Low-cost high-strength titanium-zirconium alloy wire and preparation method thereof

Abstract

The invention provides a preparation method of a low-cost high-strength titanium-zirconium alloy wire. The preparation method comprises the following steps: (1) vacuum consumable smelting; (2) primary heating number rolling; (3) secondary heating number rolling; (4) drawing; (5) straightening treatment; (6) annealing treatment; and (7) centerless grinding and polishing treatment are conducted, and the finished titanium-zirconium alloy wire is obtained. The invention further provides the low-cost and high-strength titanium-zirconium alloy wire which is prepared according to the preparation method of the low-cost and high-strength titanium-zirconium alloy wire. The tensile strength of the prepared Ti-Zr alloy wire is larger than or equal to 1010 MPa, the yield strength of the Ti-Zr alloy wire is larger than or equal to 890 MPa, the ductility of the Ti-Zr alloy wire is larger than or equal to 12.5%, and the mechanical property of the Ti-Zr alloy wire completely meets and is higher than the requirements in the standard GB / T 13810-2017; the multi-heating-number forging, the intermediate annealing procedure and the hot drawing procedure are omitted, the machining procedure is simplified, the production efficiency is improved, the machining cost is greatly saved, and the method is suitable for industrial mass production; belongs to the technical field of medical titanium-zirconium alloy wire preparation.

Description

Technical Field

[0001] This invention relates to the field of medical titanium-zirconium alloy wire preparation technology, and in particular to a low-cost, high-strength titanium-zirconium alloy wire and its preparation method. Background Technology

[0002] Titanium and titanium alloys are widely used in the medical device field due to their excellent properties such as low density, high specific strength, high temperature resistance, corrosion resistance, non-magnetic properties, and biocompatibility. However, the high cost of titanium limits its application, especially in the dental implant industry. Pure titanium, a widely used implant material, has low strength and poor wear resistance, increasing the risk of implant failure. In recent years, with the development of the medical and biomedical materials industry, titanium-zirconium alloys have gradually replaced pure titanium. However, domestically produced titanium-zirconium alloys currently suffer from poor strength-ductility matching, failing to meet the requirements of some medical device manufacturers and thus limiting their widespread application in the implant industry.

[0003] Currently, domestic research on low-cost titanium-zirconium alloy rods mainly focuses on traditional processing techniques. Patent CN120158647A discloses a method for preparing high-strength titanium-zirconium alloy wire, achieving Rm≥950MPa and A≥10%, thus addressing the issue of low strength in Ti-Zr alloy implant materials. However, its processing is cumbersome, requiring multiple forging, rolling, and hot drawing processes. This lengthy process results in significant material removal, low yield, and reduced production efficiency for titanium-zirconium alloy rods. Therefore, to ensure low-cost and high-performance implant materials and facilitate wider adoption of implants in civilian applications, it is crucial to explore a low-cost, high-strength titanium-zirconium alloy wire and its preparation method. Summary of the Invention

[0004] The purpose of this invention is to provide a low-cost, high-strength titanium-zirconium alloy wire and its preparation method, so as to solve the technical problems of cumbersome processing technology, lengthy procedures and low production efficiency in the existing preparation methods of titanium-zirconium alloy wire.

[0005] To achieve the above objectives, the technical solution adopted by the present invention is: to provide a method for preparing low-cost, high-strength titanium-zirconium alloy wire, comprising the following steps: (1) Titanium-zirconium alloy ingots were prepared by vacuum arc remelting; (2) A horizontal rolling mill is used to roll the titanium-zirconium alloy ingot in one pass at a temperature higher than the β phase transformation point. (3) Using a continuous rolling mill, the titanium-zirconium alloy ingot is rolled twice at a temperature below the α+β two-phase region temperature of the phase transformation point to obtain titanium-zirconium alloy wire. (4) The titanium-zirconium alloy wire is drawn using a disc wire drawing machine; (5) The drawn titanium-zirconium alloy wire is straightened using a slider straightening machine; (6) Anneal the straightened titanium-zirconium alloy wire; (7) The annealed titanium-zirconium alloy wire is subjected to centerless grinding and polishing to obtain the finished titanium-zirconium alloy wire.

[0006] Preferably, in step (1), the weight percentage content of each element in the titanium-zirconium alloy ingot is: Zr: 14-16%, Fe: 0-0.5%, O: 0-0.4%, C: 0-0.08%, N: 0-0.05%, H: 0-0.008%, with the balance being Ti.

