Preparation method of high-toughness beta titanium alloy wire

Abstract

The invention discloses a preparation method of a high-toughness beta titanium alloy wire. The preparation method comprises the following steps: providing a beta titanium alloy coiled wire; the coiled wire is subjected to multi-pass roller die hot drawing, and a first middle wire is obtained; performing eye mold hot drawing, sizing and rounding on the first middle wire rod to obtain a second middle wire rod; carrying out on-line short-time solution treatment on the second intermediate wire rod and cooling the second intermediate wire rod; performing eye mold hot drawing on the wire rod subjected to solution treatment to obtain a third middle wire rod; and the third middle wire rod is subjected to eye mold cold drawing, and the beta titanium alloy wire rod of the final specification is obtained. According to the preparation method of the high-toughness beta titanium alloy wire rod, the problems that crystal grains are coarse and large due to repeated solid solution of titanium alloy, sufficient precipitation behaviors cannot be obtained due to direct solid solution, the solid solution cold tensile strength is too high, the plasticity is low and cold plastic forming is difficult to achieve due to sufficient large deformation and cold deformation after solid solution, and the contradiction between the processing technology and the material performance is solved.

Description

Technical Field

[0001] This invention relates to the field of titanium alloy preparation technology, and in particular to a method for preparing high-strength and high-toughness β-titanium alloy wire. Background Technology

[0002] β-titanium alloys, due to their high content of various alloying elements, typically require solution treatment to enhance their cold and hot plastic deformation capabilities. However, the properties of solution-treated materials are often relatively low, necessitating subsequent aging treatment to utilize the precipitation strengthening effect of fine α-phase to achieve the goal of high strength and toughness. Therefore, how to achieve microstructure refinement and performance improvement while ensuring formability has become a key issue in the preparation of this type of alloy.

[0003] Currently, titanium alloy wire is typically produced using a traditional die drawing process combined with solution treatment, followed by aging to achieve precipitation strengthening. However, due to the high deformation resistance resulting from the high alloying properties of β-titanium alloys, the deformation amount in a single drawing is limited, often requiring multiple repeated solution treatments to restore plasticity. This process leads to cyclic deformation and solution treatment, resulting in significant grain coarsening and difficulty in forming a fine-grained structure. Furthermore, direct aging after solution treatment lacks sufficient nucleation sites and driving forces, limiting the effectiveness of precipitation strengthening.

[0004] Among the aforementioned problems, repeated solution treatment leads to coarse grains, weakening the material's potential for fine-grain strengthening; direct aging after solution treatment is insufficient to induce sufficient precipitation behavior; and large deformation cold drawing after solution treatment results in excessively high strength and decreased plasticity, making it difficult for the material to continue cold plastic forming. Therefore, the traditional process route presents a significant contradiction between processing feasibility and material properties. It is urgent to address the numerous problems arising from repeated solution treatment of titanium alloys leading to coarse grains, the inability to achieve sufficient precipitation behavior through direct solution treatment, and the excessively high strength and low plasticity in the solution-treated cold-drawn state after solution treatment, making cold plastic forming difficult. This highlights the contradiction between processing technology and material properties. Summary of the Invention

[0005] In view of the problems existing in the preparation methods of high-strength and high-toughness β-titanium alloy wires, the present invention is proposed.

[0006] Therefore, the purpose of this invention is to provide a method for preparing high-strength and high-toughness β-titanium alloy wire. The purpose is to: through the synergistic process route of "roller hot drawing + eye die sizing + online short-time solid solution + eye die hot drawing + eye die cold drawing", while avoiding grain coarsening, introduce high-density crystal defects to provide sufficient nucleation sites for subsequent aging precipitation, and finally obtain a fine-grained structure with excellent strength and plasticity.

[0007] To solve the above-mentioned technical problems, the present invention provides the following technical solution, including: We offer β-titanium alloy coiled wire.

[0008] The coiled wire is subjected to multiple passes of hot drawing with rollers to obtain the first intermediate wire.

[0009] The first intermediate wire is subjected to hot drawing and sizing using a die to obtain the second intermediate wire.

