Titanium alloy wire drawing preparation method and titanium alloy wire

Abstract

The application discloses a titanium alloy wire drawing preparation method, comprising the following steps: peeling and polishing titanium alloy disc round; carrying out multi-stage multi-pass roller die cold drawing on the titanium alloy disc round after peeling and polishing; when the cumulative deformation of each stage of multi-stage multi-pass roller die cold drawing reaches a preset value, according to the specification of the current stage wire, different annealing temperatures and holding time are adopted for online annealing treatment, and then the next stage of multi-stage multi-pass roller die cold drawing is carried out. The scheme provided by the application constructs a ternary precise correspondence composed of "deformation energy storage", "ladder annealing temperature" and "coordinated holding time", realizes precise regulation and control of grain refinement in the recrystallization process, and ensures the uniformity of the structure and the stability of the performance in the whole process from thick wire to thin wire.

Description

Technical Field

[0001] This invention relates to the field of alloys, and specifically to a method for preparing titanium alloy wire by drawing and titanium alloy wire. Background Technology

[0002] TB13 titanium alloy (Ti-4Al-22V) is a metastable β-type titanium alloy with excellent elasticity and cold forming properties in the solution-treated state, making it particularly suitable for manufacturing lightweight and complex eyeglass frames. In the actual production of eyeglass frames, components such as the bridge and temples often require complex cold working processes including bending, stamping, and riveting, which places extremely high demands on the plasticity of the titanium alloy wire. Insufficient plasticity of the wire can easily lead to defects such as cracking and peeling during subsequent processing, resulting in low product yield.

[0003] The solid-solution TB13 titanium alloy wire exhibits a single equiaxed β-grain structure at room temperature, with an α-grain content of less than 1%. Unlike duplex titanium alloys, its properties cannot be optimized by adjusting the morphology or ratio of the α and β phases. Therefore, grain refinement has become the primary means of improving the plasticity of this β-titanium alloy. However, the single-phase β grains of TB13 titanium alloy are extremely sensitive to heat treatment temperature. During annealing, the grains tend to grow rapidly. Since the wire used for eyeglass frames has a relatively small diameter (typically ≤ φ3.0 mm), it is heated to the required temperature quickly during heat treatment. Traditional annealing processes have a wide annealing window and are poorly controlled, which easily leads to rapid grain coarsening after complete recrystallization. As a result, instead of effectively improving plasticity, grain growth causes a sharp decrease in both plasticity (especially the ability to undergo uniform plastic deformation) and strength, contradicting the original intention of the process design.

[0004] Currently, the conventional processes for preparing TB13 titanium alloy wire in the industry mostly employ "hot working + intermediate annealing" or "cold drawing + single high-temperature annealing". These traditional processes have the following limitations: ① Hot working makes it difficult to accumulate sufficient deformation energy, resulting in insufficient recrystallization nucleation points during subsequent annealing, thus failing to achieve grain refinement. ② Using a fixed high-temperature annealing process leads to an excessively narrow holding time adjustment window, making precise matching of temperature and time extremely difficult. This can easily cause rapid grain coagulation and coarsening, resulting in a dual deterioration of plasticity and strength.

[0005] The existing technology lacks a precise control process that can specifically target TB13 titanium alloy eyeglass frame wire, especially to overcome its tendency to coarsen single-phase β grains and achieve a perfect match between significant grain refinement and high plasticity. Summary of the Invention

[0006] In view of this, in order to overcome at least one aspect of the above problems, embodiments of the present invention provide a method for preparing titanium alloy wire by drawing, comprising the following steps: Peeling and polishing of titanium alloy discs; After peeling and polishing, the titanium alloy coils are subjected to multi-stage, multi-pass cold drawing with roller dies. When the cumulative deformation of each stage of multi-pass cold drawing with roller dies reaches the preset value, online annealing is performed according to the specifications of the wire at the current stage, using different annealing temperatures and holding times. Then, the next stage of multi-pass cold drawing with roller dies is carried out. As the specifications of the wire decrease, the annealing temperature gradually decreases.

