CN111763850B - Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate - Google Patents
Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate Download PDFInfo
- Publication number
- CN111763850B CN111763850B CN202010669587.0A CN202010669587A CN111763850B CN 111763850 B CN111763850 B CN 111763850B CN 202010669587 A CN202010669587 A CN 202010669587A CN 111763850 B CN111763850 B CN 111763850B
- Authority
- CN
- China
- Prior art keywords
- forging
- titanium alloy
- upsetting
- heating
- rolling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
Abstract
The invention discloses a processing method of a fine-grain superplasticity TA15 titanium alloy medium-thickness plate, which comprises the following steps: firstly, obtaining a TA15 titanium alloy ingot through vacuum consumable arc melting; secondly, upsetting, drawing, cogging and forging the mixture after heat preservation to obtain a primary forging stock; thirdly, upsetting, drawing and forging the mixture in a beta phase region after heat preservation to obtain a secondary forging stock; fourthly, upsetting, drawing and forging the alpha + beta two-phase region to obtain a four-grade forging stock; fifthly, obtaining a forged piece through upsetting, drawing and final forging; sixthly, performing heat preservation and then performing one-fire rolling to obtain a one-fire rolling plate blank; seventhly, performing heat preservation and then performing second-heat rolling to obtain a second-heat rolling plate blank; eighthly, annealing to obtain the TA15 titanium alloy medium plate. The method selects the corresponding deformation temperature, combines the upsetting forging with multiple times of heating and large deformation, ensures that the TA15 titanium alloy ingot with large tissue thickness is crushed under large deformation, provides driving force for recrystallization, improves the grain refinement and homogenization degree, and obtains the fine-grain superplasticity TA15 titanium alloy medium plate.
Description
Technical Field
The invention belongs to the technical field of titanium alloy material processing, and particularly relates to a processing method of a fine-grain superplasticity TA15 titanium alloy medium-thickness plate.
Background
The fine-grain titanium alloy has higher superplasticity, can be processed into thin-wall structural parts through superplastic forming, can widely replace various precision castings and forgings of aircrafts, is used for manufacturing complex structural parts of aircrafts such as missile empennages, missile shells and the like, has obvious weight reduction effect, and greatly improves the effective load. The member generally has the characteristics of high rib and thin web, is complex in shape, has large projection area and has high requirements on tissue performance.
The TA15 titanium alloy has good comprehensive mechanical properties, the strength, the fracture toughness, the fatigue limit and the stress corrosion resistance of the TA15 titanium alloy are slightly higher than those of the TC4 titanium alloy, and the TA15 titanium alloy can be used as a titanium alloy material for an airplane structure, is used for manufacturing important structural parts with higher working temperature and more complex stress, such as an airplane bulkhead, a wallboard and the like, and is widely applied in China at present, wherein the TA15 titanium alloy is most widely applied to plates and is mainly applied to aeronautical key components such as an engine case, a welding bearing frame and the like. However, the TA15 titanium alloy has the problems of large deformation resistance, narrow deformation temperature range, strong tissue sensitivity, large crystal grains, uneven tissue and the like easily occurring in the plate preparation process, so that the thick plate in the titanium alloy has unstable quality, low yield and low superplasticity, and the application of the thick plate in the titanium alloy in high-end fields is limited.
The traditional TA15 titanium alloy medium plate processing technology generally adopts one-way rolling, the direction of the plate is not changed in the rolling process, crystal grains deform along one direction in the rolling process, so that the difference of transverse and longitudinal microstructures is large, the plate processing streamline is obvious, and the surface of the plate can generate 'furrows' along the rolling direction.
Disclosure of Invention
The invention aims to solve the technical problem of providing a method for processing a fine-grain superplasticity TA15 titanium alloy medium-thickness plate aiming at the defects of the prior art. According to the invention, the corresponding deformation temperature is selected according to the phase transition temperature, the temperature rise caused by deformation is controlled below the phase transition temperature, and then multiple-fire upsetting forging with large deformation is adopted, so that the TA15 titanium alloy ingot with large tissue thickness is sequentially crushed step by step under large deformation, a driving force is provided for recrystallization of the crushed crystal grains, the refinement and homogenization degree of the crystal grains is improved, the structure is refined while the alpha phase is fully crushed, the structures inside and outside the TA15 titanium alloy medium plate are close to the same, and the fine-grain superplastic TA15 titanium alloy medium plate is finally obtained.