[0007] Preferably, in step (1), sponge titanium, sponge zirconium and compound TiO2 with a particle size of 5 to 10.2 mm are used, and vacuum self-consumable melting is used to obtain titanium zirconium alloy ingots through three meltings.

[0008] Preferably, in step (2), during the first rolling, the rolling temperature is 1050-1150℃, the holding time is 2-5h, the number of rolling passes is 8-10, and the cumulative deformation is 50-80%.

[0009] Preferably, in step (3), during the second rolling, the pre-rolling temperature is 800-900℃, the holding time is 1-2h, the final rolling temperature is 750-820℃, the number of rolling passes is 5-7, and the cumulative deformation is 98.5-99.5%.

[0010] Preferably, in step (4), at room temperature, the speed of the disc wire drawing machine is controlled to be 1-2 m / min, and the cumulative deformation is 50-60%.

[0011] Preferably, in step (5), the straightening speed during the straightening process is 1 to 2 m / s.

[0012] Preferably, in step (6), a benchtop resistance furnace is used for annealing, with a stress-relief annealing temperature of 350-550°C and a holding time of 2-4 hours.

[0013] Preferably, in step (7), the centerless grinding amount is less than 0.03 mm each time.

[0014] The present invention also provides a low-cost, high-strength titanium-zirconium alloy wire, which is prepared according to the preparation method of the low-cost, high-strength titanium-zirconium alloy wire described in any of the above claims.

[0015] This invention provides a low-cost, high-strength titanium-zirconium alloy wire and its preparation method. Compared with the prior art, this invention has the following advantages: (1) The present invention first performs large deformation rolling (single-fire rolling) above the β phase transformation point. The high plasticity of the β phase region and the violent deformation induce dynamic recrystallization, which completely breaks the initial coarse grains and obtains fine equiaxed β grains, laying the foundation for fine grains and eliminating defects. Then, extreme deformation rolling (two-fire rolling) is performed in the α+β two-phase region below the phase transformation point. At this temperature, the metastable β phase is dominant and has excellent plasticity. During the ultra-large deformation process, a high dislocation density is introduced and a fine substructure is formed. At the same time, the precipitation of excessive brittle phase is suppressed, thereby obtaining a wire with both high strength and excellent plasticity. After the two-fire rolling, a specific structure with fine metastable β phase, high dislocation density, uniformity and no defects is formed, which provides a key guarantee for subsequent cold deformation and avoids shrinkage and fracture. Finally, drawing is performed at room temperature. The large cold deformation generated by drawing produces strong work hardening through the sharp increase in dislocation density and the extreme refinement of grains / subgrains, achieving a further significant leap in strength. The entire preparation process combines the most simplified two-stage hot rolling with large cold deformation. By controlling the phase state, deformation mechanism (dynamic recrystallization, dislocation strengthening) and microstructure characteristics (fine grains, metastable phases, high dislocations) in stages, the hot working microstructure and cold deformation are synergistically optimized, ultimately achieving a high balance between strength and plasticity.

[0016] (2) This invention produces wire by extreme deformation rolling (two-stage rolling) in the α+β two-phase region below the phase transformation point, and controls the final rolling temperature to be lower than the pre-rolling temperature, thus retaining more metastable β phase, which lays the foundation for subsequent large cold deformation through fine grain strengthening mechanism to improve strength and maintain plasticity.

[0017] (3) The two-stage rolling process of the present invention changes the grain structure and ensures that there are no defects such as pores. It improves both strength and plasticity. The prepared Ti-Zr alloy wire has a tensile strength ≥1010MPa, a yield strength ≥890MPa, and an elongation ≥12.5%. Its mechanical properties fully meet and exceed the requirements of standard GB / T 13810-2017.

[0018] (4) The present invention first obtains wire by smelting, one-time rolling and two-time rolling, and then obtains finished wire by room temperature continuous cold deformation drawing, straightening, stress relief annealing and centerless grinding. It omits the multi-time forging and intermediate annealing process and hot drawing process, simplifies the processing process, improves production efficiency, greatly saves processing costs, and is suitable for industrial mass production. Attached Figure Description

[0019] To more clearly illustrate the technical solutions in the embodiments of this application, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this application. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0020] Figure 1 This is a metallographic image of the finished Ti-Zr alloy wire prepared in Example 1 of this application; Figure 2 The image shows the metallographic structure of the finished Ti-Zr alloy wire prepared in Example 2 of this application. Figure 3 This is a metallographic diagram of the finished Ti-Zr alloy wire prepared in Example 3 of this application. Detailed Implementation

[0021] To make the technical problems, technical solutions, and beneficial effects to be solved by this application clearer, the following detailed description is provided in conjunction with embodiments. It should be understood that the specific embodiments described herein are merely illustrative of this application and are not intended to limit this application. Unless otherwise specified, the methods used in this invention are conventional methods; the raw materials and apparatus used, unless otherwise specified, are conventional commercially available products.