[0007] In some embodiments, online annealing is performed using different annealing temperatures and holding times according to the specifications of the filament at the current stage, further including: When the wire specifications are in the range of φ5.0mm~φ6.5mm, the annealing temperature is 800℃~820℃, and the holding time is 4~7 minutes; When the wire specifications are in the range of φ3.5mm~φ5.0mm, the annealing temperature is 770℃~800℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ2.0mm~φ3.5mm, the annealing temperature is 750℃~780℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ1.4mm to φ2.0mm, the annealing temperature is 730℃ to 760℃, and the holding time is 2 to 4 minutes.

[0008] In some embodiments, the method further includes: The drawing speed of the multi-pass cold drawing at each stage is controlled between 0.8 and 3.6 m / s, and the drawing speed increases as the size of the obtained wire decreases.

[0009] In some embodiments, the method further includes: The diameter reduction of a single drawing pass in each stage is controlled within 0.2~0.5mm, and the diameter reduction decreases as the specification decreases.

[0010] In some embodiments, after the cumulative deformation of the multi-pass cold drawing at each stage reaches a preset value, online annealing is performed according to the specifications of the wire at the current stage, using different annealing temperatures and holding times, further including: When the cumulative deformation of the multi-pass cold drawing of each stage reaches 43%~62%, online annealing is carried out using different annealing temperatures and holding times.

[0011] In some embodiments, online annealing is performed using different annealing temperatures and holding times, further including: Annealing was performed in an online annealing furnace with argon atmosphere protection and followed by air cooling.

[0012] In some embodiments, the titanium alloy disc, after being peeled and polished, undergoes multi-stage, multi-pass roll cold drawing, further comprising: The first wire of the first specification is obtained by cold drawing the titanium alloy coil through multiple passes of roller drawing, and the first wire is then subjected to online annealing treatment. The first wire is cold-drawn by multiple passes of roller drawing to obtain a second wire of the second specification, and the second wire is then subjected to online annealing. The second filament is subjected to multiple passes of cold drawing with rollers to obtain a third filament of a third specification, and the third filament is subjected to online annealing. The third filament is subjected to multiple passes of cold drawing on a roller to obtain a finished filament, and the finished filament is then subjected to online annealing.

[0013] In some embodiments, the method further includes: The annealed wire was mechanically polished to a diameter of φ1.80±0.01mm.

[0014] In some embodiments, the method further includes: A multi-level polishing wheel is used, with 320 mesh, 600 mesh and 800 mesh mesh used sequentially to polish from coarse to fine until the surface of the wire material achieves a uniform mirror finish. Use a neutral or weakly alkaline water-based cleaning agent to perform ultrasonic cleaning on the polished wire material at a temperature of 40℃~60℃.

[0015] Based on the same inventive concept, according to another aspect of the present invention, embodiments of the present invention also provide a titanium alloy wire, said titanium alloy wire being prepared by the method described in any of the above embodiments.

[0016] The present invention has one of the following beneficial technical effects: The solution proposed in this invention constructs a ternary precise correspondence consisting of "deformation energy storage (43%~62% deformation amount)", "stepped annealing temperature (based on specifications)" and "synergistic holding time (based on temperature)", which realizes precise control of grain refinement in the recrystallization process and ensures the uniformity of structure and performance stability of the entire process from coarse filament to fine filament. Attached Figure Description

[0017] 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 only some embodiments of the present invention. For those skilled in the art, other embodiments can be obtained based on these drawings without creative effort.

[0018] Figure 1A schematic flowchart of a method for preparing titanium alloy wire by drawing, provided for an embodiment of the present invention; Figure 2 The room temperature tensile properties of the 1.80 mm TB13 wire prepared in Example 1; Figure 3 The figures show cross-sectional metallographic images of the TB13 wires prepared according to the specifications of Example 1, Comparative Example 1, Example 2, and Comparative Example 2; wherein, Figure A is the metallographic structure of the wire of Example 1 at 500x magnification; Figure B is the metallographic structure of the wire of Comparative Example 1 at 500x magnification; Figure C is the metallographic structure of the wire of Example 2 at 500x magnification; and Figure D is the metallographic structure of the wire of Comparative Example 2 at 500x magnification. Figure 4 The room temperature tensile properties of TB13 wire with a diameter of φ1.80mm prepared for Comparative Example 1; Figure 5 The room temperature tensile properties of the 2.0 mm diameter TB13 wire prepared in Example 2; Figure 6 The room temperature tensile properties of the 2.0 mm diameter TB13 wire prepared for Comparative Example 2; Figure 7 Metallographic images of the surface quality and polished cross-section of TB13 wire in Comparative Example 3; Figure A is a low-magnification image of the surface of the finished wire in Comparative Example 3; Figure B is a 100x metallographic image of the cross section; and Figure C is a 200x magnified image of the crack defect in Figure B.

