A method for preparing ultrafine wire of difficult-to-process deformable high-damping titanium alloy

Abstract

The present invention provides a method for preparing a high-damping titanium alloy ultrafine wire that is difficult to process and deform, and the preparation method comprises the following steps: (1) ingot smelting; (2) homogenization treatment; (3) forging treatment; (4) groove rolling; (5) cold drawing processing; (6) annealing treatment. The present invention has a reasonable concept, and improves the processing deformation ability of high-oxygen content damping titanium alloy through component micro-control and heterogeneous structure toughening technology; and combined with the traditional preparation and processing technology of titanium alloy wire, it reduces the difficulty and threshold of material preparation, solves the problem of preparation and processing of high-oxygen content damping titanium alloy ultrafine wire, and is suitable for large-scale production, promotion and application of fasteners, elastic components, etc.

Description

Technical Field

[0001] The invention belongs to the technical field of advanced functional structure integrated metal material processing, and specifically relates to a method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire. Background Art

[0002] With the development of new technological productivity, the vibration and noise problems generated by high-power equipment in the defense and civilian fields such as aerospace, shipbuilding, and automobile production during service are becoming increasingly prominent, often leading to serious problems such as reduced component life and poor instrument accuracy. At present, commonly used vibration and noise reduction methods include adding dampers and shock absorbers, optimizing structural design, and using damping materials to manufacture parts. Among them, high-damping alloy materials can convert mechanical vibration energy into heat energy dissipation, while also having good mechanical properties. It is a functional and structural integrated metal material; and it can fundamentally reduce vibration and noise, simplify design complexity, and is a practical and efficient means of vibration and noise reduction, with important engineering value and broad application prospects.

[0003] As one of the typical representatives of damping alloy materials, high damping titanium alloy (damping coefficient tanδ≥0.01) not only has many advantages such as low density, high specific strength, corrosion resistance, but also can effectively absorb and dissipate vibration energy, and has key high-value applications in many fields. According to the difference in damping physical mechanism, high damping titanium alloys can be divided into two categories: NiTi-based damping titanium alloys based on thermoelastic martensitic phase transformation and TiNbO-based damping titanium alloys based on Sneok relaxation dissipation theory. Among them, under medium and high temperature environmental conditions (≥150ºC), Sneok relaxation dissipation type high damping titanium alloys play a key role in aerospace equipment due to their excellent damping performance and comprehensive mechanical properties. However, Sneok relaxation dissipation type high damping titanium alloys usually add a high content of interstitial alloying element O (≥0.5 wt.%), which leads to serious deterioration of its plastic deformation ability and toughness, as well as reduced thermal conductivity. These factors significantly increase the difficulty of preparation and processing of such alloys, thereby limiting their application range.

[0004] High damping titanium alloys are often used in vibration and noise reduction scenes as fasteners, elastic components, etc. Therefore, focusing on the preparation of high damping titanium alloy wires, aiming at the problem of difficult processing and deformation of Sneok relaxation dissipative high damping titanium alloys, innovatively developing a new generation of difficult-to-process and deform high damping titanium alloy ultrafine wires, and developing related preparation and processing methods have important practical engineering significance. Summary of the invention

[0005] In view of the technical difficulties existing in the above background, the present invention proposes a method for preparing ultrafine wires of high-damping titanium alloy that are difficult to process and deform. The method has a reasonable conception and improves the processing and deformation ability of high-oxygen-content damping titanium alloys through fine-tuning of components and toughening technology of heterogeneous structures. Combined with the traditional preparation and processing technology of titanium alloy wires, the difficulty and threshold of material preparation are reduced, and the problem of the difficulty in preparing and processing ultrafine wires of high-oxygen-content damping titanium alloys is solved. The method is suitable for large-scale production and promotion, and is expected to be widely used as fasteners and elastic components in the fields of aviation, aerospace, ships, etc.

