CN114433765B - Preparation method of high-strength and high-toughness TA31 titanium alloy material - Google Patents
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
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Abstract
The invention discloses a preparation method of a high-strength and high-toughness TA31 titanium alloy material, which comprises the following steps: 1. uniformly mixing titanium sponge and intermediate alloy to prepare an electrode block, and carrying out vacuum plasma welding and VAR smelting for three times to prepare a TA31 titanium alloy cast ingot; 2. at the phase transition point T β Performing upsetting and drawing for multiple times to obtain a primary blank; 3. at the phase transition point T β Performing multiple forging to obtain a forging blank; 4. at the phase transition point T β Drawing and deforming the blank to obtain an intermediate blank; 5. at the phase transition point T β And forming and forging to obtain the TA31 titanium alloy material. According to the invention, the TA31 titanium alloy cast ingot is sequentially subjected to multi-firing upsetting in the beta single-phase region, and is subjected to firing forging and drawing deformation in the high Wen Jin beta two-phase region, so that the alpha cluster in the obtained beta transformation body is finer, the strength and impact toughness of the TA31 titanium alloy material are improved, and the phenomena of uneven tissue and unstable performance caused by the difference of micro-region components are reduced.
Description
Technical Field
The invention belongs to the technical field of titanium alloy material processing, and particularly relates to a preparation method of a high-strength and high-toughness TA31 titanium alloy material.
Background
The TA31 titanium alloy is a high-strength and high-toughness near-alpha titanium alloy with good weldability and corrosion resistance which is independently developed in China and is mainly used for stress members, bolts, shafts, pressure-resistant shells and the like of underwater equipment. The GJB943A-2018 'specification of titanium alloy forgings for ships' prescribes that the room temperature mechanical properties of forgings should meet the following indexes: the tensile strength is more than or equal to 840MPa, the yield strength is more than or equal to 740MPa, and the impact absorption power is more than or equal to 47J; GJB9571-2018 "titanium and titanium alloy Bar Specification for ships" prescribes that the mechanical properties of the bars at room temperature should meet the following indexes: 1. when the diameter is 6-90 mm, the tensile strength is more than or equal to 880MPa, the yield strength is more than or equal to 780MPa, and the impact absorption power is more than or equal to 47J; 2. diameter of>When the thickness is 90-130 mm, the tensile strength is more than or equal to 840MPa, the yield strength is more than or equal to 760MPa, and the impact absorption power is more than or equal to 40J. In order to meet the technical indexes, the conventional process route adopted at present is to manually add a small amount of powdery TiO during alloy proportioning 2 As an oxygenation agent to ensure the strength index of the material, and then after post heat treatment, the impact absorption work is improved. To overcome the harm of oxygen addition and improve the impact toughness of the material, the current common practice is to adopt high Wen Jingtai heat treatment to obtain a small amount of alpha p +a large amount of beta Rotation Is a binary structure of the structure. The key point of the high Wen Jin heat treatment is to ensure the uniformity of chemical components and tissue structures of the material and the stability of the heat treatment environment, and certainly puts forward very strict requirements on the quality of raw materials and smelting, heat processing and heat treatment, and the production cost of the TA31 titanium alloy material is increased.
Disclosure of Invention
The invention aims to solve the technical problem of providing a preparation method of a high-strength and high-toughness TA31 titanium alloy material aiming at the defects of the prior art. According to the method, the TA31 titanium alloy cast ingot is sequentially subjected to multi-firing upsetting in the beta single-phase region, and is subjected to firing forging and drawing deformation in the high Wen Jin beta two-phase region, so that the alpha cluster in the obtained beta transformation body is finer, the strength and impact toughness of the TA31 titanium alloy material are obviously improved, and the phenomena of uneven tissue and unstable performance caused by the difference of micro-region components are effectively reduced.