In order to solve the technical problems, the invention adopts the technical scheme that: a processing method of a fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized by comprising the following steps:
step one, smelting: according to the design components of the target alloy, mixing, electrode pressing and assembly welding are sequentially carried out on 0-grade titanium sponge and the intermediate alloy, then TA15 titanium alloy cast ingot is obtained through three times of vacuum consumable arc melting, and local defects on the surface of the TA15 titanium alloy cast ingot are cleaned;
step two, cogging and forging: putting the TA15 titanium alloy ingot cleaned in the step one into an electric furnace and putting the ingot into the electric furnace for Tβ+160℃～TβHeating and preserving heat at the temperature of +180 ℃, then adopting a rapid forging machine of more than 2000t to perform upsetting, drawing, cogging and forging, and performing air cooling to obtain a primary forging stock; the T isβThe beta-phase transformation temperature of the TA15 titanium alloy is given as the unit, and the ratio of height to diameter adopted by the upsetting-cogging forging is (2-2.5): 1;
step three, upsetting-drawing forging of a beta phase region: putting the primary forging stock obtained in the step two into an electric furnace and putting the primary forging stock into the electric furnace for Tβ+60℃～TβHeating and preserving heat at the temperature of 80 ℃, then adopting a rapid forging machine or a press machine with the temperature of more than 2000t to perform beta-phase region upsetting forging, and performing air cooling to obtain a secondary forging stock; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2-2.5): 1;
step four, upsetting, drawing and forging the alpha + beta two-phase region: putting the secondary forging stock obtained in the third step into an electric furnace and putting the secondary forging stock into the electric furnace for Tβ-25℃～TβHeating and preserving heat at minus 30 ℃, then carrying out first upsetting-drawing forging on an alpha + beta two-phase region by adopting a rapid forging machine or a press machine of more than 2000T, cooling to obtain a three-stage forging stock, and continuously carrying out T-stage forging on the three-stage forging stockβ-25℃～TβHeating and preserving heat at the temperature of minus 30 ℃, then adopting a rapid forging machine or a press machine with the temperature of more than 2000t to perform secondary upsetting-drawing forging in an alpha + beta two-phase region, and obtaining a four-stage forging stock after air cooling; the height-diameter ratios adopted by the first upsetting forging of the alpha + beta two-phase region and the second upsetting forging of the alpha + beta two-phase region are (2-2.5): 1;
step five, finish forging and forging: putting the four-stage forging stock obtained in the fourth step into an electric furnace and putting the four-stage forging stock into the electric furnace for Tβ-30℃～TβHeating and preserving heat at the temperature of minus 40 ℃, then carrying out upsetting finish forging, and carrying out air cooling to obtain a forged piece; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2-2.5): 1, the thickness of the forging is 200-220 mm;
step six, rolling in one fire: heating and insulating the forge piece obtained in the fifth step, and then carrying out first-pass rolling for 6-8 passes by using a hot rolling mill to obtain a first-pass rolling plate blank; the thickness of the one-fire rolling plate blank is 50 mm-80 mm;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat, and then carrying out 4-6-pass second-heat rolling by using a hot rolling mill to obtain a second-heat rolling plate blank; the thickness of the second-fire rolling plate blank is 10-25 mm;
step eight, slab processing: annealing the two-fire rolled plate blank obtained in the step seven, and then sequentially polishing and shearing to obtain a TA15 titanium alloy medium plate; the thickness of the TA15 titanium alloy medium plate is 10 mm-25 mm, the average grain size is not more than 20 μm, and the TA15 titanium alloy medium plate has the transverse elongation of more than 420% and the longitudinal elongation of more than 340% at the temperature of 850-930 ℃.
Superplastic sheet materials are typically characterized by a fine and uniform texture. The TA15 titanium alloy is a near-alpha titanium alloy, the performance of the alloy is difficult to adjust through heat treatment, and in order to improve the superplastic performance, the invention refines grains through thermal deformation to improve the superplastic performance.