[0019] Figure 8 This is a schematic diagram of a qualified TB13 wire coil. Detailed Implementation

[0020] To make the objectives, technical solutions, and advantages of the present invention clearer, the embodiments of the present invention will be further described in detail below with reference to specific examples and the accompanying drawings.

[0021] It should be noted that all uses of "first" and "second" in the embodiments of the present invention are for the purpose of distinguishing two entities or parameters with the same name but different names. It is clear that "first" and "second" are only for the convenience of expression and should not be construed as limiting the embodiments of the present invention. Subsequent embodiments will not explain this in detail.

[0022] According to one aspect of the present invention, embodiments of the present invention provide a method for preparing titanium alloy wire by drawing, such as... Figure 1 As shown, it may include the following steps: S1, peeling and polishing the titanium alloy disc; S2 involves performing multi-stage, multi-pass cold drawing of titanium alloy coils after peeling and polishing. When the cumulative deformation of each stage of multi-pass cold drawing reaches a preset value, online annealing is performed using different annealing temperatures and holding times based on the specifications of the wire at the current stage. Then, the next stage of multi-pass cold drawing is performed. As the specifications of the wire decrease, the annealing temperature gradually decreases.

[0023] In some embodiments, online annealing is performed using different annealing temperatures and holding times according to the specifications of the filament at the current stage, further including: When the wire specifications are in the range of φ5.0mm~φ6.5mm, the annealing temperature is 800℃~820℃, and the holding time is 4~7 minutes; When the wire specifications are in the range of φ3.5mm~φ5.0mm, the annealing temperature is 770℃~800℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ2.0mm~φ3.5mm, the annealing temperature is 750℃~780℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ1.4mm to φ2.0mm, the annealing temperature is 730℃ to 760℃, and the holding time is 2 to 4 minutes.

[0024] In some embodiments, the method further includes: The drawing speed of the multi-pass cold drawing at each stage is controlled between 0.8 and 3.6 m / s, and the drawing speed increases as the size of the obtained wire decreases.

[0025] In some embodiments, the method further includes: The diameter reduction of a single drawing pass in each stage is controlled within 0.2~0.5mm, and the diameter reduction decreases as the specification decreases.

[0026] In some embodiments, after the cumulative deformation of the multi-pass cold drawing at each stage reaches a preset value, online annealing is performed according to the specifications of the wire at the current stage, using different annealing temperatures and holding times, further including: When the cumulative deformation of the multi-pass cold drawing of each stage reaches 43%~62%, online annealing is carried out using different annealing temperatures and holding times.

[0027] In some embodiments, online annealing is performed using different annealing temperatures and holding times, further including: Annealing was performed in an online annealing furnace with argon atmosphere protection and followed by air cooling.

[0028] In some embodiments, the titanium alloy disc, after being peeled and polished, undergoes multi-stage, multi-pass roll cold drawing, further comprising: The first wire of the first specification is obtained by cold drawing the titanium alloy coil through multiple passes of roller drawing, and the first wire is then subjected to online annealing treatment. The first wire is cold-drawn by multiple passes of roller drawing to obtain a second wire of the second specification, and the second wire is then subjected to online annealing. The second filament is subjected to multiple passes of cold drawing with rollers to obtain a third filament of a third specification, and the third filament is subjected to online annealing. The third filament is subjected to multiple passes of cold drawing on a roller to obtain a finished filament, and the finished filament is then subjected to online annealing.

[0029] In some embodiments, the method further includes: The annealed wire was mechanically polished to a diameter of φ1.80±0.01mm.

[0030] In some embodiments, the method further includes: A multi-level polishing wheel is used, with 320 mesh, 600 mesh and 800 mesh mesh used sequentially to polish from coarse to fine until the surface of the wire material achieves a uniform mirror finish. Use a neutral or weakly alkaline water-based cleaning agent to perform ultrasonic cleaning on the polished wire material at a temperature of 40℃~60℃.