[0006] In order to solve the above technical problems, the present invention provides a method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire, which mainly comprises the following steps:

[0007] (1) Ingot Melting

[0008] Pure titanium flakes, pure zirconium flakes, pure iron particles, pure molybdenum particles, pure chromium flakes and titanium dioxide powder are used as raw materials for smelting alloys. The raw materials are mixed according to the set mass percentage. Then, the raw materials are mixed evenly and placed in a vacuum suspension melting furnace for repeated melting for 3 to 5 times. The vacuum degree is 10 -3 Pa-10 -4 Pa, to obtain alloy ingot material;

[0009] (2) Homogenization

[0010] The alloy ingot material obtained in step (1) above is placed in a vacuum heat treatment furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, heated to temperature T1 in a vacuum heat treatment furnace, kept at temperature for t1, and then cooled in a vacuum heat treatment furnace to obtain an alloy homogenized ingot material;

[0011] (3) Forging treatment

[0012] The homogenized ingot material obtained in the above step (2) is kept in a heat treatment furnace at a temperature of T2 for a time of t2, and is subjected to β-opening forging, and is subjected to reciprocating drawing and upsetting treatments in sequence, with the deformation of each drawing process being 10-30% and the upsetting process being 20-40%; then, the bar is subjected to rough forging at a temperature of T2-(80-180°C); then, the bar is subjected to fine forging at a temperature of T2-(130-260°C); finally, the surface is subjected to mechanical grinding to obtain a bar with a diameter of d 1 alloy precision forging bar billet;

[0013] (4) Passage rolling

[0014] The fine forging bar blank obtained in step (3) above is placed in a heat treatment furnace at a temperature of T3 for a holding time of t3 and cooled at a furnace cooling rate of vCool down to T3-(100~180ºC) and keep the temperature for the same time t3, then water cool; then carry out groove rolling treatment, the deformation amount of each pass is 2~8%, when the cumulative deformation is 20~30%, repeat the heat treatment in the heat treatment furnace at temperature T3 and continue the groove rolling, and finally obtain a diameter of d 2 alloy wire billet;

[0015] (5) Cold drawing

[0016] The alloy wire blank obtained in the above step (4) is placed in a heat treatment furnace and subjected to stress relief annealing at a temperature T4. A lubricating coating is then applied to the surface of the alloy wire blank, followed by cold drawing. The deformation amount of each pass is 1-5%. When the cumulative deformation amount reaches 30-50%, stress relief annealing is performed again at a temperature T4. The lubricating coating and cold drawing are repeated in a cycle of annealing-lubricating-cold drawing. Finally, a wire with a diameter of d 3 alloy cold drawn primary ultra-fine wire;

[0017] (6) Annealing

[0018] The primary ultrafine wire obtained in the above step (5) is placed in a heat treatment furnace at a temperature of T5 for a holding time of t5, taken out and water-cooled, and then its surface is chemically polished to finally obtain a high-damping titanium alloy ultrafine wire.

[0019] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: the mass percentage of the elements in the high-damping titanium alloy ingot material in the step (1) is: O is 0.6-1.0%, Zr is 0.6-1.2%, Fe is 1.2-2.0%, Cr is 2.2-2.8%, Mo is 3.0-3.8%, and the remainder is Ti and unavoidable impurity elements.

[0020] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: in the step (2), the homogenization heat treatment temperature T1 is 1150-1250°C, and the time t1 is 12-24h.

[0021] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: the temperature T2 of the β-opening forging in the step (3) is 1080-1200°C, the time t2 is 2-8h, and the diameter of the alloy precision forging bar blank is d 1 is 12~30mm.

[0022] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: in the step (3), the β-opening forging is performed for 3 to 5 times, the bar rough forging is performed for 2 to 4 times, and the bar fine forging is performed for 2 to 4 times.

[0023] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: in the step (4), the temperature T3 is 860-920°C, the time t3 is 20-60min, and the furnace cooling speed is v 5~10°C / min, alloy wire billet diameter d 2 is 1~5mm.