The method comprises the steps of sequentially carrying out cogging forging, beta-phase region upsetting forging, alpha + beta two-phase region upsetting forging and finish forging on a TA15 titanium alloy ingot obtained by vacuum consumable arc melting, then carrying out one-fire rolling and two-fire rolling, and then carrying out treatment to obtain the TA15 titanium alloy medium plate. According to the invention, the corresponding deformation temperature is selected according to the phase transition temperature, the temperature rise caused by deformation is controlled below the phase transition temperature, then, multiple times of upsetting and drawing forging with large deformation are adopted, so that the TA15 titanium alloy ingot with large tissue thickness is sequentially crushed step by step under the large deformation, the larger deformation provides driving force for recrystallization of the crushed crystal grains, the refinement and homogenization degree of the crystal grains is improved, the structure is refined while the alpha phase is fully crushed, the structures inside and outside the TA15 titanium alloy medium plate are close to the same and are fine-grained structures, and the fine-grained superplasticity TA15 titanium alloy medium plate is obtained.
The fine-grain superplasticity TA15 titanium alloy medium thicknessThe processing method of the plate is characterized in that in the first and second vacuum consumable arc melting processes of the three times of vacuum consumable arc melting in the step one, the vacuum degree in the vacuum consumable arc melting furnace is less than 1.0 multiplied by 10-1Pa, in the third vacuum consumable arc melting process, the vacuum degree in the vacuum consumable arc melting is less than 5.0 multiplied by 10-2Pa; in the first step, smooth transition grinding is carried out on the cleaned TA15 titanium alloy ingot, and the depth-to-width ratio of the smooth transition grinding is not more than 1:10, and the depth is not more than 10 mm. By controlling the vacuum degree in the process of three times of vacuum consumable arc melting, the content of impurity elements in the TA15 titanium alloy ingot is obviously reduced, and the uniformity and stability of the components of the TA15 titanium alloy ingot are ensured; the optimized grinding process avoids the phenomenon that folding is generated in the subsequent forging process to form cracks, and the quality of the thick plate in the TA15 titanium alloy product is influenced.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that in the step II, the heating and heat preservation mode is step heating, and the step heating process is as follows: controlling the charging temperature of TA15 titanium alloy ingot at 790-810 ℃ and preserving heat t at the charging temperature1min, then heating to Tβ+160℃～Tβ+180 ℃ and incubation t2min, wherein, t1The diameter of the titanium alloy ingot is (TA 15/3-10) min to (TA 15/3 +10) min, t2The diameter of the TA15 titanium alloy ingot is (TA15 titanium alloy ingot diameter/2 +30) min to (TA15 titanium alloy ingot diameter/2 +40) min, and the unit of the TA15 titanium alloy ingot diameter is mm; the single-pass deformation of the upsetting, cogging and forging is 25-30%, and the single-fire accumulated deformation is not less than 80%. Because the TA15 titanium alloy has low heat conduction rate and slow heat conduction in a high-temperature state, the temperature uniformity of a TA15 titanium alloy ingot after heating and heat preservation can be obviously improved by preferably adopting step heating, and a foundation is provided for subsequent forging; because the TA15 titanium alloy ingot has very coarse structure, the upsetting-cogging forging process parameters are preferably adopted, so that coarse grains of the TA15 titanium alloy ingot after multi-fire upsetting are crushed under a large deformation, the large deformation provides a driving force for the recrystallization of the crushed grains, and the homogenization process of the grainsThe degree is improved.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that the heating and heat preservation mode in the step III is step heating, and the step heating process is as follows: firstly, the charging temperature of the primary forging stock is controlled to be 790-810 ℃, and the temperature t is kept at the charging temperature1min, then heating to Tβ+60℃～Tβ+80 ℃ and incubation t2min, wherein, t1Min (maximum section size of primary forging stock/3-10) — (maximum section size of primary forging stock/3 +10) min, t2The unit of the maximum size of the section of the primary forging stock is mm (the maximum size of the section of the primary forging stock/2 +30) min- (the maximum size of the section of the primary forging stock/2 +40) min; the single-pass deformation of the beta-phase region upsetting-drawing forging is 25-40%, and the single-fire accumulated deformation is not less than 85%; the drawing forging process of the beta phase region upsetting forging adopts a deformation mode of diagonal chamfering, and the deformation amount is 35-40%. The step heating is preferably adopted, so that the temperature uniformity of the heated and insulated primary forging stock can be obviously improved, and a foundation is provided for subsequent forging; the technological parameters of the beta-phase region upsetting-drawing forging are preferably adopted, so that the crushing of coarse grains is facilitated, and the homogenization degree of the grains is improved; the preferential drawing forging process adopts a deformation mode of diagonal chamfering, so that the phenomenon of nonuniform deformation is obviously reduced, deformation dead zones are eliminated, and the uniformity of the structure and the consistency of performance are improved.