CN112676503A - Forging processing method for TC32 titanium alloy large-size bar - Google Patents
Forging processing method for TC32 titanium alloy large-size bar Download PDFInfo
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Abstract
The invention relates to the technical field of titanium alloy forging, and particularly discloses a forging processing method of a TC32 titanium alloy large-size bar. The invention can realize the precise regulation and control of the tissue to obtain the required mechanical property, improve the consistency of the flaw detection level of the bar, ensure the uniform tissue and performance and increase the yield.
Description
Technical Field
The invention relates to the technical field of titanium alloy, in particular to a forging processing method of a TC32 titanium alloy large-size bar.
Background
The titanium alloy has the characteristics of low density, high specific strength, good corrosion resistance, low elastic modulus, small heat conductivity coefficient, high yield ratio and the like, and has been applied to the fields of aviation, aerospace, ships, chemical engineering, petroleum and the like, wherein in the field of aviation, the titanium alloy is used as one of main structural materials of modern advanced airplanes, is mainly used for undercarriage components of airplanes, is used for skins, frames, beams, heat shields, shells and the like of airframes, and the like, and when a large amount of advanced titanium alloy materials are adopted, one of remarkable marks of the advancement of the new generation airplanes can greatly improve the structural weight reduction effect and the safety reliability.
With the development of the design principle of airplane design from pure static strength to safety-life, damage-safety and the current damage tolerance, the titanium alloy material gradually develops from the direction of pursuing single high strength or high fatigue performance to damage tolerance type comprehensive high performance such as medium and high strength, high modulus, high toughness, low crack propagation rate, good fatigue performance and the like. Typical representatives abroad are a strength damage tolerance type titanium alloy in Ti-6Al-4V beta ELI and a Ti-62222S high strength damage tolerance type titanium alloy. The medium-strength damage tolerance type titanium alloy TC4-DT and the high-strength damage tolerance type titanium alloy TC21 are also developed in China successively. At present, TC4-DT titanium alloy is used for manufacturing integrated large-sized frame, beam, joint and other key force-bearing components. The TC21 titanium alloy is used as a high-strength high-toughness damage tolerance type titanium alloy and can be used for large integral forgings and large welding integral components.
With the updating of weaponry, the requirements of high indexes of titanium alloy materials in China are met, and simultaneously, higher requirements on the uniformity and stability of titanium alloy products are provided. The domestic titanium alloy raw material generally has the defects of long processing period, multiple fire times, high cost and the like. For raw materials, excessive forging fire can lead to excessively fine structures, the fine structures can reduce the process window of a small forging, and the final product cannot obtain the optimal comprehensive mechanical property. However, the forging process is less, which easily causes uneven structure, and the free end of the bar is too long, which causes great loss of raw materials. In particular to key structural parts with important application, higher requirements on the structural uniformity and batch stability of the titanium alloy bar are provided.
The TC32 titanium alloy is a novel medium-high-toughness titanium alloy, has excellent comprehensive performance, has good matching of strength-plasticity-toughness-fatigue performance-damage tolerance performance, and has comprehensive performance superior to the similar medium-high-toughness titanium alloys such as TC4 (American Ti6Al 4V) and TA15 (Russian BT 20). The alloy is suitable for various processes of two-phase region forging, quasi-beta heat treatment, two-phase region forging, two-phase region heat treatment, quasi-beta forging and two-phase region heat treatment and the like, da/dN is equivalent to TC4-DT titanium alloy in a lamellar structure state, da/dN is equivalent to TC21 titanium alloy in a basket structure state, and meanwhile, the alloy has good fatigue performance and very wide application prospect.
According to the background, the technical research on machining of phi 210 mm-phi 380mm bars is carried out on the novel TC32 titanium alloy, so that the low-cost and large-scale stable production of TC32 large-size bars is realized, and the development requirement of the aviation industry is met.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a forging processing method of a TC32 titanium alloy large-size bar to produce the large-size bar with the diameter phi of 210-380 mm, wherein the titanium alloy bar is an alpha + beta two-phase structure, the uniformity of the bar structure is good, the mechanical property is stable, and the forging processing method is suitable for industrial production.
In order to achieve the purpose, the invention adopts the technical scheme that: a forging processing method of TC32 titanium alloy large-size bars is characterized in that the bars are subjected to recrystallization homogenization forging after cogging forging, then forged below a beta transition temperature, and finally forged into finished products.