In order to solve the technical problems, the invention adopts the following technical scheme: the preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized by comprising the following steps of:
step one, uniformly mixing sponge titanium and intermediate alloy to prepare an electrode block, and then carrying out vacuum plasma welding and VAR smelting for three times to prepare a TA31 titanium alloy cast ingot;
step two, casting the TA31 titanium alloy ingot obtained in the step one at a phase transition point T β Performing upsetting and drawing for multiple times to obtain a primary blank;
step three, the primary blank obtained in the step two is positioned at a phase transition point T β Performing multiple-firing forging to obtain a forging blank;
fourthly, forging the blank obtained in the third step at a phase transition point T β Drawing and deforming for 1-2 times by fire to obtain an intermediate blank;
step five, the intermediate blank obtained in the step four is positioned at a phase transition point T β Forging the alloy material to obtain a TA31 titanium alloy material; after the TA31 titanium alloy material is subjected to heat treatment, the mechanical properties meet the requirements of GJB943A-2018 on strength and impact absorption power of GJB9571-2018 on titanium and titanium alloy bar materials for ships.
For near alpha titanium alloys, the strengthening mechanism is mainly interface strengthening, i.e., strengthening of the alloy is achieved by pinning of the alpha/beta interface to the dislocations. The TA31 titanium alloy cast ingot prepared by the method is not added with external oxygen, the oxygen content is relatively low, the strength of the TA31 titanium alloy is reduced, and aiming at the problem, the TA31 titanium alloy cast ingot is firstly cast at a phase transition point T β The upper beta single-phase region is subjected to multiple-fire upsetting to fully crush the as-cast crystal grains to obtain uniform and fine original beta crystal grains, thus obtaining fine and uniform alpha in the subsequent process p The grains provide a preliminary structure foundation, and then the obtained primary blank is at a phase transition point T β Under the condition of multiple-firing forging and 1-2-firing drawing deformation, compared with the conventional method adopting post-period high Wen Jin static heat treatment to control groupThe method adopts high Wen Jin deformation to reduce the content of primary alpha phase so as to obtain more lamellar tissues, the form of an alpha 0 transformation body is further regulated and controlled while the content of the primary alpha phase is ensured, a large number of substructures such as vacancies, dislocation and the like are introduced into beta grains through the deformation of the beta grains at high temperature, the nucleation probability of secondary alpha lamellar is improved so as to obtain finer alpha bunches, and the finer alpha bunches are further formed and converted into fine equiaxed alpha phase at lower temperature or are directly reserved to room temperature, so that the strength and toughness of the TA31 titanium alloy material are effectively improved; in addition, compared with static heat treatment, even if the phase change points of the materials are different due to the difference of micro-area components in the deformation process of the high Wen Jin, the material can be improved to a certain extent in the subsequent heat deformation process, and the performance of the TA31 titanium alloy material is further ensured.
The preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized in that the mass content of oxygen in the titanium sponge in the first step is 0.045% -0.060%. Oxygen belongs to an interstitial solid solution in the titanium alloy, so that the strength of the titanium alloy can be remarkably improved, and the impact toughness of the alloy can be reduced. The invention adopts the titanium sponge with the oxygen content, effectively controls the oxygen mass content in the titanium sponge, and avoids adding a small amount of TiO while ensuring the strength allowance and impact toughness of the TA31 titanium alloy material 2 The chemical composition of the micro-area is uneven caused by the intermediate alloy.
The preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized in that the number of times of upsetting and pulling in the second step is 2-3, the forging ratio of upsetting and pulling in each time is 5.0-7.2, and the upsetting and pulling temperature is 1050-1150 ℃.
The preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized in that the drawing temperature of the multi-firing forging is (T) β -25℃)～(T β The forging ratio of each upsetting and pulling time is 3.4-6.8 at 15 ℃ below zero.
The preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized in that the drawing deformation temperature in the fourth step is (T) β -25℃)～(T β 15 ℃ below zero, the drawing deformation is firstly carried out every time when the fire is usedFlattening the forging blank to a thickness to width ratio of 1: and 2, returning to the square and rounding. The conventional drawing process is limited by drawing deformation and modes, so that the defect of core deformation easily exists in the middle blank making process, and obvious difference exists between the inner and outer tissues of the blank. Particularly, for a rod blank adopting a near beta phase transition point drawing process, the surface of the rod blank is fully recrystallized to form equiaxed grains, and the inside of the rod blank still maintains the original double-state organization structure due to insufficient deformation. Therefore, the invention increases the deformation of the core part of the bar blank by controlling the drawing deformation mode and the deformation, namely the drawing deformation is deformed by the mode of 'flattening square-round', and the deformation effect of upsetting deformation is generated approximately in the drawing process by controlling the thickness-width ratio of the flattening square, thereby increasing the crushing of the core tissue of the blank. The flat square with the preferable thickness-to-width ratio of 1:2 can lead the internal and external tissues of the forged blank to be relatively uniform and consistent after forging, and is beneficial to further improving the performance of the TA31 titanium alloy material.
The method for preparing the high-strength and high-toughness TA31 titanium alloy material is characterized in that the forming forging method in the fifth step is selected from rolling, finish forging and free forging, and the temperature of the rolling forming is (T) β -50℃)～(T β -40 ℃ below zero) and adopting precision forging and free forging forming at the temperature (T) β -40℃)～(T β -30℃)。
Compared with the prior art, the invention has the following advantages:
1. compared with the conventional preparation method combining forging and high-temperature static heat treatment, the method sequentially performs multi-firing upsetting and pulling on the TA31 titanium alloy cast ingot in the beta single-phase region, performs firing forging and elongation deformation on the high Wen Jin beta two-phase region, obtains finer alpha bundles in the beta transformation body, obviously improves the strength and impact toughness of the TA31 titanium alloy material, and effectively reduces the phenomena of uneven tissue and unstable performance caused by the difference of micro-region components.
2. The invention effectively solves the problems of insufficient structure deformation of the core part of the rod blank and large difference between the inner and outer structures in the conventional drawing and rounding process by controlling the drawing deformation mode and the deformation amount, and the obtained intermediate blank has uniform structure, thereby laying a foundation for the final structure and performance of the later-stage titanium alloy material.
3. According to the invention, through the regulation and control design of the oxygen content and the tissue morphology of the TA31 titanium alloy material, the oxygen content in the titanium sponge is controlled, the strength allowance and the impact toughness of the TA31 titanium alloy material are ensured, and meanwhile, the addition of a small amount of TiO is avoided 2 And the chemical components of the micro-area are uneven and the performance of the TA31 titanium alloy material is unstable due to the intermediate alloy.
4. The TA31 titanium alloy material prepared by the invention has uniform and fine structure after heat treatment, and meets the requirements of GJB943A-2018 on the TA31 titanium alloy material in the specification of titanium alloy forgings for ships and GJB9571-2018 on the specification of titanium alloy bars for ships.
The technical scheme of the invention is further described in detail through the drawings and the embodiments.
Drawings
FIG. 1 is a high-power structure diagram of the end face of the TA31 titanium alloy cake prepared in example 1 of the present invention.
Fig. 2 is a high-power structure diagram of the end face of the TA31 titanium alloy bar prepared in example 2 of the present invention.
Fig. 3 is a high-power structure diagram of the end face of the TA31 titanium alloy bar prepared in example 3 of the present invention.