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that in the step four, the process of heating and heat preservation of the first upsetting-drawing forging of the alpha + beta two-phase region is as follows: controlling the charging temperature of the secondary forging stock to be 500-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-25℃～Tβ-30 ℃ and incubation t1min; said t is1The unit of the maximum size of the section of the secondary forging stock is mm (the maximum size of the section of the secondary forging stock/2 +30) min- (the maximum size of the section of the secondary forging stock/2 +40) min; the single-pass deformation of the first upsetting-drawing forging of the alpha + beta two-phase region is 25-40%, and the single-fire accumulated deformation is not less than 85%; and the cooling mode after the first upsetting-drawing forging of the alpha + beta two-phase region is water cooling. The product has good tasteThe temperature uniformity in the secondary forging stock after heating and heat preservation is improved by selecting heating and heat preservation, and a foundation is provided for subsequent forging; the preferred alpha + beta two-phase region with large deformation is subjected to first upsetting-drawing forging, so that the full crushing and refining of crystal grains are facilitated; under the rapid cooling rate of water cooling, fine acicular martensite is precipitated from the obtained three-stage forging stock, and in the subsequent forging and rolling processes, the fine acicular martensite is crushed, broken and spheroidized in the processing process with large deformation amount to form a fine and uniform equiaxial structure.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that in the step four, the process of heating and heat preservation of the second upsetting-drawing forging of the alpha + beta two-phase region is as follows: controlling the charging temperature of the three-stage forging stock to be 450-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-30℃～Tβ-40 ℃ and incubation t2min; said t is2The unit of the maximum size of the section of the third-stage forging stock is mm; the single-pass deformation of the second upsetting-drawing forging of the alpha + beta two-phase region is 30-40%, and the single-fire accumulated deformation is not less than 85%.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that the specific process of heating and heat preservation in the fifth step is as follows: controlling the charging temperature of the four-stage forging stock to be 450-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-30℃～Tβ-40 ℃ and incubation t0min; said t is0The unit of the maximum size of the section of the four-level forging stock is mm; the single-pass deformation of the upsetting-drawing finish forging is 30-40%, and the single-fire accumulated deformation is not less than 85%.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that the heating temperature of the one-fire rolling in the sixth step is Tβ-40℃～Tβ-50 ℃ and holding time t1The thickness of the forged piece is 0.8-5 min to 0.8+ 5min, and the heat preservation time is from four-stage forged pieceStarting calculation after the furnace is placed into the heating furnace and the furnace temperature of the heating furnace is stable; the single-pass deformation of the 1 st to 3 rd passes in the one-pass rolling process is 20-25%, and the deformation of the rest single-pass is not less than 8%;
the processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that the heating temperature of the two-fire rolling in the seventh step is Tβ-50℃～Tβ-60 ℃ and holding time t2The heat preservation time is calculated from the time when the primary rolling slab enters the heating furnace and the furnace temperature of the heating furnace is stable; and the initial single-pass deformation of the two-heat rolling is 20-26%, the other single-pass deformation is 12-20%, and the two-heat rolling adopts reversing rolling, so that the direction of the two-heat rolling is perpendicular to the direction of the one-heat rolling in the step six. By adopting the reversing rolling process, the difference between the transverse deformation and the longitudinal deformation of the plate blank rolled by one fire is obviously reduced, crystal grains are uniformly deformed, the tissue defects of texture, processing streamline and the like which are unfavorable for uniformity and formed by rolling the plate blank rolled by one fire due to large unidirectional deformation are improved, the tissue uniformity is high, and the difference between the transverse performance and the longitudinal performance of the obtained plate blank rolled by two fire is small.
The preferred large deformation one-pass and two-pass rolling ensures that the rolling deformation reaches deep into the slab core, so that the rolling cross section deforms uniformly.
The processing method of the fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized in that the annealing treatment in the step eight is carried out at the temperature of 850-900 ℃ for 1-1.5 h. Because large deformation energy is accumulated in the processing process with large deformation amount, in the preferable heat treatment process, the deformation energy provides driving force for grain nodularization and recrystallization in the two-fire rolling plate blank, the grain nodularization effect is good, the recrystallization is sufficient, the structure is uniform and fine, and the problems of nonuniform structure and inconsistent performance in the rolling process of the TA15 alloy plate are solved.