[0024] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: in the step (5), the temperature T4 is 620-680°C, the time t4 is 3-15 minutes, and the primary ultrafine wire diameter is d 3 is 0.09~0.5mm.

[0025] The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire, wherein: in the step (6), the temperature T5 is 450-850°C, and the time t4 is 0.5-12h.

[0026] By adopting the above technical solution, the present invention has the following beneficial effects:

[0027] The preparation method of the difficult-to-process deformable high-damping titanium alloy ultrafine wire of the present invention is reasonably conceived. The prepared difficult-to-process deformable high-damping titanium alloy ultrafine wire not only has excellent comprehensive mechanical properties and damping properties, but also fills the gap in the field of high-oxygen content damping titanium alloy ultrafine wire, and is expected to be promoted and applied in elastic components and fasteners in the fields of aviation, ships, etc.

[0028] The present invention improves the processing deformation ability of high-oxygen damping titanium alloy through component fine-control and heterogeneous structure toughening technology; combined with the traditional preparation and processing technology of titanium alloy wire, it reduces the difficulty and threshold of material preparation, and solves the problem of difficulty in preparation and processing of high-oxygen damping titanium alloy ultrafine wire. It is suitable for large-scale production and promotion, and is expected to be widely used as fasteners and elastic components in the fields of aviation, aerospace, ships, etc.

[0029] The present invention has the following advantages or features:

[0030] (1) Homogenization treatment is aimed at the composition segregation problem between dendrites formed during the cooling and solidification process of vacuum melting of alloy. The process of long-term heat preservation under vacuum high temperature is adopted to reduce the composition segregation formed by solidification, improve the uniformity of alloy composition, and improve the deformation ability of alloy, thereby compensating for the difficult processing deformation problem caused by the addition of high content of interstitial element O;

[0031] (2) The three-step cooling forging process of blanking, rough forging and fine forging is adopted in the forging process because the grain size is coarse after the alloy is homogenized and the high oxygen content in the alloy easily leads to cracking of the ingot forging. The development of the three-step cooling multi-fire forging process not only improves the uniformity of the alloy microstructure, but also reduces the difficulty of alloy processing deformation, thereby improving the quality of the alloy bar.

[0032] (3) The two-stage solution process is adopted in the groove rolling, which is based on the characteristics of the α / β isomorphous transformation behavior of titanium alloy. In the early high temperature stage, the α phase is dissolved in the matrix β phase by heat preservation, and the nucleation position of the secondary α phase is controlled by slow cooling. In the later stage, the secondary α phase is precipitated and grown in the matrix by heat preservation. In this way, the precipitation amount, spatial position, morphology and other factors of the α phase are regulated, and the heterogeneous microstructure is introduced to improve the plastic deformation ability of the alloy and reduce the difficulty of processing deformation of high O content titanium alloy.

[0033] (4) The cold drawing process is based on the traditional cold drawing process of titanium alloy wire. The deformation of the alloy in each pass (1-5%) is strictly controlled to improve the drawing quality of the wire by increasing the number of drawing times. When the accumulated cold drawing deformation reaches 30-50%, the T4 annealing process is used to reduce the internal stress of the material and improve the continuous processing deformation capacity of the alloy wire. In addition, to ensure the smooth progress of the cold drawing process, ultrafine graphite powder and molybdenum disulfide are used as lubricants to reduce the friction during the drawing process and improve the surface quality of the high damping titanium alloy wire. The results show that the comprehensive technical methods such as multiple passes with small deformation, annealing process and lubricant coating are used in the cold drawing process to ensure the smooth progress of the cold drawing process. BRIEF DESCRIPTION OF THE DRAWINGS

[0034] In order to more clearly illustrate the specific implementation methods of the present invention or the technical solutions in the prior art, the drawings required for use in the specific implementation methods or the description of the prior art will be briefly introduced below. Obviously, the drawings in the following description are some implementation methods of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying creative work.