Detailed Description
Example 1
The embodiment comprises the following steps:
step one, uniformly mixing titanium sponge and intermediate alloy to prepare an electrode block, then placing the electrode block in a vacuum plasma welding box for vacuum plasma welding, and then carrying out VAR smelting for three times to prepare a TA31 titanium alloy cast ingot with the diameter phi 640mm, and then peeling and cutting a riser; the mass content of oxygen in the titanium sponge is 0.045% and 0.046%;
step two, respectively upsetting and pulling the TA31 titanium alloy cast ingot after riser cutting obtained in the step one at 1150 ℃ and 1050 ℃ for 3 times, wherein the forging ratio of the 1 st time and the 3 rd time is 7.2, and the forging ratio of the 2 nd time is 5.0, so as to obtain a primary blank;
step three, the step two is carried outPrimary blank at T β Performing 2 times of forging at 15 ℃ below zero, wherein the forging ratio of each time of forging is 6.8, so as to obtain a forged blank;
step four, the forging blank obtained in the step three is subjected to T β Performing 1-fire drawing deformation at 15 ℃ below zero, wherein the forging blank is flattened to have a thickness-to-width ratio of 1:2, returning to the square and rounding to obtain an intermediate blank;
step five, putting the intermediate blank obtained in the step four in T β And (3) performing free forging forming at the temperature of 35 ℃ below zero for 1 time to obtain the TA31 titanium alloy cake material with the diameter of phi 200mm multiplied by 200mm (diameter multiplied by length).
As shown in fig. 1, the microstructure of the TA31 titanium alloy cake material prepared in this example is composed of a small amount of equiaxed alpha phase+beta transition body structure, and the microstructure is uniform and fine, as shown in fig. 1.
Example 2
The embodiment comprises the following steps:
step one, uniformly mixing titanium sponge and intermediate alloy to prepare an electrode block, then placing the electrode block in a vacuum plasma welding box for vacuum plasma welding, and then carrying out VAR smelting for three times to prepare a TA31 titanium alloy cast ingot with the diameter phi 640mm, and then peeling and cutting a riser; the mass content of oxygen in the titanium sponge is 0.060% and 0.059%;
step two, respectively upsetting and pulling the TA31 titanium alloy cast ingot obtained in the step one after riser cutting at 1150 ℃ and 1050 ℃ for 2 times, wherein the forging ratio of each time is 7.2, so as to obtain a primary blank;
step three, the primary blank obtained in the step two is subjected to T β Forging at 15 ℃ below zero for 1 time, wherein the forging ratio of each time is 6.8, so as to obtain a forged blank;
step four, the forging blank obtained in the step three is subjected to T β 2-time drawing deformation is carried out at the temperature of 15 ℃ below zero, and the forging blank is flattened to a thickness-to-width ratio of 1 at first after each time of drawing deformation: 2, returning to the square and rounding to obtain an intermediate blank;
step five, putting the intermediate blank obtained in the step four in T β Performing 2 times of fire at-30deg.CForging to obtain the TA31 titanium alloy bar with the diameter phi of 52 mm.
As shown in fig. 2, the microstructure of the TA31 titanium alloy bar prepared in this example is composed of a small amount of equiaxed alpha phase, short rod-shaped alpha phase and beta transition body structure, and the microstructure is uniform and fine.
Example 3
The embodiment comprises the following steps:
step one, uniformly mixing titanium sponge and intermediate alloy to prepare an electrode block, then placing the electrode block in a vacuum plasma welding box for vacuum plasma welding, and then carrying out VAR smelting for three times to prepare a TA31 titanium alloy cast ingot with the diameter phi 640mm, and then peeling and cutting a riser; the mass content of oxygen in the titanium sponge is 0.055% and 0.0565%;
step two, respectively upsetting and pulling the TA31 titanium alloy cast ingot obtained in the step one after riser cutting at 1150 ℃ and 1050 ℃ for 2 times, wherein the forging ratio of each time is 7.2, so as to obtain a primary blank;
step three, the primary blank obtained in the step two is subjected to T β Forging at 25 ℃ below zero for 1 time with a forging ratio of 3.4 to obtain a forging blank;
step four, the forging blank obtained in the step three is subjected to T β 2-time drawing deformation is carried out at the temperature of 25 ℃ below zero, and the forging blank is flattened to a thickness-to-width ratio of 1 at first after each time of drawing deformation: 2, returning to the square and rounding to obtain an intermediate blank;
step five, putting the intermediate blank obtained in the step four in T β Performing finish forging at-30deg.C for 2 times, and then at T β And (3) performing fire rolling at the temperature of 40 ℃ below zero to obtain the TA31 titanium alloy bar with the diameter phi of 35 mm.