Further, the forging processing method of the TC32 titanium alloy large-specification bar is realized by the following steps:
cogging and forging
Carrying out upsetting-drawing forging on TC32 cast ingots for 1-2 times at 1150-1200 ℃, controlling the total forging ratio of a single fire to be 5-10, controlling the height-diameter ratio of the final blank to be 1.3-1.5, and carrying out air cooling after forging;
(II) homogenization forging
Heating to 30-50 ℃ below the beta transition temperature, carrying out 1-time upsetting-drawing forging on the blank in the step (I), controlling the forging ratio to be 1.6-2.1, controlling the height-diameter ratio of the forged blank to be 1.3-1.5, directly returning to the furnace after forging to 70-100 ℃ above the beta transition temperature, preserving heat for a proper time, and discharging from the furnace;
forging below (III) beta transition temperature
Heating to 30-70 deg.C below beta transition temperature, and finishing with 3-6 fire;
(IV) forging the finished product
And (5) performing 1-2 fire finished product forging on the blank processed in the step (three).
Further, in the step (II), the holding time of the homogenizing forging is calculated according to the minimum sectional dimension of the billet x the heating coefficient delta (min/mm), and the heating coefficient delta is generally 0.4-0.7.
Further, in the step (II), after the heating is finished at 70-100 ℃ above the beta transition temperature, the first upsetting and the first drawing are carried out, the total upsetting and drawing forging ratio is controlled to be 1.0-1.3, the height-diameter ratio of the forged blank is controlled to be 1.3-1.5, and air cooling or water cooling is adopted after forging.
Further, in the step (III), the 1 st fire is carried out for reversing upsetting forging at the temperature of 30-70 ℃ below the beta transition temperature, the upsetting deformation is controlled to be 20-30%, air cooling is carried out after the upsetting deformation is finished, the 2 nd to 6 th fires are drawing forging, and the drawing forging ratio of each fire is controlled to be 1.4-1.6.
Further, in the step (IV), the finished product is forged by adopting a V-shaped anvil for drawing, and the forging ratio of each fire is controlled to be 1.1-1.3.
Compared with the prior art, the invention has the beneficial effects that:
(1) on the basis of conventional free forging, a recrystallization homogenization forging technology is integrated in cogging forging, so that the titanium alloy material is subjected to static recrystallization to realize rapid refinement and homogenization of the structure, the method is simple and controllable, and the precise regulation and control of the structure can be realized by regulating and controlling forging parameters to obtain the required mechanical property; meanwhile, the problems that the structure is uneven and the beta crystal grains are too fine due to the fact that the beta crystal grains are crushed by multiple fire times and large deformation in a single-phase region in the conventional free forging, and the strength and toughness of the final bar and the forging are poor in matching are solved;
(2) the method adopts reversing upsetting and drawing when forging below the beta transition temperature, strictly controls the height-diameter ratio of the blank entering a two-phase area to be 1.3-1.5, reduces the risk of overheating the blank caused by large deformation amount of the reversing upsetting and drawing, enables the deformation of a difficult deformation area of the blank to be more sufficient, obtains uniform tissues and properties and low anisotropy, improves the consistency of the flaw detection level of the bar, reduces the free end of the bar and increases the yield;
(3) the method is particularly suitable for industrial production of large titanium alloy bars, the forging process is simple and controllable, and the large TC32 titanium alloy bars with good structure uniformity, excellent comprehensive performance, low cost and stable batch can be produced;
(4) the fire times for producing phi 380mm multiplied by 3000-4000mm bars are only 8 fire, and the fire times for producing phi 210mm multiplied by 2800-3500mm bars are only 7 fire, so that the processing cost is reduced by about 30 percent compared with the 12-16 fire processing cost of the traditional titanium alloy forging, the comprehensive yield is improved by about 5 percent, and the method is suitable for industrial production;
(5) the TC32 titanium alloy bar produced by the method can be used for various processes such as two-phase region forging and quasi-beta heat treatment, two-phase region forging and two-phase region heat treatment, quasi-beta forging and two-phase region heat treatment and the like, and has wide applicability.
Drawings
FIG. 1 is a macroscopic structural diagram of a bar material with a diameter of 210mm prepared in the first embodiment of the present invention;
FIG. 2 is a schematic diagram of an air-fired macrostructure of a bar with a diameter of 210mm prepared in the first embodiment of the present invention;
FIG. 3 is a microstructure (200X) of a 210mm diameter bar prepared in accordance with a first embodiment of the present invention;
FIG. 4 is a macrostructure diagram of a bar material with a size of 380mm phi prepared in the second embodiment of the present invention;
FIG. 5 is a schematic diagram of the air-fired macrostructure of a bar material with a diameter of 380mm prepared in the second embodiment of the present invention;
FIG. 6 is a microstructure (200X) of a 380mm diameter bar prepared in example two of the present invention.
Detailed Description
The invention will now be further elucidated with reference to specific embodiments. The following are only preferred embodiments of the present invention and are not intended to limit the scope of the present invention. Any similar or equivalent substitution should be made within the scope of the present invention without departing from the spirit of the present invention. And the details which are not described below should be performed according to the conventional techniques in the art. The following are: "o" refers to the height of a billet with an octagonal cross-section, "□" refers to the height of a billet with a square cross-section, and "Φ" refers to the diameter of a billet with a circular cross-section.