Compared with the prior art, the invention has the following advantages:
1. the invention adopts multi-fire large-deformation upsetting forging to fully crush the alpha phase to achieve the purpose of refining the structure, simultaneously leads the structures inside and outside the TA15 titanium alloy medium plate to be close to consistent and to be fine-grained structures, the thickness of the finally obtained TA15 titanium alloy medium plate is 10-25 mm, the average grain size is not more than 20 mu m, the transverse elongation of the TA15 titanium alloy medium plate at the temperature of 850-930 ℃ is more than 420 percent, and the longitudinal elongation is more than 340 percent.
2. The invention adopts the reversing rolling process, obviously reduces the difference between the transverse deformation and the longitudinal deformation in the rolling process, ensures that crystal grains are uniformly deformed, improves the texture defects which are unfavorable for uniformity, such as texture, processing streamline and the like, formed by rolling the plate with larger unidirectional deformation, has high uniformity of the texture, reduces the difference between the transverse performance and the longitudinal performance of the plate, improves the plate surface quality, effectively controls the same plate difference, refines the crystal grains, reduces the anisotropy of the texture, improves the yield of the plate and finally obtains the fine-grained TA15 titanium alloy medium plate.
3. The TA15 titanium alloy is sensitive to deformation temperature, and the deformation resistance is large in the deformation process, the deformation temperature rise is severe, the grain growth is easy to cause, the structure refinement is not facilitated, and the superplasticity is improved.
4. According to the invention, the pass processing rates of the first-pass rolling and the second-pass rolling are strictly limited, a larger pass deformation rate is kept during the initial pass rolling, the high-temperature plasticity of the blank is utilized to carry out large-deformation rolling, the crystal grains are fully crushed, the pass deformation rate is reduced along with the reduction of the temperature of the blank, the cracking of the blank caused by the overlarge deformation is effectively prevented, and the surface quality of the TA15 titanium alloy medium plate is improved while the fine crystal structure is obtained.
5. The thick plate in the TA15 titanium alloy prepared by the invention has uniform structure, fine crystal grains, average crystal grain size less than or equal to 20 mu m, obviously improved mechanical property and ultrasonic flaw detection level compared with the conventional plate, and higher process controllability and batch production stability.
The technical solution of the present invention is further described in detail by the accompanying drawings and examples.
Drawings
FIG. 1 is a microstructure of a TA15 fine-grained medium-thickness plate made of titanium alloy according to example 1 of the present invention.
FIG. 2 is a microstructure of a TA15 fine-grained medium-thickness plate made of titanium alloy according to example 2 of the present invention.
FIG. 3 is a microstructure of a TA15 fine-grained medium-thickness plate made of titanium alloy according to example 3 of the present invention.
Detailed Description
In steps two to five of examples 1 to 4 of the present invention, the aspect ratio is the ratio of the length to the diameter of the ingot or the ratio of the length to the side length of each stage of the square bar-shaped forged billet to be processed correspondingly.
Example 1
The embodiment comprises the following steps:
step one, smelting: according to the design components of a target alloy, carrying out automatic material mixing, electrode pressing and assembly welding on 0-grade sponge titanium and a middle alloy in sequence, then carrying out three times of vacuum consumable arc melting to obtain a TA15 titanium alloy cast ingot with the diameter of 560mm multiplied by 2000mm (diameter multiplied by length), wherein the vacuum degree in a vacuum consumable arc melting furnace in the first time of vacuum consumable arc melting is 0.07Pa, the vacuum degree in the vacuum consumable arc melting furnace in the second time of vacuum consumable arc melting is 0.05Pa, the vacuum degree in the vacuum consumable arc melting furnace in the third time of vacuum consumable arc melting is 0.01Pa, then carrying out split cleaning after peeling and grinding on the TA15 titanium alloy cast ingot, and then carrying out smooth transition grinding, wherein the depth-to-width ratio of the smooth transition grinding is 1:12, and the depth is 8 mm;
step two, cogging and forging: putting the TA15 titanium alloy ingot cleaned in the step one into an electric furnace, and controlling the loading of the ingotThe furnace temperature is 800 ℃, the temperature is kept for 180min at the charging temperature, then the temperature is raised to 1150 ℃, the temperature is kept for 320min, then a 2000t quick forging machine is adopted for upsetting, drawing, cogging and forging, and after air cooling, a square bar-shaped primary forging stock with the section size of 460mm multiplied by 460mm (width multiplied by height) is obtained; the T isβThe beta-phase transformation temperature of TA15 titanium alloy is 980 ℃, and the ratio of height to diameter adopted by upsetting, cogging and forging is (2.3-2.5): 1; the single-pass deformation of the upsetting, cogging and forging is 27-30%, and the single-fire accumulated deformation is 84%;