[0022] To verify the reliability of the effectiveness of the present invention, the present invention will be described below with reference to Examples 1 to 3, and compared with Comparative Examples 1 to 2.

[0023] Example 1 This embodiment provides a method for preparing low-cost, high-strength titanium-zirconium alloy wire, including the following steps: (1) Using sponge titanium, sponge zirconium and compound TiO2 with a particle size of 5 to 10.2 mm, the alloy composition is prepared according to the following composition, and vacuum self-consumable melting is used to obtain a Ti-Zr alloy ingot with stable and uniform composition after three meltings. The chemical composition and mass percentage of the Ti-Zr alloy ingot are as follows: Zr 14.5%, Fe 0.06%, C 0.04%, H 0.006%, O 0.28%, N 0.02%, and the balance is Ti.

[0024] (2) Using a horizontal rolling mill, the Ti-Zr alloy ingot is rolled in one pass (bill rolling) at 1050℃ for 3 hours. The rolling passes are 9 times and the cumulative deformation is controlled at 75%.

[0025] (3) A continuous rolling mill was used. The temperature before rolling was 830℃. The Ti-Zr alloy ingot was held at 830℃ for 1 hour and then rolled for the second time. The final rolling temperature was 750℃ and the number of rolling passes was 6. The cumulative deformation was controlled at 99.5% to obtain Ti-Zr alloy wire.

[0026] (4) At room temperature, Ti-Zr alloy wire is drawn using a disc wire drawing machine at a drawing speed of 2.0 m / min. The deformation per pass is controlled at 12%, and the cumulative deformation is controlled at 50-60%.

[0027] (5) The Ti-Zr alloy wire after drawing is straightened by a slider straightening machine, and the straightening speed is controlled at 1.2m / s.

[0028] (6) The straightened Ti-Zr alloy wire was annealed using a tabletop resistance furnace. The stress-relieving annealing temperature was 380℃ and the holding time was 2h.

[0029] (7) The annealed Ti-Zr alloy wire is ground by a centerless mill with a grinding amount of 0.02 mm each time. Then the surface of the Ti-Zr alloy wire is polished to obtain a finished Ti-Zr alloy wire with a diameter of 6.0 mm.

[0030] Example 2 This embodiment provides a method for preparing low-cost, high-strength titanium-zirconium alloy wire, including the following steps: (1) Using sponge titanium, sponge zirconium and compound TiO2 with a particle size of 5 to 10.2 mm, the alloy composition is prepared according to the following composition, and vacuum self-consumable melting is used to obtain a Ti-Zr alloy ingot with stable and uniform composition after three meltings. The chemical composition and mass percentage of the Ti-Zr alloy ingot are as follows: Zr 15.1%, Fe 0.08%, C 0.05%, H 0.005%, O 0.35%, N 0.03%, and the balance is Ti.

[0031] (2) Using a horizontal rolling mill, the Ti-Zr alloy ingot is rolled in one pass (bill rolling) at 1100℃ for 3 hours. The rolling passes are 9 times and the cumulative deformation is controlled at 75%.

[0032] (3) A continuous rolling mill was used. The temperature before rolling was 860℃. The Ti-Zr alloy ingot was held at 860℃ for 1 hour and then rolled for the second time. The final rolling temperature was 800℃ and the number of rolling passes was 6. The cumulative deformation was controlled at 99.5% to obtain Ti-Zr alloy wire.

[0033] (4) At room temperature, Ti-Zr alloy wire is drawn using a disc wire drawing machine at a drawing speed of 1.5 m / min, with the deformation per pass controlled at 15% and the cumulative deformation controlled at 50-60%.

[0034] (5) The Ti-Zr alloy wire after drawing is straightened by a slider straightening machine, and the straightening speed is controlled at 1.5m / s.