[0035] Figure 1 It is a schematic flow chart of the method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire of the present invention;

[0036] Figure 2 The hard-to-process, deformable, high-damping titanium alloy ultrafine wire sample of the present invention;

[0037] Figure 3 This is a sample of a high-damping titanium alloy ultrafine wire prepared by the method for preparing a difficult-to-machine deformable high-damping titanium alloy ultrafine wire according to Example 1 of the present invention;

[0038] Figure 4 This is a sample of a high-damping titanium alloy ultrafine wire prepared by the method for preparing a difficult-to-machine deformable high-damping titanium alloy ultrafine wire according to Example 2 of the present invention;

[0039] Figure 5 This is a picture of a high-damping titanium alloy ultrafine wire sample prepared by the method for preparing a difficult-to-machine deformable high-damping titanium alloy ultrafine wire according to Example 2 of the present invention. DETAILED DESCRIPTION

[0040] The technical solution of the present invention will be described clearly and completely below in conjunction with the accompanying drawings. Obviously, the described embodiments are only part of the embodiments of the present invention, not all of the embodiments. Based on the embodiments of the present invention, all other embodiments obtained by ordinary technicians in this field without creative work are within the scope of protection of the present invention.

[0041] The present invention is further explained below in conjunction with specific implementation modes.

[0042] like Figure 1 As shown, the present embodiment provides a method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire, which mainly includes the following steps:

[0043] S1 Ingot Melting

[0044] Pure titanium sheets, pure zirconium sheets, pure iron particles, pure molybdenum particles, pure chromium sheets and titanium dioxide powder are used as raw materials for smelting alloys. The mass percentage of O is 0.6-1.0%, Zr is 0.6-1.2%, Fe is 1.2-2.0%, Cr is 2.2-2.8%, Mo is 3.0-3.8%, and the balance is Ti and unavoidable impurity elements. Then, the proportioned raw materials are mixed evenly and repeatedly smelted 3-5 times in a vacuum suspension melting furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, to obtain alloy ingot material. Among them, the melting temperature exceeds 2000°C, which is related to the current applied during the experiment; the vacuum suspension melting furnace is generally in a constant voltage variable current mode during operation, and the output power is adjusted by changing the current size, thereby changing the melting crucible temperature; the melting time includes the melting time and the liquid suspension diffusion time. Generally, the liquid suspension diffusion takes 10-15 minutes after the material is melted.

[0045] The present invention improves the plastic deformation ability of the prepared alloy by using the above-mentioned mass percentage of the smelting alloy raw material; firstly, under the above-mentioned Fe element content ratio, the problem of easy segregation and poor thermal stability of the Fe element during smelting can be reduced; under the above-mentioned Mo element content ratio, the hardenability of the prepared alloy can be increased, the alloy β stability can be maintained, and the thermal stability of the Fe and Cr elements can be improved; secondly, under the above-mentioned neutral element Zr content ratio, the precipitation of the hard and brittle ω phase in the β phase can be inhibited, the ingot grains can be refined, and the oxidation resistance of the alloy can be improved, thereby significantly improving the processing deformation ability of the prepared alloy; by configuring the above-mentioned mass percentage of the smelting alloy raw material, the foundation can be laid for the preparation of high-damping titanium alloy ultrafine wires.

[0046] S2 Homogenization

[0047] The alloy ingot material obtained in step S1 is placed in a vacuum heat treatment furnace and heated to a temperature T1 of 1150-1250°C and a vacuum degree of 10 -3 Pa-10 -4 Pa, the holding time t1 is 12~24h and then cooled in the vacuum heat treatment furnace to obtain the alloy homogenized ingot material;