step three, upsetting-drawing forging of a beta phase region: putting the square-rod-shaped primary forging stock obtained in the step two into an electric furnace, controlling the charging temperature of the square-rod-shaped primary forging stock to be 810 ℃, preserving heat for 150min at the charging temperature, then heating to 1050 ℃ and preserving heat for 270min, then adopting a 2000t quick forging machine to carry out beta-phase region upsetting forging, and obtaining a square-rod-shaped secondary forging stock with the cross section size of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2.2-2.5): 1; the single-pass deformation of the beta phase region upsetting-drawing forging is 30-37%, and the single-fire accumulated deformation is 87%; the drawing forging process of the beta phase region upsetting forging adopts a deformation mode of diagonal chamfering, and the deformation amount is 35-37%;
step four, upsetting, drawing and forging the alpha + beta two-phase region: loading the square-rod-shaped secondary forging stock obtained in the third step into an electric furnace, controlling the charging temperature of the square-rod-shaped secondary forging stock to be 550 ℃, then heating to 950 ℃ at the speed of 4 ℃/min and preserving heat for 260min, then carrying out primary upsetting forging in an alpha + beta two-phase region by using a 2000t quick forging machine, obtaining a square-rod-shaped tertiary forging stock with the cross section size of 460mm multiplied by 460mm (width multiplied by height) after water cooling, loading the square-rod-shaped tertiary forging stock into the electric furnace, controlling the charging temperature of the square-rod-shaped tertiary forging stock to be 480 ℃, then heating to 940 ℃ at the speed of 5 ℃/min and preserving heat for 270min, then carrying out secondary upsetting forging in the alpha + beta two-phase region by using a 2000t quick forging machine, and obtaining a square-rod-shaped forging stock with the cross section size of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the first upsetting-drawing forging of the alpha + beta two-phase region is (2-2.2): 1, the single-pass deformation is 28-35%, and the single-fire cumulative deformation is 88%; the height-diameter ratio adopted by the second upsetting-drawing forging of the alpha + beta two-phase region is (2.3-2.5): 1, the single-pass deformation is 32-35%, and the single-fire cumulative deformation is 87%;
step five, finish forging and forging: putting the square-rod-shaped four-stage forging blank obtained in the fourth step into an electric furnace, controlling the charging temperature of the square-rod-shaped four-stage forging blank to be 600 ℃, then heating to 940 ℃ at the speed of 3 ℃/min, preserving heat for 270min, then carrying out upsetting and drawing finish forging, and carrying out air cooling to obtain a forging piece with the thickness of 200 mm; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2-2.1): 1, the single-pass deformation is 30-34%, and the single-fire cumulative deformation is 85%;
step six, rolling in one fire: heating and preserving the forge piece obtained in the fifth step at 930 ℃ for 250min, wherein the preserving time is calculated from the time when the forge piece enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 7-pass one-fire rolling by adopting a hot rolling mill to obtain a 50 mm-thick one-fire rolling plate blank; the single-pass deformation of the first four passes of the one-fire rolling is 20-24%, and the single-pass deformation of the last three passes is 8-15%;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat for 100min at 920 ℃, calculating the preserving heat time from the time when the first-heat rolling plate blank enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 5-pass second-heat rolling by adopting a hot rolling mill to obtain a second-heat rolling plate blank with the thickness of 10 mm; the first three secondary deformation of the two-fire rolling is 20-24%, and the second secondary deformation is 14-18%; the second-fire rolling adopts reversing rolling, so that the direction of the second-fire rolling is vertical to the direction of the first-fire rolling in the sixth step;
step eight, slab processing: and annealing the two-fire rolling plate blank obtained in the step seven at the temperature of 850 ℃ for 1h, and then sequentially grinding and shearing to obtain the TA15 titanium alloy medium plate with the average grain size of 17 mu m and the thickness of 10 mm.
Fig. 1 is a microstructure diagram of the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example, and as can be seen from fig. 1, the average grain size of the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example is 17 μm, and the structure is uniform.