[0031] Specifically, the initial raw material can be a solution-treated TB13 titanium alloy disc after peeling, with the following composition (wt%): Al: 4.0~4.3, V: 22.5~23.0, Mo: 0.2~1.0, O < 0.10, Fe < 0.10, and other impurity elements < 0.30. The disc size can be φ8.0mm, the phase transformation point is 730℃, the microstructure is a uniform single β equiaxed structure, and the average grain size is 35~50μm. Then, the wire is subjected to multi-stage drawing and stepped online annealing. Specifically, the raw wire coil is cold-drawn in multiple passes using a water-soluble lubricant. The drawing speed is controlled between 0.8 and 3.6 m / s, increasing with decreasing gauge size. Each pass reduces the diameter by 0.2 to 0.5 mm, decreasing with decreasing gauge size. When the cumulative deformation of a rolling pass reaches 43% to 62%, annealing is performed in an online annealing furnace with argon atmosphere protection, followed by air cooling. The heating temperature is 730 to 820℃, and the holding time is 2 to 5 minutes. After heat treatment, the wire surface is cleaned and polished before the next rolling pass, and so on.

[0032] Different online annealing processes were applied to TB13 titanium alloy wires in different diameter ranges, specifically including: When the wire specifications are in the range of φ5.0mm~φ6.5mm, the annealing temperature is 800℃~820℃, and the holding time is 4~7 minutes.

[0033] When the wire specifications are in the range of φ3.5mm~φ5.0mm, the annealing temperature is 770℃~800℃ and the holding time is 3~5 minutes.

[0034] When the wire specifications are in the range of φ2.0mm~φ3.5mm, the annealing temperature is 750℃~780℃ and the holding time is 3~5 minutes.

[0035] When the wire specifications are in the range of φ1.4mm~φ2.0mm, the annealing temperature is 730℃~760℃, and the holding time is 2~4 minutes.

[0036] Preferably, before the wire enters the annealing process of any of the above-mentioned specification ranges, its cumulative deformation should be controlled within the range of 43% to 62%.

[0037] Preferably, all annealing temperatures are strictly controlled above the β-phase transformation point (730°C) of TB13 titanium alloy to ensure that the microstructure is a single β-phase and to avoid the precipitation of harmful α-phase.

[0038] Finally, the annealed filaments were mechanically polished multiple times using a flap wheel or belt polisher. A neutral or weakly alkaline water-based cleaning agent was then used, followed by ultrasonic online cleaning to remove residual oil from the surface. After cleaning, the filaments were rinsed with water, dried, and then wound up.

[0039] The proposed solution constructs a ternary precise correspondence consisting of "deformation energy storage (43%~62% deformation amount)", "stepped annealing temperature (based on specifications)" and "synergistic holding time (based on temperature)", which realizes precise control of grain refinement in the recrystallization process and ensures the uniformity of structure and performance stability of the entire process from coarse filament to fine filament.

[0040] Moreover, the online annealing furnace is used for heat treatment, which ensures good wire straightness and eliminates the need for subsequent straightening, thus avoiding surface damage. At the same time, there is no oxide scale under argon protection, and there is no need for acid washing or mechanical peeling before finishing. High-quality finished products are obtained directly through cleaning and multi-stage polishing, which simplifies the production process and improves the yield and surface quality.

[0041] Through the above-mentioned step annealing and deformation control based on specifications, the prepared wire with a specification of ≤φ2.0mm can obtain a full β-phase ultrafine grain structure with an average grain size of ≤10μm, and its room temperature elongation after fracture (A) is high. 100mmStability ≥13%, tensile strength ≥780MPa, meeting the stringent processing requirements of high-end eyeglass frames.

[0042] Example 1: (1) Raw material selection: 8.0mm diameter TB13 titanium alloy discs in solid solution state were selected after peeling. The composition was Al: 4.28wt%, V: 22.92wt%, O: 0.088wt%, Fe: 0.050wt%, Mo: 0.35wt%, with the balance being Ti and other impurities. The phase transformation point of the discs was 730℃, and they had a uniformly distributed β equiaxed structure with an average grain size of approximately 38μm.

[0043] (2) Multi-stage drawing and stepped online annealing: The coil from step 1 was drawn in multiple passes using a roller die to reduce its diameter to φ5.5mm, with a deformation of 52.73% and a diameter reduction of 0.5mm per pass. The drawing speed was controlled at 0.8~1.5m / s. Subsequently, the coil was subjected to a first online annealing treatment and air cooling. The protective gas was high-purity argon, the temperature was 800℃, and the holding time was 5min.