[0048] S3 forging treatment

[0049] The homogenized ingot material in step S2 is placed in a heat treatment furnace with a temperature T2 of 1080-1200°C and a holding time t2 of 2-8h to perform β-opening forging (the process is: forging treatment is performed using a forging machine at a high temperature higher than the β transformation temperature. The side extrusion is usually called drawing, and the height extrusion is usually called upsetting. The important process parameters of this step are the heating temperature and the holding time). The drawing and upsetting treatments are performed reciprocally in sequence (the side extrusion is usually called drawing, and the height extrusion is usually called upsetting. The process control is mainly drawing The deformation of each stretching is generally 10-30%, and that of each upsetting is 20-40%). The blank is forged for 3 to 5 times; then the bar is rough forged for 2 to 4 times at a temperature of 900 to 1120°C; then the bar is fine forged for 2 to 4 times at a temperature of 820 to 1070°C (the difference between rough forging and fine forging is the internal structure of the bar. In order to obtain the ideal structure, rough forging is performed first and then fine forging is performed to obtain the ideal performance); finally, the surface is mechanically ground to obtain the diameter d 1 is alloy forging bar blank with a diameter of 12-30 mm;

[0050] S4 groove rolling

[0051] The fine forging bar blank of step S3 is placed in a heat treatment furnace with a temperature T3 of 860-920°C and a holding time t3 of 20-60 min.v The temperature is cooled to 680~820ºC at a furnace cooling rate of 5~10 °C / min, and the same holding time t3 is 20~60min, and then water cooling is performed; then groove rolling is performed (groove rolling is a kind of rolling deformation. A groove of a certain size is processed on a normal flat roll, and the bar is rolled and deformed in the groove to reduce the deformation difficulty of the material). The deformation amount of each pass is 2~8%; when the cumulative deformation is 20~30%, it is repeatedly heat treated in a heat treatment furnace at a temperature of T3, and then groove rolling is continued to obtain a diameter of d 2 is alloy wire blank of 1~5mm;

[0052] S5 Cold Drawing

[0053] The alloy wire blank obtained in the above step S4 is placed in a heat treatment furnace and subjected to stress relief annealing at a temperature T4 of 620-680°C for 3-15 min. After water cooling, a lubricating coating is applied to the surface of the alloy wire blank, followed by cold drawing. The deformation amount of each pass is 1-5%. After the cumulative deformation amount reaches 30-50%, stress relief annealing is performed again at temperature T4, and the lubricating coating and cold drawing are applied again. Annealing-lubricating-cold drawing are repeated repeatedly to finally obtain a wire with a diameter of d 3 is 0.09~0.5mm alloy cold drawn primary ultra-fine wire;

[0054] S6 annealing treatment

[0055] The primary ultrafine wire obtained in the above step S5 is placed in a heat treatment furnace with a temperature T5 of 700-850°C and a holding time t5 of 0.5-12h. After being taken out, it is water-cooled and then chemically polished (i.e., a certain ratio of chemical reagents is used to corrode the tiny protruding burrs on the surface of the wire, thereby improving its surface quality and finish) to finally obtain a high-damping titanium alloy ultrafine wire.

[0056] Embodiment 1:

[0057] The difficult-to-process, deformable, high-damping titanium alloy ultrafine wire in Example 1 of the present invention is mainly composed of the following elements in percentage by mass: 0.8% O, 0.8% Zr, 1.7% Fe, 2.2% Cr, 3% Mo, and the remainder Ti and unavoidable impurity elements.

[0058] Combination Figure 1 The schematic flow chart of the method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire of the present invention is shown, wherein the predetermined smelting ingot mass is 5 kg, and the method may specifically include the following steps:

[0059] S1-1, ingot smelting: pure titanium sheet, pure zirconium sheet, pure iron particles, pure molybdenum particles, pure chromium sheet and titanium dioxide powder are used as smelting alloy raw materials, and the proportions are set according to the set mass percentage, that is, 4515g of pure titanium sheet, 40g of pure zirconium sheet, 85g of pure iron particles, 150g of pure molybdenum particles, 110g of pure chromium sheet and 100g of titanium dioxide powder. After the proportioned raw materials are evenly mixed, they are repeatedly smelted 4 times in a vacuum suspension smelting furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, to obtain alloy ingot material;