As a result of observing the microstructure of the end face of the TA31 titanium alloy bar prepared in this example after heat treatment, as shown in fig. 3, it is clear from fig. 3 that the microstructure of the TA31 titanium alloy bar is composed of a small amount of equiaxed alpha phase+beta transition body structure, and the microstructure is uniform and fine.
The mechanical properties of the TA31 titanium alloy cakes and TA31 titanium alloy bars prepared in examples 1 to 3 of the present invention were measured, and the results are shown in table 1.
TABLE 1
As can be seen from Table 1, the TA31 titanium alloy materials prepared in examples 1 to 3 of the present invention were heat-treated to have the strength including the tensile strength Rm and the yield strength Rp 0.2 The titanium alloy material and the impact absorbing power KV2 meet the requirements of TA31 titanium alloy materials in GJB943A-2018 'titanium alloy forging Specification for ships and GJB 9571-2018' titanium and titanium alloy rod Specification for ships, thereby meeting the requirements of TA31 titanium alloy materials for ships and simultaneously meeting the standard requirements in the two specifications in the extensibility A.
The above description is only of the preferred embodiments of the present invention, and is not intended to limit the present invention. Any simple modification, variation and equivalent variation of the above embodiments according to the technical substance of the invention still fall within the scope of the technical solution of the invention.
Claims (1)
1. The preparation method of the high-strength and high-toughness TA31 titanium alloy material is characterized by comprising the following steps of:
step one, uniformly mixing sponge titanium and intermediate alloy to prepare an electrode block, and then carrying out vacuum plasma welding and VAR smelting for three times to prepare a TA31 titanium alloy cast ingot; the mass content of oxygen in the titanium sponge is 0.045% -0.060%;
step two, casting the TA31 titanium alloy ingot obtained in the step one at a phase transition point T β Performing upsetting and drawing for multiple times to obtain a primary blank; the times of the upsetting and pulling are 2-3, the forging ratio of each upsetting and pulling is 5.0-7.2, and the upsetting and pulling temperature is 1050-1150 ℃;
step three, the primary blank obtained in the step two is positioned at a phase transition point T β Performing multiple-firing forging to obtain a forging blank; the temperature of the multi-firing forging is (T) β -25℃）~（T β -15 ℃ and the forging ratio of each forging change is 3.4-6.8;
fourthly, forging the blank obtained in the third step at a phase transition point T β Performing drawing deformation for 1-2 times to obtain an intermediate blank; the temperature of the elongation deformation is (T) β -25℃）~（T β -15 ℃ and flattening the forging blank to a thickness-to-width ratio of 1 after each hot drawing deformation: 2, returning to the square and rounding;
step five, the intermediate blank obtained in the step four is positioned at a phase transition point T β Forging the alloy material to obtain a TA31 titanium alloy material; the mechanical properties of the TA31 titanium alloy material after heat treatment meet the requirements of GJB943A-2018 on strength and impact absorption power of GJB9571-2018 on titanium and titanium alloy bar specification for ships; the method of forming forging is selected from rolling, finish forging and free forging, and the temperature of the forming by rolling is (T) β -50℃）~（T β -40 ℃ below zero) and adopting precision forging and free forging forming at the temperature (T) β -40℃）~（T β -30℃）。