[0010] The second intermediate wire is subjected to online short-time solution treatment and then cooled.

[0011] The solution-treated wire is subjected to hot drawing with a die to obtain the third intermediate wire.

[0012] The third intermediate wire is cold-drawn using an eye die to obtain the final β titanium alloy wire.

[0013] As a preferred embodiment of the preparation method of the high-strength and high-toughness β-titanium alloy wire of the present invention, the deformation rate of the multi-pass hot drawing is 15%-25%, and the heating temperature before drawing is lower than the phase transformation point of β-titanium alloy.

[0014] In a preferred embodiment of the method for preparing the high-strength and high-toughness β-titanium alloy wire of the present invention, the deformation rate of the pass for hot drawing and sizing of the eye die is 10%-20%, and the heating temperature before drawing is lower than the phase transformation point of the β-titanium alloy.

[0015] In a preferred embodiment of the method for preparing the high-strength and high-toughness β-titanium alloy wire of the present invention, the heating temperature of the online short-time solution treatment is lower than the phase transformation point of the β-titanium alloy, followed by water cooling.

[0016] In a preferred embodiment of the preparation method of the high-strength and high-toughness β-titanium alloy wire of the present invention, the deformation rate of the hot drawing pass of the eye die after solution treatment is 10%-20%, and the heating temperature before drawing is lower than the phase transformation point of β-titanium alloy.

[0017] In a preferred embodiment of the method for preparing the high-strength and high-toughness β-titanium alloy wire of the present invention, the deformation rate of each pass of the cold drawing with the eye die is 5%-10%.

[0018] In a preferred embodiment of the method for preparing the high-strength and high-toughness β-titanium alloy wire of the present invention, the heating temperature below the phase transformation point of the β-titanium alloy is 700°C.

[0019] In a preferred embodiment of the preparation method of the high-strength and high-toughness β-titanium alloy wire of the present invention, the composition of the β-titanium alloy coiled wire includes Ti, Al, Mo, V, Cr, Zr and Sn.

[0020] In a preferred embodiment of the preparation method of the high-strength and high-toughness β-titanium alloy wire of the present invention, the β-titanium alloy coiled wire is a Ti5Al5Mo5V3Cr1Zr1Sn alloy.

[0021] In a preferred embodiment of the preparation method of the high-strength and high-toughness β-titanium alloy wire of the present invention, the wire is prepared by the preparation method described above.

[0022] The beneficial effects of this invention are as follows: This invention combines the advantages of roll drawing technology with an innovative drawing method that achieves rapid hot-drawing deformation with large deformation per pass by heating the alloy to near its phase transformation point. Considering the poor roundness of roll drawing, an eye die is used for sizing and rounding after roll drawing to ensure that the roundness meets the requirements of subsequent wire processing. The large deformation drawing by the roll introduces dislocation distortion energy. Low-temperature, short-time solidification, under the action of high distortion energy, causes the material to rapidly recrystallize, forming numerous recrystallization nucleation sites, thus achieving uniform fine grain formation. The combined deformation mechanism of "hot drawing + cold drawing" with small deformation after solidification generates dislocations again, increasing the intragranular distortion energy. The subsequent aging process provides more precipitate nucleation sites, which is more conducive to the precipitation of secondary fine needle-like α-phase, dispersed in the matrix. This results in an alloy with high strength and high toughness. This combined roll drawing and solution treatment deformation mechanism results in wires with moderate strength and high plasticity, facilitating subsequent cold forming of alloy wire parts without the risk of deformation or cracking. Furthermore, the aging treatment imparts excellent high strength and high toughness to the parts. In this invention, the heating temperature is 700℃ in the roll drawing, solution treatment, and die sizing processes. This process temperature is slightly lower than the phase transformation point of this β-titanium alloy. Therefore, further microstructural analysis, such as... Figure 3 It can be seen that a small amount of primary α phase exists at the grain boundaries. During the heating and holding process of the alloy in multiple hot drawing and solution treatment, the primary α phase distributed at the grain boundaries can effectively suppress grain coarsening and also have a certain effect on enhancing the material properties. Attached Figure Description