[0060] S1-2, homogenization treatment: the ingot material prepared in step S1-1 is placed in a vacuum heat treatment furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, heated to a temperature T1 of 1200°C in a furnace, kept at a temperature of 20h, and then cooled in a furnace to obtain an alloy homogenized ingot material;

[0061] S1-3, forging treatment: the homogenized ingot material obtained in step S1-2 is placed in a heat treatment furnace at a temperature T2 of 1150°C for a holding time t2 of 4h, and subjected to β-open forging, and then subjected to reciprocating drawing-upsetting treatment in sequence, and the open forging is performed for 3 times; then, the bar is rough forged for 3 times at a temperature of 1050°C; then, the bar is fine forged for 3 times at a temperature of 970°C; finally, the surface is mechanically ground to obtain a diameter of d 1 is a 15 mm alloy precision forging bar blank;

[0062] S1-4, pass rolling: the alloy forging bar blank obtained in step S1-3 is placed in a heat treatment furnace with a temperature T3 of 900°C and a holding time t3 of 40 min, and v The temperature is cooled to 810ºC at a furnace cooling rate of 5 °C / min, and the same holding time t3 is 40min, and then water cooling is performed; then the groove rolling treatment is performed, and the deformation amount of each pass is 2%; when the cumulative deformation is 24%, the heat treatment at temperature T3 of 900°C is repeated, and the groove rolling is continued, and finally a diameter of d 2 is 1.5 mm alloy wire blank;

[0063] S1-5, cold drawing: the alloy wire blank obtained in step S1-4 is first subjected to stress relief annealing at a temperature T4 of 680°C, the heat preservation time is 5 min, and ultrafine graphite powder and molybdenum disulfide lubricating coating are coated on the surface of the alloy wire blank after water cooling, and then cold drawing is performed, the deformation amount of each pass is 2%, and when the cumulative deformation amount reaches 36%, stress relief annealing is performed again at a temperature T4 of 680°C, and lubricating coating and cold drawing are applied again, and annealing-lubricating-cold drawing are repeated to finally obtain a wire with a diameter ofd 3 is 0.19mm alloy cold drawn primary ultra-fine wire;

[0064] S1-6, annealing treatment: the primary ultrafine wire obtained in step S1-5 is placed in a heat treatment furnace with a temperature T5 of 600°C, 650°C, 700°C, 750°C and 780°C for a holding time t5 of 30 min. After being taken out, it is water-cooled and then its surface is chemically polished to finally obtain a high damping titanium alloy ultrafine wire.

[0065] Finally, a room temperature quasi-static mechanical property test was performed on the ultrafine titanium alloy wire with high damping and difficult to process prepared in the above Example 1. The ultrafine titanium alloy wire with high damping and difficult to process has excellent strength and plasticity after being annealed by different processes.

[0066] Table 1 Mechanical properties of high damping titanium alloy ultrafine wire under different annealing conditions in Example 1:

[0067]

[0068] Embodiment 2:

[0069] The difficult-to-process, deformable, high-damping titanium alloy ultrafine wire in Example 2 of the present invention is mainly composed of the following elements in percentage by mass: 0.8% O, 1.0% Zr, 1.8% Fe, 2.5% Cr, 3.5% Mo, and the remainder Ti and unavoidable impurity elements.

[0070] Combination Figure 1 The schematic flow chart of the method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire of the present invention is shown, wherein the predetermined smelting ingot mass is 5 kg, and the method may specifically include the following steps:

[0071] S2-1, ingot smelting: pure titanium sheet, pure zirconium sheet, pure iron particles, pure molybdenum particles, pure chromium sheet and titanium dioxide powder are used as smelting alloy raw materials, and the proportions are set according to the set mass percentage, that is, 4460g of pure titanium sheet, 50g of pure zirconium sheet, 90g of pure iron particles, 175g of pure molybdenum particles, 125g of pure chromium sheet and 100g of titanium dioxide powder. After the proportioned raw materials are evenly mixed, they are repeatedly smelted 5 times in a vacuum suspension smelting furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, to obtain alloy ingot material;

