn) particles: The Ti, Al, Nb, Mo, and Sn particles used were ultrasonically cleaned in anhydrous ethanol for 20 minutes, followed by acid washing. After cleaning and drying, the following proportions were prepared: Al: 4.8006 g, Nb: 2.4002 g, Mo: 0.8010 g, Sn: 4.0004 g, with the remainder being Ti: 68.000 g. The resulting material was Ti-6Al-3Nb-1Mo-5Sn.

[0086] Step 2, Melting: Place the raw materials into the vacuum melting furnace chamber, and simultaneously place Zr blocks inside the chamber to prevent the influence of oxygen during the melting process. Maintain a vacuum of 10°C. -3 A 2A electric arc is applied to melt the raw material particles. The ingot is then turned over and a magnetic stirrer (5A) is used to mix the raw materials evenly. This process is repeated 5-8 times until there are no protruding particles on the molten surface. After cooling, a silver-white button-shaped Ti-6Al-3Nb-1Mo-5Sn ingot is obtained. The dimensions of the silver-white button-shaped ingot are: diameter 45.78mm and thickness 13.39mm.

[0087] Step 3, composition homogenization: The ingot block obtained in step 2 is placed into a tube furnace. After the tube furnace is purged, the temperature is increased to 1100℃ at a rate of 10℃ / min. The temperature is held for 2 hours to allow the components to diffuse fully. Water cooling is then performed to obtain a Ti-6Al-3Nb-1Mo-5Sn button ingot with a homogeneous composition.

[0088] Step 4, Hot rolling:

[0089] The muffle furnace is heated to 1050℃ at a heating rate of 10℃ / min and held. The button ingot is placed in the muffle furnace and held for 30 minutes. After holding, it is rolled by a hot rolling mill at a rate of 0.4mm each time. After each rolling, it is held at 1050℃ for 1 minute. The plate thickness is rolled to 7mm and then water-cooled.

[0090] The muffle furnace is kept at 950℃. The plate after the first rolling step is placed into the muffle furnace and held for 30 minutes. Then, it is rolled at a rate of 0.4 mm per roll in the hot rolling mill. After each roll, it is held at 950℃ for 1 minute. The plate thickness is rolled to 2 mm and then water cooled.

[0091] The microstructure of the Ti-6Al-3Nb-1Mo-5Sn plate containing 5 wt% Sn prepared by the above steps after wire cutting, polishing, and etching is as follows: Figure 4 As shown, Figure 4 (a) and (b) are metallographic images at a 50µm scale, and (c) and (d) are at a 20µm scale. The metallographic microstructure shows that the lath structure of this titanium alloy is mostly transformed into spheroidized equiaxed grains, and the grains coarsen with the growth of these grains. Although the spheroidized structure coarsens, the longitudinal elongation of the alloy is still significantly improved, and the transverse and longitudinal strengths remain at a high level. The mechanical properties of the prepared tensile samples were measured using a universal testing machine. The longitudinal yield strength was 1050MPa, the tensile strength was 1220MPa, and the elongation was 20%. The transverse mechanical properties showed a yield strength of 1080MPa, a tensile strength of 1200MPa, and an elongation of 12.5%. Figure 7 , Figure 8 As shown.

[0092] Example 5

[0093] A method for preparing a high-performance titanium alloy material that promotes spheroidization is disclosed in this embodiment. The titanium-based alloy matrix involved is Ti80. Microstructural transformation of the titanium-based alloy is promoted by replacing Zr with tin doping and by controlling the hot rolling process, thereby promoting spheroidization and achieving strength and toughness of the titanium alloy. The composition mass ratio is Ti-6Al-3Nb-1Mo-6Sn, and the preparation method includes the following steps:

[0094] Step 1: Preparation of the titanium-based alloy matrix and Sn particles: The Ti, Al, Nb, and Mo particles used were ultrasonically cleaned in anhydrous ethanol for 20 minutes, followed by acid washing. After cleaning and drying, the following proportions were prepared: Al: 4.8003 g, Nb: 2.4002 g, Sn: 4.8002 g, Mo: 0.8001 g, with the remainder being Ti: 67.202 g. The resulting material was Ti-6Al-3Nb-1Mo-6Sn.