[0035] (6) The straightened Ti-Zr alloy wire was annealed using a tabletop resistance furnace. The stress-relieving annealing temperature was 420℃ and the holding time was 2h.

[0036] (7) The annealed Ti-Zr alloy wire is ground by a centerless mill with a grinding amount of 0.02 mm each time. Then the surface of the Ti-Zr alloy wire is polished to obtain a finished Ti-Zr alloy wire with a diameter of 6.0 mm.

[0037] Example 3 This embodiment provides a method for preparing low-cost, high-strength titanium-zirconium alloy wire, including the following steps: (1) Using sponge titanium, sponge zirconium and compound TiO2 with a particle size of 5 to 10.2 mm, the alloy composition is prepared according to the following composition, and vacuum self-consumable melting is used to obtain a Ti-Zr alloy ingot with stable and uniform composition after three meltings. The chemical composition and mass percentage of the Ti-Zr alloy ingot are as follows: Zr 15.9%, Fe 0.07%, C 0.03%, H 0.002%, O 0.40%, N 0.03%, and the balance is Ti.

[0038] (2) Using a horizontal rolling mill, the Ti-Zr alloy ingot is rolled in one pass (bill rolling) at 1150℃ for 3 hours. The rolling passes are 9 times and the cumulative deformation is controlled at 75%.

[0039] (3) A continuous rolling mill was used. The temperature before rolling was 900℃. The Ti-Zr alloy ingot was held at 900℃ for 1 hour and then rolled for the second time. The final rolling temperature was 820℃ and the number of rolling passes was 6. The cumulative deformation was controlled at 99.5% to obtain Ti-Zr alloy wire.

[0040] (4) At room temperature, Ti-Zr alloy wire is drawn using a disc wire drawing machine at a drawing speed of 1.0 m / min, with the deformation per pass controlled at 18% and the cumulative deformation controlled at 50-60%.

[0041] (5) The Ti-Zr alloy wire after drawing is straightened by a slider straightening machine, and the straightening speed is controlled at 1.8m / s.

[0042] (6) The straightened Ti-Zr alloy wire was annealed using a tabletop resistance furnace. The stress-relieving annealing temperature was 530℃ and the holding time was 3h.

[0043] (7) The annealed Ti-Zr alloy wire is ground by a centerless mill with a grinding amount of 0.01 mm each time. Then the surface of the Ti-Zr alloy wire is polished to obtain a finished Ti-Zr alloy wire with a diameter of 6.0 mm.

[0044] Comparative Example 1 The difference between this implementation method and Example 1 is that in step (3), the pre-rolling temperature and the final rolling temperature are both 830℃. The Ti-Zr alloy ingot is held at 830℃ for 1 hour and then subjected to a second rolling process. The number of rolling passes is 6, and the cumulative deformation is controlled at 99.5% to obtain Ti-Zr alloy wire. The remaining operations are the same, and finally, a finished Ti-Zr alloy wire with a diameter of 6.0mm is obtained.

[0045] Comparative Example 2 The difference between this implementation method and Example 1 is that in step (2), a fast forging machine is first used to hold the temperature at 1000℃ for 4 hours for billet forging, and then a precision forging machine is used to hold the temperature at 800℃ for 3 hours for forging. The deformation amount per forging is controlled at 60%. In step (3), a horizontal rolling mill is used for rolling, the rolling temperature is controlled at 780℃, and the temperature is held for 1.5 hours. The deformation amount per pass is controlled at 8%. The remaining operations are the same, and finally, a Φ6.0mm finished Ti-Zr alloy wire is obtained.

[0046] It should be noted that in the above embodiments 1 to 3, in step (1), the weight percentage content of each element in the titanium-zirconium alloy ingot is as follows: Zr: 14-16%, Fe: 0-0.5%, O: 0-0.4%, C: 0-0.08%, N: 0-0.05%, H: 0-0.008%, with the balance being Ti; sponge titanium, sponge zirconium, and compound TiO2 with a particle size of 5-10.2 mm are used as raw materials. In step (2), during the first rolling, the rolling temperature is 1050-1150℃, the holding time is 2-5h, the number of rolling passes is 8-10, and the cumulative deformation is 50-80%. In step (3), during the second rolling, the pre-rolling temperature is 800-900℃, the holding time is 1-2h, the final rolling temperature is 750-820℃, the number of rolling passes is 5-7, and the cumulative deformation is 98.5-99.5%. In step (4), the speed of the disc wire drawing machine is controlled at 1-2 m / min, and the deformation is 50-60%. In step (5), the straightening speed during the straightening process is 1-2 m / s. In step (6), the annealing temperature is 350-550℃, and the holding time is 2-4 h. In step (7), the centerless grinding amount per pass is less than 0.03 mm. As long as the above parameters are within the specified range, they can be adjusted according to the specific circumstances in actual production.