[0072] S2-2, homogenization treatment: the alloy ingot material prepared in step S2-1 is placed in a vacuum heat treatment furnace, and heated to a temperature T1 of 1240°C and a vacuum degree of 10 -3 Pa-10 -4Pa, the holding time t1 is 16h and then cooled with the furnace to obtain the alloy homogenized ingot material;

[0073] S2-3, forging treatment: the alloy homogenized ingot material obtained in step S2-2 is placed in a heat treatment furnace at a temperature T2 of 1150°C for a holding time t2 of 4h, and subjected to β-open forging, and then subjected to reciprocating drawing-upsetting treatment in sequence, and the open forging is performed for 5 times; then, the bar is rough forged for 3 times at a temperature of 1050°C; then, the bar is fine forged for 4 times at a temperature of 970°C; finally, the surface is mechanically ground to obtain a diameter of d 1 is a 20 mm alloy precision forging bar blank;

[0074] S2-4, pass rolling: the alloy precision forging bar blank obtained in step S2-3 is placed in a heat treatment furnace with a temperature T3 of 900°C and a holding time t3 of 40 min, and v The temperature is cooled to 830°C at a furnace cooling rate of 5°C / min, and the same holding time t3 is 40min, followed by water cooling; then the groove rolling treatment is carried out, and the deformation amount of each pass is 2%; when the cumulative deformation is 20%, the heat treatment at temperature T3 of 900°C is repeated, and the groove rolling is continued, and finally a diameter of d 2 is 1.2 mm alloy wire blank;

[0075] S2-5, cold drawing: the alloy wire blank obtained in step S2-4 is first subjected to stress relief annealing at a temperature T4 of 700°C, the heat preservation time is 4 min, ultrafine graphite powder and molybdenum disulfide lubricating coating are coated on the surface of the alloy wire blank after water cooling, and then cold drawing is performed, the deformation amount of each pass is 2%, and after the cumulative deformation amount reaches 40%, stress relief annealing is performed again at a temperature T4 of 700°C, and lubricating coating and cold drawing are applied again, and annealing-lubricating-cold drawing are repeated to finally obtain a wire with a diameter of d 3 is 0.09mm alloy cold drawn primary ultra-fine wire;

[0076] S2-6, annealing treatment: the alloy cold-drawn primary ultrafine wire obtained in step S2-5 is placed in a heat treatment furnace with a temperature T5 of 700°C, 750°C and 780°C for a holding time t5 of 30 min, taken out and water-cooled, and then the surface is chemically polished to finally obtain a high-damping titanium alloy ultrafine wire.

[0077] Finally, a room temperature quasi-static mechanical property test was performed on the ultrafine titanium alloy wire with high damping and difficult to process prepared in Example 2. The ultrafine titanium alloy wire with high damping and difficult to process has excellent strength and plasticity after annealing.

[0078] Table 2 Mechanical properties of high damping titanium alloy ultrafine wire under different annealing conditions in Example 2:

[0079]

[0080] The present invention has a reasonable concept. Through fine-tuning of components and toughening technology of heterogeneous structures, the processing deformation ability of high oxygen content damping titanium alloy is improved. Combined with the traditional preparation and processing technology of titanium alloy wire, the difficulty and threshold of material preparation are reduced, and the problem of difficulty in preparation and processing of ultrafine wire of high oxygen content damping titanium alloy is solved. It is suitable for large-scale production and promotion, and is expected to be widely used as fasteners and elastic components in the fields of aviation, aerospace, ships, etc.