EXAMPLE one (phi 210mm size bar forging method)
Selecting a TC32 titanium alloy cast ingot with the specification of phi 780mm, wherein the beta transition temperature of the cast ingot is 905 ℃. The specific forging process is as follows:
cogging and forging
Finishing divided 2 fires, heating the TC32 cast ingot to 1150 ℃ by the 1 st fire, preserving heat, discharging the ingot from a furnace, performing two-upsetting and two-drawing to a square, controlling the forging ratio to be 9-10, controlling the height-diameter ratio of the blank to be about 2.0, and performing air cooling after forging; heating and preserving heat at 1080 ℃ by fire 2, performing two-upsetting two-drawing forging to the eight directions, controlling the forging ratio to be 9-10, finally controlling the height-diameter ratio of the blank to be 1.5, and performing air cooling after forging;
(II) homogenization forging
Firstly, heating the blank in the step (I) to 870 ℃, preserving heat, performing one-upsetting one-drawing forging to an octagon after discharging, controlling the forging ratio to be 2.1, controlling the height-diameter ratio of the blank after forging to be 1.5, directly returning to 990 ℃ after forging, controlling the material returning and transferring time to be not more than 120s, controlling the heat preservation time to be 330-360min, performing one-upsetting one-drawing forging to an octagon after discharging, controlling the forging ratio to be 1.26, controlling the height-diameter ratio of the blank to be 1.5, and cooling by water after forging;
forging below (III) beta transition temperature
And (5) carrying out 5-time forging on the blank processed in the step (II) to 230mm in eight directions. Wherein, the 1-step heating is reversing upsetting-drawing forging, the heating temperature is 875 ℃, the two-upsetting-two-drawing forging is carried out to the eight direction, the upsetting deformation is controlled at 25 percent, and air cooling is carried out after forging; drawing out and forging the rest 4 fires, wherein the heating temperature is 870 ℃, the forging ratio of each fire is controlled to be 1.5-1.6, finally forging to 230mm in eight directions, and air cooling is adopted after forging;
(IV) forging the finished product
And (3) after the blank material which is subjected to the step (III) is heated at 865 ℃, performing round throwing and drawing by adopting a V-shaped anvil until the size of the finished product is achieved, controlling the drawing-forging ratio to be 1.13, and finally obtaining the finished product with the specification of phi 210mm bar.
FIG. 1 is a photograph of R-state macrostructure of a bar material with a diameter of 210mm prepared by forging according to the first process of example, and it can be seen that the R-state macrostructure has no obvious metallurgical defect and the macrostructure is fuzzy; FIG. 2 is a photograph of the bar after being air-fired, which shows that the bar after being air-fired has a uniform macrostructure and fine grains; FIG. 3 is a photograph showing the microstructures of the edge, R/2 and core of the corresponding bar, and it can be seen that the microstructures from the edge to the core are very uniform. Table 1 shows the mechanical properties of the corresponding bars, and it can be seen that the bars have excellent comprehensive properties:
EXAMPLE two (phi 380mm size bar forging method)
Selecting a TC32 titanium alloy cast ingot with the specification of phi 780mm, wherein the beta transition temperature of the cast ingot is 905 ℃. The specific forging process is as follows:
cogging and forging
Heating TC32 cast ingots to 1150 ℃ for heat preservation, taking the cast ingots out of a furnace for two upsetting and two drawing to eight directions, controlling the forging ratio to be 5-6, after the second upsetting is finished, adopting diagonal drawing to 600mm, controlling the height-diameter ratio of the ingots to be 1.5, and adopting air cooling after forging;
(II) homogenization forging
Firstly, heating the blank in the step (I) to 875 ℃ for heat preservation, performing one-upsetting one-drawing forging to an octagon after discharging, controlling the forging ratio to be 1.6, controlling the height-diameter ratio of the blank after forging to be 1.5, directly returning to 990 ℃ after forging, controlling the material returning and transferring time to be not more than 120s, controlling the heat preservation time to be 330-360min, performing one-upsetting one-drawing forging to the octagon 600mm after discharging, controlling the forging ratio to be 1.26, controlling the height-diameter ratio of the blank to be 1.5, and performing air cooling after forging;
forging below (III) beta transition temperature
Forging the blank processed in the step (II) for 3 times to an octagon 410mm, wherein 1 fire is reversing upsetting forging, the heating temperature is 875 ℃, two-upsetting and two-drawing forging is carried out to the octagon, the upsetting deformation is controlled at 30%, and air cooling is carried out after forging; drawing out and forging the rest 2 fires, controlling the heating temperature to 870 ℃, controlling the forging ratio at 1.5-1.6 every fire, finally forging to 410mm in eight directions, and air cooling after forging;
(IV) forging the finished product
And (3) after the blank material which is subjected to the step (III) is heated at 865 ℃, performing round throwing and drawing by adopting a V-shaped anvil until the size of the finished product is achieved, controlling the drawing-forging ratio to be 1.13, and finally obtaining the finished product with the specification of a phi 380mm rod material.