[0047] The finished Ti-Zr alloy wires prepared in Examples 1-3 were tested, and their metallographic structures were obtained as follows: Figures 1-3 As shown. From Figures 1-3 As can be seen, while introducing solid solution strengthening and grain refinement strengthening, the axial ratio of the α phase was increased, which promoted the cone slip and successfully obtained Ti-Zr alloy wire with ultrafine grain structure.

[0048] To verify the effectiveness of the present invention, the mechanical properties of the finished Ti-Zr alloy wires of Examples 1-3 and Comparative Examples 1-2 were tested below. The testing methods were carried out in accordance with the provisions of GB / T 13810-2017 "Titanium and Titanium Alloy Processed Materials for Surgical Implants". The test results of the mechanical properties of the finished Ti-Zr alloy wires of Examples 1-3 and Comparative Examples 1-2 are shown in Table 1.

[0049] Table 1. Test results of mechanical properties of finished Ti-Zr alloy wire

[0050] As shown in Table 1: Comparing Examples 1 to 3, it can be seen that the preparation process of Examples 1 to 3 of the present invention can produce Ti-Zr alloy wires with stable mechanical properties, Rm of 1014 to 1034 MPa, Rp0.2 of 891 to 940 MPa, and A of 12.5 to 15.0%, which fully meet and exceed the mechanical property requirements in standard GB / T 13810-2017. Therefore, it can be seen that the finished Ti-Zr alloy wires prepared by the present invention have excellent plasticity and strength.

[0051] Comparing Examples 1-3 with Comparative Example 1, it can be seen that the tensile strength and yield strength of the finished Ti-Zr alloy wire prepared in Comparative Example 1 are both lower than those in Examples 1-3. Therefore, it can be seen that the present invention, by performing extreme deformation rolling (two-stage rolling) in the α+β two-phase region below the phase transformation point to form wire, and controlling the final rolling temperature to be lower than the pre-rolling temperature, retains more metastable β phase, laying the foundation for subsequent large cold deformation through fine grain strengthening mechanism to improve strength and maintain plasticity.

[0052] Comparing Examples 1-3 with Comparative Example 2, it can be seen that the tensile strength and yield strength of the finished Ti-Zr alloy wire prepared in Comparative Example 2 are both lower than those in Examples 1-3. This shows that the two-stage rolling process of the present invention changes the grain structure and ensures the absence of defects such as pores, thereby improving both strength and plasticity. In addition, the present invention omits the multi-stage forging, intermediate annealing, and hot drawing processes, simplifying the processing steps, improving production efficiency, and greatly saving processing costs, making it suitable for large-scale industrial production.

[0053] Therefore, this invention enables the production of low-cost, high-strength titanium-zirconium alloy wire for dental use, providing qualified raw materials for dental implant products while reducing usage costs, promoting the market share of domestically produced implants, and making them affordable products for the general public.