[0081] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, rather than to limit it. Although the present invention has been described in detail with reference to the aforementioned embodiments, those skilled in the art should understand that they can still modify the technical solutions described in the aforementioned embodiments, or replace some or all of the technical features therein with equivalents. However, these modifications or replacements do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A method for preparing a difficult-to-process deformable high-damping titanium alloy ultrafine wire, characterized in that , mainly including the following steps: (1) Ingot Melting Pure titanium flakes, pure zirconium flakes, pure iron particles, pure molybdenum particles, pure chromium flakes and titanium dioxide powder are used as raw materials for smelting alloys. The raw materials are mixed according to the set mass percentage. Then, the raw materials are mixed evenly and placed in a vacuum suspension melting furnace for repeated melting for 3 to 5 times. The vacuum degree is 10 -3 Pa-10 -4 Pa, to obtain alloy ingot material; (2) Homogenization The alloy ingot material obtained in step (1) above is placed in a vacuum heat treatment furnace with a vacuum degree of 10 -3 Pa-10 -4 Pa, heated to temperature T1 in a vacuum heat treatment furnace, kept at temperature for t1, and then cooled in a vacuum heat treatment furnace to obtain an alloy homogenized ingot material; (3) Forging treatment The homogenized ingot material obtained in the above step (2) is kept in a heat treatment furnace at a temperature of 1080-1200°C for 2-8 hours, and then subjected to β-opening forging, and then subjected to reciprocating drawing and upsetting treatments in sequence, wherein the deformation amount of each drawing process is 10-30%, and the deformation amount of each upsetting process is 20-40%; then, the bar is rough forged at a temperature of (1080-1200°C)-(80-180ºC); then, the bar is fine forged at a temperature of (1080-1200°C)-(130-260ºC); finally, the surface is mechanically ground to obtain a bar with a diameter of d 1 alloy precision forging bar billet; (4) Passage rolling The fine forging bar blank obtained in step (3) is placed in a heat treatment furnace at a temperature of 860-920°C for a holding time of 20-60 min and cooled at a furnace cooling rate of v Cool down to (860~920°C)-(100~180ºC) and keep warm for 20~60min, then water cool; then perform pass rolling, with a deformation of 2~8% per pass. When the cumulative deformation is 20~30%, repeat the heat treatment in a heat treatment furnace at 860~920°C and continue pass rolling, and finally obtain a diameter of d 2 alloy wire billet; (5) Cold drawing The alloy wire blank obtained in the above step (4) is placed in a heat treatment furnace and subjected to stress relief annealing at a temperature T4. A lubricating coating is then applied to the surface of the alloy wire blank, followed by cold drawing. The deformation amount of each pass is 1-5%. When the cumulative deformation amount reaches 30-50%, stress relief annealing is performed again at a temperature T4. The lubricating coating and cold drawing are repeated in a cycle of annealing-lubricating-cold drawing. Finally, a wire with a diameter of d 3 alloy cold drawn primary ultra-fine wire; (6) Annealing The primary ultrafine wire obtained in the above step (5) is placed in a heat treatment furnace at a temperature of T5 for a holding time of t5, taken out and water cooled, and then the surface is chemically polished to finally obtain a high damping titanium alloy ultrafine wire; The mass percentages of the elements in the high damping titanium alloy ingot material in step (1) are: 0.6-1.0% O, 0.6-1.2% Zr, 1.2-2.0% Fe, 2.2-2.8% Cr, 3.0-3.8% Mo, and the remainder being Ti and unavoidable impurity elements.

2. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: In the step (2), the homogenization heat treatment temperature T1 is 1150-1250°C, and the time t1 is 12-24h.

3. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: The diameter of the alloy forging bar stock in step (3) is d 1 is 12~30mm.

4. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: In the step (3), the β-opening forging is performed for 3 to 5 times, the bar rough forging is performed for 2 to 4 times, and the bar fine forging is performed for 2 to 4 times.

5. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: The furnace cooling speed in step (4) v 5~10°C / min, alloy wire billet diameter d 2 is 1~5mm.

6. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: In step (5), the temperature T4 is 620-680°C, the time t4 is 3-15 min, and the primary ultrafine filament diameter is d 3 is 0.09~0.5mm.

7. The method for preparing the difficult-to-process deformable high-damping titanium alloy ultrafine wire according to claim 1, characterized in that: In the step (6), the temperature T5 is 450-850°C, and the time t4 is 0.5-12h.

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