[0044] After the first online annealing, the wire is drawn in the second rolling process, reducing the diameter from φ5.5mm to φ3.8mm. The drawing speed is controlled at 1.0~2.0m / s, the deformation is 52.26%, and the diameter reduction per pass is 0.4~0.5mm. Then, a second online annealing treatment is performed at a temperature of 780℃ for 4 minutes. The cooling method is air cooling, and the protective gas is high-purity argon.

[0045] After the second online annealing, the wire is drawn in the third rolling process, reducing the diameter from φ3.8mm to φ2.8mm. The drawing speed is controlled at 1.5~2.5m / s, the deformation is 45.7%, and the diameter reduction per pass is 0.2~0.3mm. Then, the wire is annealed in the third online process at a temperature of 760℃ for 5 minutes. The cooling method is air cooling, and the protective gas is high-purity argon.

[0046] After the third online annealing, the wire is drawn in the final rolling pass, reducing the diameter from φ2.8mm to φ1.82mm. The drawing speed is controlled at 2.0~3.0m / s, the deformation is 58.97%, and the diameter reduction per pass is 0.2mm. The finished product is then subjected to online annealing at 740℃ for 3 minutes, cooled by air, and protected by high-purity argon.

[0047] (3) Cleaning and Polishing: The annealed filament was mechanically polished using a flap wheel polishing machine to a diameter of φ1.80±0.01mm. The polishing process employed a multi-level grit combination polishing wheel, using 320 mesh, 600 mesh, and 800 mesh grit sequentially from coarse to fine, until a uniform mirror finish was achieved on the filament surface. A neutral or weakly alkaline water-based cleaning agent was used to ultrasonically clean the polished filament at 40℃~60℃ to thoroughly remove residual oil and fingerprints. After cleaning, the filament was rinsed with water, dried, and then rolled up.

[0048] The room temperature tensile properties of the 1.80mm TB13 wire prepared in Example 1 are as follows: Figure 2 As shown in the figure. Simultaneously, metallographic evaluation was performed on samples of the prepared filaments, and the results are attached. Figure 3 As shown in Figure A, under these processing conditions, the TB13 wire exhibits an ultrafine β-equiaxed grain structure with an average grain size of approximately 5 μm, representing a reduction of approximately 87% compared to the original disc-shaped grain size. This results in a good balance between strength and plasticity (Rm ≥ 780 MPa, A). 100mm (≥13%), which is better than competing products of the same type.

[0049] Comparative Example 1: The same coil was selected as in Example 1, and the same drawing process was used. The only change was that the annealing process was carried out at 800°C for 5 minutes throughout.

[0050] The room temperature tensile properties of the 1.80mm TB13 wire prepared in Comparative Example 1 are as follows: Figure 4 As shown in the figure. Simultaneously, metallographic evaluation was performed on samples of the prepared filaments, and the results are attached. Figure 3 As shown in Figure B, it can be seen that under this process condition, the β grains of TB13 wire are severely coarsened, with an average grain size of ≥50μm. Compared to Example 1, the material strength and plasticity are both reduced to a lower level, and the microstructure and properties are severely deteriorated.

[0051] Example 2: (1) Raw material selection: 8.0mm diameter TB13 titanium alloy discs in solid solution state after peeling were selected. The composition was Al 4.12wt%, V 22.82wt%, O 0.092wt%, Fe 0.068wt%, Mo 0.26wt%, with the balance being Ti and other impurities. The phase transformation point of the discs was 730℃, and they had a uniformly distributed β equiaxed structure with an average grain size of about 42μm.

[0052] (2) Multi-stage drawing and stepped online annealing: The coil from step 1 was drawn in multiple passes using a roller die to reduce its diameter to φ6.0mm, with a deformation of 43.75% and a diameter reduction of 0.5mm per pass. The drawing speed was controlled at 0.8~1.5m / s. Subsequently, the coil was subjected to a first online annealing treatment and air cooling. The protective gas was high-purity argon, the temperature was 820℃, and the holding time was 4min.