[0023] To more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the following description of the embodiments will be briefly introduced. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0024] Figure 1 The metallographic structure of the Φ3.38mm β titanium alloy wire in the embodiment after solution treatment, hot drawing, cold drawing and aging is shown. Figure 2 The microstructure and crystal size diagram of the Φ3.38mm β titanium alloy wire after solution treatment, hot drawing, and cold drawing in the embodiment are shown. Figure 3 The microstructure and crystal size diagram of the Φ3.38mm β titanium alloy wire in the embodiment after solution treatment, hot drawing, cold drawing and aging are shown. Figure 4The diagram shows the phase content distribution of the 3.38mm β-titanium alloy wire in the embodiment after solution treatment, hot drawing, cold drawing, and aging. Detailed Implementation

[0025] To enable those skilled in the art to better understand the present invention, the present invention will be further described in detail below with reference to specific embodiments and accompanying drawings.

[0026] The terminology used in this invention is that which is currently widely used in the art in consideration of the function of the invention; however, these terms may vary according to the intent of those skilled in the art, precedent, or new technology in the art. Furthermore, specific terms may be chosen by the applicant, and in such cases, their detailed meanings will be described in the detailed description of the invention. Therefore, the terms used in this specification should not be construed as simple names, but rather based on their meanings and the overall description of the invention.

[0027] Example 1, the first embodiment of the present invention, provides a method for preparing high-strength and high-toughness β-titanium alloy wire, the method comprising: steps 110-160.

[0028] Step 110. Provide β titanium alloy coiled wire.

[0029] The β-titanium alloy coiled wire, after undergoing large deformation hot continuous rolling, peeling, and surface cleaning, is used as the billet, with an initial diameter of, for example, Φ10.2mm.

[0030] Step 120. Perform multiple hot drawing processes on the coiled wire to obtain the first intermediate wire.

[0031] The coiled wire is fed into a tubular electric furnace and heated to a specific temperature (e.g., 700℃) and held for 3-5 minutes. Then, it undergoes multiple hot drawing passes using a roller drawing machine. This step utilizes the rolling friction characteristics of the rollers to significantly reduce the drawing force, achieving a large deformation rate of 15%-25% per pass, reducing the wire diameter to Φ3.9mm-Φ5.7mm. The wire at this stage is referred to as the first intermediate wire.

[0032] Step 130. Perform hot drawing and sizing on the first intermediate wire using a die to obtain the second intermediate wire.

[0033] Since roller drawing may result in poor wire roundness, the first intermediate wire needs to be reheated (e.g., 700℃) and held for 2-3 minutes before being hot-drawn in a single pass through a die. The deformation rate of this step is controlled at 10%-20%, and its main purpose is to correct the roundness and obtain wire with accurate dimensions of Φ3.5mm-Φ5.2mm, which is the second intermediate wire.

[0034] Step 140. Perform online short-time solution treatment on the second intermediate wire and then cool it.

[0035] The second intermediate wire is subjected to a short-term (3-5 minutes) solution treatment at a specific temperature (e.g., 700°C) in a continuous pass-through manner, followed immediately by water cooling (quenching). This step aims to utilize the distortion energy accumulated from the aforementioned thermal deformation to induce rapid recovery and recrystallization, laying the foundation for obtaining a fine-grained structure.

[0036] Step 150. Perform hot drawing of the solution-treated wire using a die to obtain the third intermediate wire.

[0037] The solution-quenched wire is reheated (e.g., to 700℃) and held for 2-3 minutes. Then, it is hot-drawn in a single pass through a die, with the deformation rate controlled at 10%-20% per pass, until it reaches Φ3.2mm-Φ4.8mm, thus obtaining the third intermediate wire. This step aims to reintroduce a certain amount of dislocations to provide nucleation sites for subsequent aging precipitation.

[0038] Step 160. Perform cold drawing of the third intermediate wire using an eye die to obtain the final β titanium alloy wire.