[0095] Step 2, Melting: Place the raw materials into the vacuum melting furnace chamber, and simultaneously place zirconium blocks inside the chamber to prevent the influence of oxygen during the melting process. Maintain the vacuum at 10°C. -3 A 2A electric arc is applied to melt the raw material particles. The ingot is then turned over and a magnetic stirrer (5A) is used to mix the raw materials evenly. This process is repeated 5-8 times until there are no protruding particles on the molten surface. After cooling, a silver-white button-shaped Ti-6Al-3Nb-1Mo-6Sn ingot is obtained. The dimensions of the silver-white button-shaped ingot are: diameter 45.58mm and thickness 13.866mm.

[0096] Step 3, homogenization of composition: The ingot block obtained in step 2 is placed into a tube furnace. After the tube furnace is cleaned, the temperature is increased to 1100℃ at a heating rate of 10℃ / min. The temperature is held for 2 hours to allow the components to fully diffuse. The ingot is then water-cooled to obtain a button ingot with homogeneous composition.

[0097] Step 4, Hot rolling:

[0098] The muffle furnace is heated to 1050℃ at a heating rate of 10℃ / min and held. The button ingot is placed in the muffle furnace and held for 30 minutes. Then, it is rolled by a hot rolling mill at a rate of 0.4mm each time. After each rolling, it is held at 1050℃ for 1 minute. The plate thickness is rolled to 7mm and then water-cooled.

[0099] The sheet material is held at 950℃ in a muffle furnace. After the first rolling step, the sheet material is placed in the muffle furnace and held for 30 minutes. Then, it is rolled at a rate of 0.4 mm per roll in a hot rolling mill. After each roll, the sheet material is held at 950℃ for 1 minute. The sheet material is then water-cooled after the thickness is reduced to 2 mm.

[0100] The microstructure of the Ti-6Al-3Nb-1Mo-6Sn plate containing 6wt% Sn prepared by the above steps after wire cutting, polishing, and etching is as follows: Figure 5 As shown, Figure 5(a) and (b) are metallographic images at a 50µm scale, and (c) and (d) are metallographic images at a 20µm scale. The metallographic microstructure shows that the titanium alloy of this composition consists of clustered, slender lath phases and a small amount of spheroidized equiaxed crystals. However, some laths are coarsened and exhibit a certain directionality, resulting in slightly poor uniformity of the microstructure distribution. With further increases in Sn content, the uniformity of the microstructure decreases, accompanied by an increase in grain size. However, the alloy maintains good plasticity without sacrificing strength, especially with a longitudinal elongation of up to 23%. The mechanical properties of the prepared tensile samples were determined using a universal testing machine. The longitudinal tensile yield strength was 880MPa, the tensile strength was 1020MPa, and the elongation was 23%; the transverse tensile yield strength was 920MPa, the tensile strength was 1050MPa, and the elongation was 14.2%. Figure 8 , Figure 9 As shown.

[0101] In summary, the titanium-based alloy matrix involved in this invention is Ti80. By adding tin (Sn) as an alloying element to replace zirconium (Zr) through a reasonable smelting method, the limitations on the alloying pathways and dosage caused by Zr's low melting point (231.9℃) and easy volatilization are overcome. It fully leverages its diverse core functions. Its alloying function not only regulates the mechanical, physical, and chemical properties of the alloy but also imparts special processing characteristics (such as machinability and weldability). It improves ductility and toughness while maintaining the strength of the titanium alloy. Sn atoms preferentially replace Ti atoms in the α-Ti lattice, forming a Ti-Sn solid solution. Since the atomic radius of Sn (0.158 nm) is larger than that of Ti (0.147 nm), the lattice distortion is significant, increasing the resistance to dislocation slip, thereby enhancing the alloy strength. It promotes the microstructure transformation of the titanium-based alloy, promotes spheroidization of the microstructure, and achieves strength and toughness. Under high temperature (>800℃) or long-term aging conditions, Sn can combine with Ti to form Ti5Sn3 or Ti2Sn3, which further enhances the strength through "precipitation strengthening" (such as increasing tensile strength by 50-100MPa).