[0053] After the first online annealing, the wire is drawn in the second rolling process, reducing the diameter from φ6.0mm to φ4.2mm. The drawing speed is controlled at 1.0~2.5m / s, the deformation is 51%, and the diameter reduction per pass is 0.4~0.5mm. Then, a second online annealing process is carried out at a temperature of 780℃ for 5 minutes. The cooling method is air cooling, and the protective gas is high-purity argon.

[0054] After the second online annealing, the wire is drawn in the third rolling process, reducing the diameter from φ4.2mm to φ3.0mm. The drawing speed is controlled at 1.5~2.5m / s, the deformation is 48.98%, and the diameter reduction per pass is 0.2~0.3mm. Then, the wire is annealed in the third online process at a temperature of 760℃ for 5 minutes. The cooling method is air cooling, and the protective gas is high-purity argon.

[0055] After the third online annealing, the wire is drawn in the final rolling pass, reducing the diameter from φ3.0mm to φ2.02mm. The drawing speed is controlled at 2.0~3.0m / s, the deformation is 54.67%, and the diameter reduction per pass is 0.2mm. The finished product is then subjected to online annealing at 750℃ for 3 minutes, cooled by air, and protected by high-purity argon.

[0056] (3) Cleaning and Polishing: The annealed filament was mechanically polished using a flap polishing machine to a diameter of φ2.0±0.01mm. The polishing process employed a multi-level grit combination polishing wheel, using 320 mesh, 600 mesh, and 800 mesh grit sequentially from coarse to fine, until a uniform mirror finish was achieved on the filament surface. A neutral or weakly alkaline water-based cleaning agent was used to ultrasonically clean the polished filament at 40℃~60℃ to thoroughly remove residual oil and fingerprints. After cleaning, the filament was rinsed with water, dried, and then rolled up.

[0057] The room temperature tensile properties of the Φ2.0mm TB13 wire prepared in Example 2 are as follows: Figure 5 As shown in the figure. Simultaneously, metallographic evaluation was performed on samples of the prepared filaments, and the results are attached. Figure 3As shown in Figure C, under these processing conditions, the TB13 wire exhibits an ultrafine β-equiaxed grain structure with an average grain size of approximately 8 μm, which is ~81% smaller than the original disc-shaped grain size. It also demonstrates excellent strength-ductility matching (Rm≥780MPa, A). 100mm (≥14%), which is better than competing products of the same type.

[0058] Comparative Example 2: Using the same coiled raw material as in Example 2, multi-pass cold drawing with rollers and stepped online annealing were performed. The only change was that the deformation before annealing was controlled to be <43%.

[0059] The room temperature tensile properties of the 2.0mm TB13 wire prepared in Comparative Example 2 are as follows: Figure 6 As shown in the figure. Simultaneously, metallographic evaluation was performed on samples of the prepared filaments, and the results are attached. Figure 3 As shown in Figure D, it can be seen that under these processing conditions, the β-grains of TB13 wire did not undergo refinement, with an average grain size of 40~50μm. Compared to Example 2, the material's strength and plasticity are both at a lower level.

[0060] Comparative Example 3: Using the same coiled raw material as in Example 2, multi-pass cold drawing with rollers and stepped online annealing were performed. The only change was that the deformation before annealing was controlled to be >62%.

[0061] The 2.0mm TB13 wire prepared in Comparative Example 3 exhibited large-area cracking, as shown in the attached figure. Figure 7 As shown, under this process condition, the deformation amount of >62% of the passes exceeds the processing plasticity of TB13 wire, resulting in cracking and peeling of the material, which fails to meet the quality requirements.

[0062] Based on the same inventive concept, according to another aspect of the present invention, embodiments of the present invention also provide a titanium alloy wire, such as... Figure 8 As shown, the titanium alloy wire is prepared by the method described in any of the above embodiments.

[0063] The above are exemplary embodiments disclosed in this invention. However, it should be noted that various changes and modifications can be made without departing from the scope of the embodiments of this invention as defined by the claims. The functions, steps, and / or actions of the methods according to the disclosed embodiments described herein do not need to be performed in any particular order. Furthermore, although the elements disclosed in the embodiments of this invention may be described or claimed individually, they may be understood as multiple unless explicitly limited to a singular number.

[0064] It should be understood that, as used herein, the singular form “a” is intended to include the plural form as well, unless the context clearly supports an exception. It should also be understood that, as used herein, “and / or” refers to any and all possible combinations of one or more of the associated listed items.