[0039] Finally, the third intermediate wire is not heated and is directly subjected to single-pass cold drawing with the deformation rate controlled at 5%-10% per pass. It is eventually drawn to the target specification, such as Φ3.1mm-Φ4.6mm, thereby obtaining a finished β-titanium alloy wire with both high strength and high plasticity.

[0040] In one specific embodiment, the deformation rate of each pass in multi-pass hot drawing is 15%-25%, and the heating temperature before drawing is lower than the phase transformation point of β titanium alloy.

[0041] The deformation amount (i.e., the deformation rate per pass) for each pass is set within a large deformation range of 15% to 25%. Before entering the roll drawing process for each pass, the wire is heated in a tube furnace. The heating temperature is strictly controlled below the phase transformation point of the β-titanium alloy (approximately 715℃ for the Ti5Al5Mo5V3Cr1Zr1Sn alloy), for example, 700℃. Simultaneously, to ensure uniform temperature across the wire cross-section, the holding time at the heating temperature is controlled to be 3 to 5 minutes.

[0042] In one specific embodiment, the deformation rate of the hot drawing and sizing process of the eye die is 10%-20%, and the heating temperature before drawing is lower than the phase transformation point of β titanium alloy.

[0043] The deformation amount (deformation rate per pass) of this single pass is controlled between 10% and 20%. Before drawing, the first intermediate wire is also heated in a tubular electric furnace to a temperature below the phase transformation point of β titanium alloy (e.g., 700°C) and held for 2 to 3 minutes to ensure that the material has good plasticity so as to facilitate sizing and rounding.

[0044] In one specific embodiment, the heating temperature of the online short-time solution treatment is lower than the phase transformation point of the β-titanium alloy, followed by water cooling.

[0045] The second intermediate wire is continuously passed through a solution treatment device (such as a tunnel furnace) and heated to a temperature below the phase transformation point of β-titanium alloy (e.g., 700°C). The holding time at this temperature is very short, only 3 to 5 minutes, after which the wire is rapidly immersed in a water bath for quenching and cooling to obtain a supersaturated solid solution.

[0046] In one specific embodiment, the deformation rate of the hot drawing pass of the eye mold after solution treatment is 10%-20%, and the heating temperature before drawing is lower than the phase transformation point of β titanium alloy.

[0047] After online short-time solution treatment and quenching, hot drawing using an eye die is performed. The deformation rate per pass is controlled within a small range of 10% to 20%. Before drawing, the wire is reheated in a tubular electric furnace to a temperature below the phase transformation point of β-titanium alloy (e.g., 700°C) and held for 2 to 3 minutes.

[0048] In one specific implementation, the deformation rate per pass of the cold drawing process is 5%-10%.

[0049] After solution treatment and hot drawing to obtain the third intermediate wire, the final shaping step is die-drawing. The deformation rate in this pass is strictly controlled within a low range of 5% to 10%. This cold drawing process is carried out at room temperature without heating, aiming to further improve the strength and dimensional accuracy of the wire, while avoiding a sharp decrease in plasticity due to excessive work hardening because of its small deformation.

[0050] In one specific embodiment, the heating temperature below the phase transformation point of the β-titanium alloy is 700°C.

[0051] All heating steps involved in the above method, including the temperature before multi-pass hot drawing with rollers, before hot drawing with eye-shaped sizing and rounding, the temperature of online short-time solution treatment, and the temperature before hot drawing with eye-shaped sizing after solution treatment, are uniformly set at 700℃. This temperature is slightly lower than the phase transformation point (~715℃) of typical alloys (such as Ti5Al5Mo5V3Cr1Zr1Sn). This process temperature is slightly lower than the phase transformation point of this β-titanium alloy, which can ensure that the material is in a highly ductile state, effectively suppress excessive grain growth, and use the primary α phase at the grain boundaries to pin the grain boundaries.

[0052] In one specific embodiment, the β-titanium alloy coiled wire comprises Ti, Al, Mo, V, Cr, Zr, and Sn.