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Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102418060A (en) * | 2011-12-12 | 2012-04-18 | 西部钛业有限责任公司 | Processing method for TC4 titanium alloy large-sized bar |
| CN103397289A (en) * | 2013-08-11 | 2013-11-20 | 西北有色金属研究院 | Preparation method of TC4ELI titanium alloy bar |
| CN105063426A (en) * | 2015-09-14 | 2015-11-18 | 沈阳泰恒通用技术有限公司 | Titanium alloy and application of titanium alloy to machining of train connecting piece |
| CN105177355A (en) * | 2015-07-17 | 2015-12-23 | 西部超导材料科技股份有限公司 | Near-alpha titanium alloy with high dynamic performance and preparation method of near-alpha titanium alloy |
| CN107604283A (en) * | 2017-09-28 | 2018-01-19 | 湖南金天钛业科技有限公司 | A kind of method for producing big specification Ti55531 alloy biscuits |
| CN108097852A (en) * | 2017-12-18 | 2018-06-01 | 西安赛特思迈钛业有限公司 | A kind of forging method of TC4 titanium alloy large sizes bar |
| CN108950263A (en) * | 2018-06-28 | 2018-12-07 | 洛阳双瑞精铸钛业有限公司 | A kind of preparation method of high impact toughness TA24 sheet alloy |
| CN111057903A (en) * | 2019-12-09 | 2020-04-24 | 湖南湘投金天科技集团有限责任公司 | Large-size titanium alloy locking ring and preparation method thereof |
| CN112080656A (en) * | 2020-09-10 | 2020-12-15 | 西北有色金属研究院 | Preparation method of high-strength titanium alloy rod for additive manufacturing powder making |
| CN112795812A (en) * | 2020-12-30 | 2021-05-14 | 西安西工大超晶科技发展有限责任公司 | TC4 titanium alloy bar and preparation method thereof |
| CN113182476A (en) * | 2021-04-28 | 2021-07-30 | 西部钛业有限责任公司 | Preparation method of high-strength TC11 titanium alloy forging |
| RU2758045C1 (en) * | 2021-02-02 | 2021-10-25 | Общество с ограниченной ответственностью «Хермит Рус» | Method for producing billets in the form of a bar from (a+b)-titanium alloys |
-
2022
- 2022-02-08 CN CN202210118404.5A patent/CN114433765B/en active Active
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102418060A (en) * | 2011-12-12 | 2012-04-18 | 西部钛业有限责任公司 | Processing method for TC4 titanium alloy large-sized bar |
| CN103397289A (en) * | 2013-08-11 | 2013-11-20 | 西北有色金属研究院 | Preparation method of TC4ELI titanium alloy bar |
| CN105177355A (en) * | 2015-07-17 | 2015-12-23 | 西部超导材料科技股份有限公司 | Near-alpha titanium alloy with high dynamic performance and preparation method of near-alpha titanium alloy |
| CN105063426A (en) * | 2015-09-14 | 2015-11-18 | 沈阳泰恒通用技术有限公司 | Titanium alloy and application of titanium alloy to machining of train connecting piece |
| CN107604283A (en) * | 2017-09-28 | 2018-01-19 | 湖南金天钛业科技有限公司 | A kind of method for producing big specification Ti55531 alloy biscuits |
| CN108097852A (en) * | 2017-12-18 | 2018-06-01 | 西安赛特思迈钛业有限公司 | A kind of forging method of TC4 titanium alloy large sizes bar |
| CN108950263A (en) * | 2018-06-28 | 2018-12-07 | 洛阳双瑞精铸钛业有限公司 | A kind of preparation method of high impact toughness TA24 sheet alloy |
| CN111057903A (en) * | 2019-12-09 | 2020-04-24 | 湖南湘投金天科技集团有限责任公司 | Large-size titanium alloy locking ring and preparation method thereof |
| CN112080656A (en) * | 2020-09-10 | 2020-12-15 | 西北有色金属研究院 | Preparation method of high-strength titanium alloy rod for additive manufacturing powder making |
| CN112795812A (en) * | 2020-12-30 | 2021-05-14 | 西安西工大超晶科技发展有限责任公司 | TC4 titanium alloy bar and preparation method thereof |
| RU2758045C1 (en) * | 2021-02-02 | 2021-10-25 | Общество с ограниченной ответственностью «Хермит Рус» | Method for producing billets in the form of a bar from (a+b)-titanium alloys |
| CN113182476A (en) * | 2021-04-28 | 2021-07-30 | 西部钛业有限责任公司 | Preparation method of high-strength TC11 titanium alloy forging |
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