[0065] The embodiment numbers disclosed in the above embodiments of the present invention are for descriptive purposes only and do not represent the superiority or inferiority of the embodiments.

[0066] Those skilled in the art should understand that the discussion of any of the above embodiments is merely exemplary and is not intended to imply that the scope of the invention (including the claims) is limited to these examples. Within the framework of the invention, technical features of the above embodiments or different embodiments can be combined, and many other variations of different aspects of the invention exist, which are not provided in the details for the sake of brevity. Therefore, any omissions, modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the invention should be included within the protection scope of the invention.

Claims

1. A method for preparing titanium alloy wire by drawing, characterized in that, Includes the following steps: Peeling and polishing of titanium alloy discs; After peeling and polishing, the titanium alloy coils are subjected to multi-stage, multi-pass cold drawing with roller dies. When the cumulative deformation of each stage of multi-pass cold drawing with roller dies reaches the preset value, online annealing is performed according to the specifications of the wire at the current stage, using different annealing temperatures and holding times. Then, the next stage of multi-pass cold drawing with roller dies is carried out. As the specifications of the wire decrease, the annealing temperature gradually decreases.

2. The method as described in claim 1, characterized in that, Based on the current specifications of the wire, online annealing is performed using different annealing temperatures and holding times, further including: When the wire specifications are in the range of φ5.0mm~φ6.5mm, the annealing temperature is 800℃~820℃, and the holding time is 4~7 minutes; When the wire specifications are in the range of φ3.5mm~φ5.0mm, the annealing temperature is 770℃~800℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ2.0mm~φ3.5mm, the annealing temperature is 750℃~780℃, and the holding time is 3~5 minutes; When the wire specifications are in the range of φ1.4mm to φ2.0mm, the annealing temperature is 730℃ to 760℃, and the holding time is 2 to 4 minutes.

3. The method as described in claim 1, characterized in that, Also includes: The drawing speed of the multi-pass cold drawing at each stage is controlled between 0.8 and 3.6 m / s, and the drawing speed increases as the size of the obtained wire decreases.

4. The method as described in claim 3, characterized in that, Also includes: The diameter reduction of a single drawing pass in each stage is controlled within 0.2~0.5mm, and the diameter reduction decreases as the specification decreases.

5. The method as described in claim 1, characterized in that, Once the cumulative deformation of the multi-pass cold drawing at each stage reaches the preset value, online annealing is performed according to the specifications of the wire at the current stage, using different annealing temperatures and holding times. This further includes: When the cumulative deformation of the multi-pass cold drawing of each stage reaches 43%~62%, online annealing is carried out using different annealing temperatures and holding times.

6. The method as described in claim 5, characterized in that, Online annealing is performed using different annealing temperatures and holding times, further including: Annealing was performed in an online annealing furnace with argon atmosphere protection and followed by air cooling.

7. The method as described in claim 1, characterized in that, The titanium alloy discs, after being peeled and polished, undergo multi-stage, multi-pass cold drawing on roller dies, further including: The first wire of the first specification is obtained by cold drawing the titanium alloy coil through multiple passes of roller drawing, and the first wire is then subjected to online annealing treatment. The first wire is cold-drawn by multiple passes of roller drawing to obtain a second wire of the second specification, and the second wire is then subjected to online annealing. The second filament is subjected to multiple passes of cold drawing with rollers to obtain a third filament of a third specification, and the third filament is subjected to online annealing. The third filament is subjected to multiple passes of cold drawing on a roller to obtain a finished filament, and the finished filament is then subjected to online annealing.

8. The method as described in claim 7, characterized in that, Also includes: The annealed wire was mechanically polished to a diameter of φ1.80±0.01mm.

9. The method as described in claim 8, characterized in that, Also includes: A multi-level polishing wheel is used, with 320 mesh, 600 mesh and 800 mesh mesh used sequentially to polish from coarse to fine until the surface of the wire material achieves a uniform mirror finish. Use a neutral or weakly alkaline water-based cleaning agent to perform ultrasonic cleaning on the polished wire material at a temperature of 40℃~60℃.

10. A titanium alloy wire, characterized in that, The titanium alloy wire is prepared based on the method described in any one of claims 1-9.

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