[0053] The β-titanium alloy coiled wire to which the above method is applicable has an alloy composition comprising titanium (Ti), aluminum (Al), molybdenum (Mo), vanadium (V), chromium (Cr), zirconium (Zr), and tin (Sn). The combined effect of these multi-element alloying elements ensures that the alloy can achieve significant strengthening after heat treatment through the precipitation of fine secondary α phases.

[0054] In one specific embodiment, the β-titanium alloy coiled wire is a Ti5Al5Mo5V3Cr1Zr1Sn alloy.

[0055] The β-titanium alloy coiled wire is a Ti-5Al-5Mo-5V-3Cr-1Zr-1Sn alloy (i.e., Ti5Al5Mo5V3Cr1Zr1Sn). This alloy is a representative high-alloy β-titanium alloy with a phase transformation point of approximately 715℃, and is a typical application of the composite process route of this invention that can achieve its strength and toughness.

[0056] This invention also directly produces high-strength and high-toughness β-titanium alloy wire using the above-described preparation method. This wire has a uniform and fine grain structure with fine needle-like α-precipitates dispersed within the grains. It also possesses moderate initial working strength and excellent plasticity, facilitating subsequent cold forming processes (such as bending and riveting). Furthermore, it achieves a good balance of extremely high strength and toughness after subsequent aging treatment.

[0057] Example 2: Based on Example 1 above, this example provides a more detailed description of the technical solution of this application in conjunction with actual production.

[0058] The blanks for β-titanium alloy coiled wire were grouped, and each group underwent different drawing and solution treatment processes. The detailed schemes are as follows: Group 1: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 3 minutes, it was subjected to multiple hot drawing passes using a roll drawing machine. The wire after these multiple hot drawing passes was then reheated to 700℃ and held for 3 minutes before being subjected to a single hot drawing pass using a die. A short-term solution treatment at 700℃ was performed, followed immediately by water cooling, yielding β-titanium alloy wire with a diameter of 3.38 mm. The mechanical properties of this β-titanium alloy wire with a diameter of 3.38 mm are: tensile strength 922 Rm / MPa, yield strength 876 Rp0.2 / MPa, etc.

[0059] Group 2: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 3 minutes, it was subjected to multiple hot drawing passes using a roll drawing machine. The wire after multiple hot drawing passes was then reheated to 700℃ and held for 3 minutes, followed by a single hot drawing pass using an eye die. A short-term solution treatment at 700℃ was performed, followed immediately by water cooling. The solution-quenched wire was then reheated to 700℃ and held for 3 minutes, followed by a single hot drawing pass using an eye die to obtain β-titanium alloy wire Φ3.38mm. The mechanical properties of this β-titanium alloy wire Φ3.38mm are tensile strength 973Rm / MPa, yield strength 909Rp0.2 / MPa, etc.

[0060] Group 3: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 3 minutes, it underwent multiple hot drawing passes using a roll drawing machine. The wire after multiple hot drawing passes was then reheated to 700℃ and held for 3 minutes before being hot drawn in a single pass using an eye die. A short-term solution treatment at 700℃ was performed, followed immediately by water cooling. The solution-quenched wire was then reheated to 700℃ and held for 3 minutes before being hot drawn in a single pass using an eye die. The single-pass hot-drawn wire was then cold-drawn directly without reheating to obtain β-titanium alloy wire Φ3.38mm. The mechanical properties of this β-titanium alloy wire Φ3.38mm are tensile strength 1006Rm / MPa, yield strength 912Rp0.2 / MPa, etc.

[0061] Group 4: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 3 minutes, it underwent multiple hot drawing passes using a roll drawing machine. The wire after multiple hot drawing passes was then reheated to 700℃ and held for 3 minutes before being hot drawn in a single pass using an eye die. A short-term solution treatment at 700℃ was performed, followed immediately by water cooling. The solution-quenched wire was then reheated to 700℃ and held for 3 minutes before being hot drawn in a single pass using an eye die. The single-pass hot-drawn wire was then cold-drawn directly without reheating. The cold-drawn titanium alloy wire was then heated to 515℃, held for 10 hours, and then cooled to obtain β-titanium alloy wire Φ3.38mm. The mechanical properties of this β-titanium alloy wire Φ3.38mm are tensile strength 1488Rm / MPa, yield strength 1349Rp0.2 / MPa, etc.