FIG. 4 is a photograph of the R-state macrostructure of a bar material with a specification of phi 380mm prepared by forging according to the second process of example, and it can be seen that the R-state macrostructure has no obvious metallurgical defect and has uniform and fine structure; FIG. 5 is a photograph of the bar after being air-fired, and it can be seen that the bar after being air-fired has a uniform macrostructure and fine grains; FIG. 6 is a photograph of the microstructures of the edge, R/2 and core of the corresponding bar, and it can be seen that the microstructures from the edge to the core are very uniform. Table 1 shows the mechanical properties of the corresponding bars, and the bars have excellent comprehensive properties.
TABLE 1 TC32 mechanical properties of titanium alloy bars
Claims (6)
1. A forging processing method of TC32 titanium alloy large-size bars is characterized in that the bars are subjected to recrystallization homogenization forging after cogging forging, then forged below a beta transition temperature, and finally forged into finished products.
2. The forging processing method of the TC32 titanium alloy large-size bar according to claim 1, which is realized by the following steps:
cogging forging
Carrying out upsetting-drawing forging on TC32 cast ingots for 1-2 times at 1150-1200 ℃, controlling the total forging ratio of a single fire to be 5-10, controlling the height-diameter ratio of the final blank to be 1.3-1.5, and carrying out air cooling after forging;
(II) homogenization forging
Heating to 30-50 ℃ below the beta transition temperature, carrying out 1-time upsetting-drawing forging on the blank in the step (I), controlling the forging ratio to be 1.6-2.1, controlling the height-diameter ratio of the forged blank to be 1.3-1.5, directly returning to the furnace after forging to 70-100 ℃ above the beta transition temperature, preserving heat for a proper time, and discharging from the furnace;
forging below (III) beta transition temperature
Heating to 30-70 deg.C below beta transition temperature, and finishing with 3-6 fire;
(IV) forging the finished product
And (5) performing 1-2 fire finished product forging on the blank processed in the step (three).
3. The forging method of TC32 large-sized bar of titanium alloy according to claim 2, wherein in the step (II), the holding time of the homogenization forging is calculated according to the minimum sectional dimension of the billet x the heating coefficient delta (min/mm), and the heating coefficient delta is generally 0.4-0.7.
4. The forging method of TC32 large-sized bar of titanium alloy as claimed in claim 2, wherein in step (II), after heating above the β -transus temperature by 70-100 ℃, upsetting-drawing is performed, the total upsetting-drawing forging ratio is controlled to be 1.0-1.3, the height-diameter ratio of the forged blank is controlled to be 1.3-1.5, and air cooling or water cooling is employed after forging.
5. The forging processing method of TC32 titanium alloy large-size bar as claimed in claim 2, 3 or 4, wherein in step (III), the reverse upsetting forging is performed at the 1 st fire 30-70 ℃ below the beta-transus temperature, the upsetting deformation is controlled at 20-30%, air cooling is performed after completion, the 2 nd to 6 th fires are drawing forging, and the drawing forging ratio is controlled at 1.4-1.6 per fire.
6. The method for forging large-size TC32 titanium alloy bars according to claim 5, wherein in step (IV), the finished product is forged by V-anvil drawing, and the forging ratio is controlled to be 1.1-1.3 per fire.
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| CN112935163A (en) * | 2021-01-22 | 2021-06-11 | 西安瑞达金属材料科技有限公司 | Radial forging method for infinite deformation of titanium alloy bar |
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| CN114147161A (en) * | 2021-12-10 | 2022-03-08 | 湖南金天钛业科技有限公司 | Drawing forging method for relieving anisotropy of ultrahigh-strength titanium alloy bar |
| CN114178456A (en) * | 2021-11-26 | 2022-03-15 | 湖南金天钛业科技有限公司 | Forging processing method for oversized titanium alloy forging stock |
| CN114226618A (en) * | 2021-12-07 | 2022-03-25 | 太原科技大学 | Reverse control process for finish forging forming of large-scale shaft forgings based on mixed crystal regulation |
| CN114850367A (en) * | 2022-05-28 | 2022-08-05 | 西部超导材料科技股份有限公司 | Preparation method of Ti6246 titanium alloy large-size bar |
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| CN115595521A (en) * | 2022-10-19 | 2023-01-13 | 湖南湘投金天钛业科技股份有限公司（Cn） | Forging method of Ti17 titanium alloy large-size bar with high structural uniformity |
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