[0054] In summary, this invention provides a low-cost, high-strength titanium-zirconium alloy wire and its preparation method. Compared with the prior art: (1) This invention first performs large deformation rolling (single-fire rolling) above the β phase transformation point, utilizing the high plasticity of the β phase region and the violent deformation to induce dynamic recrystallization, thoroughly breaking the initial coarse grains, obtaining fine equiaxed β grains, laying the foundation for fine grains and eliminating defects; then, it performs extreme deformation rolling (two-fire rolling) in the α+β two-phase region below the phase transformation point. At this temperature, the metastable β phase dominates and has excellent plasticity, making it suitable for ultra-large deformation rolling. The deformation process introduces high dislocation density and forms a fine substructure, while suppressing excessive precipitation of brittle phases, thus obtaining a wire with both high strength and excellent plasticity. After two hot rolling processes, a specific microstructure is formed, characterized by fine metastable β phases, high dislocation density, and uniformity without defects, providing crucial support for subsequent cold deformation and preventing shrinkage cavities and fractures. Finally, drawing is performed at room temperature. The large amount of cold deformation generated by drawing leads to strong work hardening through a sharp increase in dislocation density and extreme grain / subgrain refinement, achieving a further significant leap in strength. The entire preparation process combines a simplified two-hot rolling process with large cold deformation. By controlling the phase state, deformation mechanism (dynamic recrystallization, dislocation strengthening), and microstructure characteristics (fine grains, metastable phases, high dislocation density) in stages, the hot working microstructure and cold deformation are synergistically optimized, ultimately achieving a high balance between strength and plasticity. (2) This invention produces wire by extreme deformation rolling (two-stage rolling) in the α+β two-phase region below the phase transformation point, controlling the final rolling temperature to be lower than the pre-rolling temperature, thus retaining more metastable β phase, laying the foundation for subsequent large cold deformation through fine grain strengthening mechanism to improve strength and maintain plasticity. (3) The two-stage rolling of this invention changes the grain structure and ensures the absence of defects such as pores, improving both strength and plasticity. The prepared Ti-Zr alloy wire has a tensile strength ≥1010MPa, a yield strength ≥890MPa, and an elongation ≥12.5%, and its mechanical properties fully meet and exceed the requirements of standard GB / T 13810-2017. (4) This invention first obtains wire through smelting, single-fire rolling, and double-fire rolling. Then, it obtains finished wire through continuous room temperature cold deformation drawing, straightening, stress-relief annealing, and centerless grinding. This process omits multi-fire forging, intermediate annealing, and hot drawing, simplifying the processing steps, improving production efficiency, and greatly saving processing costs. It is suitable for large-scale industrial production. This invention can be widely applied in the field of medical titanium-zirconium alloy wire preparation technology.

[0055] The above-described embodiments are only used to illustrate the technical solutions of this application, and are not intended to limit them. Although this application 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 of the technical features. Such modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the spirit and scope of the technical solutions of the embodiments of this application, and should all be included within the protection scope of this application.

Claims

1. A method for preparing low-cost, high-strength titanium-zirconium alloy wire, characterized in that, Includes the following steps: (1) Titanium-zirconium alloy ingots were prepared by vacuum arc remelting; (2) A horizontal rolling mill is used to roll the titanium-zirconium alloy ingot in one pass at a temperature higher than the β phase transformation point. (3) Using a continuous rolling mill, the titanium-zirconium alloy ingot is rolled twice at a temperature below the α+β two-phase region temperature of the phase transformation point to obtain titanium-zirconium alloy wire. (4) The titanium-zirconium alloy wire is drawn using a disc wire drawing machine; (5) The drawn titanium-zirconium alloy wire is straightened using a slider straightening machine; (6) Anneal the straightened titanium-zirconium alloy wire; (7) The annealed titanium-zirconium alloy wire is subjected to centerless grinding and polishing to obtain the finished titanium-zirconium alloy wire.

2. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (1), the weight percentage content of each element in the titanium-zirconium alloy ingot is as follows: Zr: 14-16%, Fe: 0-0.5%, O: 0-0.4%, C: 0-0.08%, N: 0-0.05%, H: 0-0.008%, with the balance being Ti.

3. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 2, characterized in that, In step (1), sponge titanium, sponge zirconium and compound TiO2 with a particle size of 5 to 10.2 mm are used, and vacuum self-consumable melting is carried out three times to obtain titanium zirconium alloy ingots.

4. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (2), during the first rolling, the rolling temperature is 1050-1150℃, the holding time is 2-5h, the number of rolling passes is 8-10, and the cumulative deformation is 50-80%.

5. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (3), during the second rolling, the pre-rolling temperature is 800-900℃, the holding time is 1-2h, the final rolling temperature is 750-820℃, the number of rolling passes is 5-7, and the cumulative deformation is 98.5-99.5%.

6. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (4), at room temperature, the speed of the disc wire drawing machine is controlled at 1 to 2 m / min, and the cumulative deformation is 50 to 60%.

7. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (5), the straightening speed during the straightening process is 1 to 2 m / s.

8. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (6), a benchtop resistance furnace is used for annealing. The stress-relief annealing temperature is 350-550℃, and the holding time is 2-4 hours.

9. The method for preparing low-cost, high-strength titanium-zirconium alloy wire according to claim 1, characterized in that, In step (7), the centerless grinding amount is less than 0.03 mm each time.

10. A low-cost, high-strength titanium-zirconium alloy wire, characterized in that, It is prepared by the method for preparing low-cost, high-strength titanium-zirconium alloy wire according to any one of claims 1-9.

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