[0062] Group 5: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 3 minutes, it was subjected to multiple hot drawing passes using a roll drawing machine. The wire after these multiple hot drawing passes was then reheated to 700℃ and held for 3 minutes before being subjected to a single hot drawing pass using a die. A short-term solution treatment at 700℃ was performed, followed immediately by water cooling. The solution-quenched titanium alloy wire was then heated to 515℃, held for 10 hours, and then cooled to obtain β-titanium alloy wire with a diameter of Φ3.38mm. The mechanical properties of this β-titanium alloy wire with a diameter of Φ3.38mm are: tensile strength 1366Rm / MPa, yield strength 1221Rp0.2 / MPa, etc.

[0063] Group 6: β-titanium alloy coiled wire was provided. After heating to 700℃ in a tubular electric furnace and holding for 6 minutes, the wire was hot-drawn through a die. A short-term solution treatment at 700℃ was then performed, followed immediately by water cooling. The solution-quenched titanium alloy wire was heated to 515℃, held for 10 hours, and then cooled to obtain β-titanium alloy wire with a diameter of 3.38 mm. The mechanical properties of this β-titanium alloy wire with a diameter of 3.38 mm are as follows: tensile strength 1293 Rm / MPa, yield strength 1154 Rp0.2 / MPa, etc. Table 1

[0064] Table 1 compares the mechanical properties of 3.38mm β-titanium alloy wires obtained after different drawing processes, solution treatments, and aging processes on different groups of β-titanium alloy coils. The table also includes the mechanical properties of 3.38mm β-titanium alloy wires obtained after solution treatment, hot drawing, cold drawing, and aging processes in group 4. Figure 1 Metallographic structure diagram for group 4, attached Figure 3 Microstructure and crystal size diagrams for group 4 and attached figures. Figure 4 This is a phase content distribution diagram for group 4. See attached diagram for comparison. Figure 2 The wire and its attachments obtained after the group 3 processing technology Figure 3 The schematic diagram of the microstructure and crystal size of the wire obtained from the group 4 processing technology shows that the subsequent aging process provides more nucleation sites for precipitation, which is more conducive to the precipitation of secondary fine needle-like α phases, which are dispersed in the matrix. This gives the alloy high strength and high toughness.

[0065] This invention combines the advantages of roll drawing technology with an innovative hot-drawing method that achieves rapid roll drawing deformation with large deformation per pass by heating the alloy to near its phase transformation point. Considering the poor roundness of roll drawing, an eye die is used for sizing and rounding after roll drawing to ensure the roundness meets the requirements of subsequent wire processing. The large deformation roll drawing introduces dislocation distortion energy. Low-temperature, short-time solution treatment, under the action of high distortion energy, causes the material to rapidly recrystallize, forming numerous recrystallization nucleation sites, thus achieving uniform fine grain formation. The combined deformation mechanism of "hot drawing + cold drawing" with small deformation after solution treatment generates dislocations again, increasing the intragranular distortion energy. The subsequent aging process provides more precipitate nucleation sites, which is more conducive to the precipitation of secondary fine needle-like α-phase, dispersed throughout the matrix. This results in an alloy with high strength and high toughness. This combined roll drawing and solution treatment deformation mechanism results in wires with moderate strength and high plasticity, facilitating subsequent cold forming of alloy wire parts without the risk of deformation or cracking. Furthermore, the aging treatment imparts excellent high strength and high toughness to the parts. In this invention, the heating temperature is 700℃ in the roll drawing, solution treatment, and die sizing processes. This process temperature is slightly lower than the phase transformation point of this β-titanium alloy. Therefore, further microstructural analysis, such as... Figure 3 It can be seen that a small amount of primary α phase exists at the grain boundaries. During the heating and holding process of the alloy in multiple hot drawing and solution treatment, the primary α phase distributed at the grain boundaries can effectively suppress grain coarsening and also have a certain effect on enhancing the material properties.