[0102] The titanium-based alloy matrix involved in this invention is Ti80, and its strength and toughness are achieved by controlling the rolling process. By adjusting the rolling temperature and holding time, the content and morphology of the matrix phase and precipitated phases are precisely controlled, promoting the spheroidization transformation of the microstructure. This effectively improves the unevenness of the alloy's properties in different orientations caused by the texture formed during the rolling process, ensuring the material's multi-directional and multi-dimensional mechanical properties, expanding its application scenarios, and meeting the demand for high-performance titanium alloys in more fields.

[0103] This invention, through innovative process design, significantly addresses the core pain points of titanium-based materials—despite their excellent performance—including difficulties in processing, high manufacturing costs, and challenges in industrialization. It provides new options for a wider range of industries.

[0104] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and not to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art should understand that modifications can still be made to the technical solutions described in the foregoing embodiments, or equivalent substitutions can be made to some or all of the technical features; and these modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A method for preparing a high-performance titanium alloy material that promotes spheroidization, characterized in that: Includes the following steps Suddenly: Step 1: Prepare a titanium-based alloy matrix and tin particles to obtain Ti-6Al-3Nb-1Mo-XSn raw material; In the Ti-6Al-3Nb-1Mo-XSn raw material, the value of X is 2-6, that is, the Sn particle addition amount is 2wt%-6wt%; Step 2: Place the raw materials prepared in Step 1 into the vacuum melting furnace chamber, put Zr blocks into the chamber, draw a vacuum, and pass an electric arc to melt the raw material particles to form an ingot block. Turn the ingot block over and add magnetic stirring to mix the raw materials evenly. After cooling, a Ti-6Al-3Nb-1Mo-XSn silver-white button ingot block is obtained. Step 3: Place the silver-white button ingot block obtained in Step 2 into a tube furnace. After the tube furnace is cleaned, it is heated, kept at that temperature, and then water-cooled to obtain a uniformly composed Ti-6Al-3Nb-1Mo-XSn button ingot. Step 4: The button ingot after the composition homogenization treatment in Step 3 is first rolled in the single-phase region to obtain the first plate. Then, the first plate is rolled and deformed in the two-phase region and water-cooled to obtain the high-performance titanium alloy plate. When the button ingot is initially rolled in the single-phase region, the button ingot is first placed in a muffle furnace and held for 20-40 minutes; the rolling temperature is 100℃-150℃ above the phase transformation point of Ti80 alloy, and the rolling temperature is controlled at 1040℃-1060℃; the deformation amount is 45%-50% of the thickness before deformation.

2. The preparation method according to claim 1, characterized in that: In step 2, when the raw materials are placed into the vacuum melting furnace chamber, Al elements are placed at the bottom of the melting crucible, Sn elements are placed above the center of the Al elements, and then Ti, Nb, and Mo elements are placed in sequence from bottom to top.

3. The preparation method according to claim 1, characterized in that: In step 2, the vacuum is maintained for 10 seconds. -3 Pa, apply an arc current of 2A and a magnetic stirring current of 5A, and flip the mixture 5-8 times until there are no particle protrusions on the molten surface.

4. The preparation method according to claim 1, characterized in that: In step 3, after gas washing, the tubular furnace is heated to 1050℃-1150℃ at a heating rate of 10℃ / min and held at that temperature for 1.5-2.5h.

5. The preparation method according to claim 1, characterized in that: In step 4, the first plate When the material is rolled in the two-phase region, the rolling temperature is 50℃-100℃ below the phase transformation point of Ti80 alloy, and the rolling temperature is controlled at 940℃-960℃.

6. The preparation method according to claim 1, characterized in that: In step 4, the first plate When rolling the material in the two-phase region, the first plate is first placed in a muffle furnace and held for 20-40 minutes before rolling. The deformation is 65%-70% of the thickness of the first plate.

7. A high-performance titanium alloy material for promoting spheroidization prepared by the preparation method according to any one of claims 1-6, characterized in that, The mechanical properties of the high-performance titanium alloy material were tested. The longitudinal mechanical test results were: yield strength 880MPa-1080MPa, tensile strength 1020MPa-1220MPa, and elongation 12.5%-23%; the transverse tensile test results were: yield strength 920MPa-1100MPa, tensile strength 1050MPa-1290MPa, and elongation 11%-20%.

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