[0066] It is important to note that the constructions and arrangements of this application shown in several different exemplary embodiments are merely illustrative. Although only a few embodiments are described in detail in this disclosure, those who consult this disclosure will readily understand that many modifications are possible (e.g., changes in the size, dimensions, structure, shape, and proportions of various elements, as well as parameter values ​​(e.g., temperature, pressure, etc.), mounting arrangements, use of materials, color, orientation, etc.) without substantially departing from the novel teachings and advantages of the subject matter described in this application). For example, an element shown as integrally formed may be composed of multiple parts or elements, the position of elements may be inverted or otherwise changed, and the nature or number or position of discrete elements may be altered or changed. Therefore, all such modifications are intended to be included within the scope of the invention. The order or sequence of any process or method steps may be changed or rearranged according to alternative embodiments. In the claims, any "device plus function" clause is intended to cover the structure described herein that performs the function, and not only structurally equivalent but also equivalent in structure. Other substitutions, modifications, alterations, and omissions may be made in the design, operation, and arrangement of the exemplary embodiments without departing from the scope of the invention. Therefore, the invention is not limited to the specific embodiments, but extends to various modifications that still fall within the scope of the appended claims. Furthermore, for the purpose of providing a concise description of exemplary embodiments, not all features of actual embodiments (i.e., those features not relevant to the currently considered best mode for carrying out the invention, or those features not relevant to implementing the invention) may be omitted.

[0067] It should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and are not intended to limit it. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can be made to the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, and all such modifications or substitutions should be covered within the scope of the claims of the present invention.

Claims

1. A method of producing a high-toughness β titanium alloy wire, characterized by: The application relates to a preparation method of a beta titanium alloy wire rod. A beta titanium alloy coil wire rod is provided; A multi-pass roller die hot drawing is performed on the coil wire rod to obtain a first intermediate wire rod; Eye die hot drawing is performed on the first intermediate wire rod to obtain a second intermediate wire rod; An online short-time solid solution treatment is performed on the second intermediate wire rod and the wire rod is cooled; Eye die hot drawing is performed on the wire rod after the solid solution treatment to obtain a third intermediate wire rod; Eye die cold drawing is performed on the third intermediate wire rod to obtain a beta titanium alloy wire rod with a final specification.

2. The method of producing a high-ductility β titanium alloy wire according to claim 1, characterized by: The pass deformation rate of the multi-pass roller die hot drawing is 15%-25%, and the heating temperature before drawing is lower than the phase transition point of the beta titanium alloy.

3. The method of making a high toughness beta titanium alloy wire of claim 1, wherein: The pass deformation rate of the eye die hot drawing is 10%-20%, and the heating temperature before drawing is lower than the phase transition point of the beta titanium alloy.

4. The method of making a high toughness beta titanium alloy wire of claim 1, wherein: The heating temperature of the online short-time solid solution treatment is lower than the phase transition point of the beta titanium alloy, and then water cooling is performed.

5. The method of making high toughness beta titanium alloy wire of claim 1, wherein: The pass deformation rate of the eye die hot drawing after the solid solution treatment is 10%-20%, and the heating temperature before drawing is lower than the phase transition point of the beta titanium alloy.

6. The method of producing a high-toughness β titanium alloy wire according to claim 5, characterized by: The pass deformation rate of the eye die cold drawing is 5%-10%.

7. The method of producing a high-ductility β titanium alloy wire according to any one of claims 2 to 5, characterized in that: The heating temperature lower than the phase transition point of the beta titanium alloy is 700 DEG C.

8. The method of making high toughness beta titanium alloy wire of claim 1, wherein: The components of the beta titanium alloy coil wire rod include Ti, Al, Mo, V, Cr, Zr and Sn.

9. The method of producing a high-ductility β titanium alloy wire according to claim 8, characterized by: The beta titanium alloy coil wire rod is Ti5Al5Mo5V3Cr1Zr1Sn alloy.

10. A high-toughness beta titanium alloy wire, characterized by, The wire rod is prepared by the preparation method in any one of claims 1-9.

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