The strain rate of the TA15 titanium alloy fine-grain medium-thickness plate prepared by the embodiment is 1 multiplied by 10-4The result of a 880 ℃ high-temperature tensile test performed under the condition of/s shows that the longitudinal elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 440%, and the transverse elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 392%, which indicates that the TA15 titanium alloy fine-grain medium-thickness plate prepared in the embodiment has excellent superplastic performance.
Example 2
The embodiment comprises the following steps:
step one, smelting: according to the design components of a target alloy, carrying out automatic mixing, electrode pressing and assembly welding on 0-grade sponge titanium and a middle alloy in sequence, then carrying out three times of vacuum consumable arc melting to obtain a TA15 titanium alloy cast ingot with the diameter of 630mm multiplied by 2200mm (diameter multiplied by length), wherein the vacuum degree in a vacuum consumable arc melting furnace in the first time of vacuum consumable arc melting is 0.08Pa, the vacuum degree in the vacuum consumable arc melting furnace in the second time of vacuum consumable arc melting is 0.06Pa, the vacuum degree in the vacuum consumable arc melting furnace in the third time of vacuum consumable arc melting is 0.02Pa, then carrying out split cleaning after peeling and grinding on the TA15 titanium alloy cast ingot, and then carrying out smooth transition grinding, wherein the depth-to-width ratio of the smooth transition grinding is 1:15, and the depth is 6 mm;
step two, cogging and forging: loading the cleaned TA15 titanium alloy ingot in the first step into an electric furnace, controlling the charging temperature of the TA15 titanium alloy ingot to be 810 ℃, preserving heat for 210min at the charging temperature, then heating to 1150 ℃ and preserving heat for 350min, then carrying out upsetting-drawing cogging forging by using a 3150t quick forging machine, and obtaining a square-bar-shaped primary forging blank with the section size of 480mm multiplied by 480mm (width multiplied by height) after air cooling; the T isβThe beta-phase transformation temperature of TA15 titanium alloy is 980 ℃, and the ratio of height to diameter adopted by upsetting, cogging and forging is (2-2.3): 1; the single-pass deformation of upsetting, cogging and forging is 25-28%, and the single-fire accumulated deformation is 80%;
step three, upsetting-drawing forging of a beta phase region: putting the square-rod-shaped primary forging stock obtained in the step two into an electric furnace, controlling the charging temperature of the square-rod-shaped primary forging stock to be 800 ℃, preserving heat for 170min at the charging temperature, then heating to 1050 ℃ and preserving heat for 280min, then adopting a 3150t quick forging machine to carry out beta-phase region upsetting forging, and obtaining a square-rod-shaped secondary forging stock with the section size of 480mm multiplied by 480mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2.3-2.5): 1; the single-pass deformation of the beta-phase region upsetting-drawing forging is 25-34%, and the single-fire accumulated deformation is 85%; the drawing forging process of the beta phase region upsetting forging adopts a deformation mode of diagonal chamfering, and the deformation amount is 37-40%;
step four, upsetting, drawing and forging the alpha + beta two-phase region: loading the square-rod-shaped secondary forging stock obtained in the third step into an electric furnace, controlling the charging temperature of the square-rod-shaped secondary forging stock to be 500 ℃, then heating to 965 ℃ at the speed of 3 ℃/min and preserving heat for 280min, then carrying out primary upsetting forging in an alpha + beta two-phase region by adopting a 3150t quick forging machine, obtaining a square-rod-shaped tertiary forging stock with the cross section dimension of 480mm multiplied by 480mm (width multiplied by height) after water cooling, loading the square-rod-shaped tertiary forging stock into the electric furnace, controlling the charging temperature of the square-rod-shaped tertiary forging stock to be 600 ℃, then heating to 950 ℃ at the speed of 4 ℃/min and preserving heat for 280min, then carrying out secondary upsetting forging in the alpha + beta two-phase region by adopting a 3150t quick forging machine, and obtaining a square-rod-shaped quaternary forging stock with the cross section dimension of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the first upsetting-drawing forging of the alpha + beta two-phase region is (2-2.4): 1, the single-pass deformation is 25-32%, and the single-fire cumulative deformation is 85%; the height-diameter ratio adopted by the second upsetting-drawing forging of the alpha + beta two-phase region is (2.1-2.4): 1, the single-pass deformation is 30-35%, and the single-fire cumulative deformation is 85%;
step five, finish forging and forging: putting the square-rod-shaped four-stage forging blank obtained in the fourth step into an electric furnace, controlling the charging temperature of the square-rod-shaped four-stage forging blank to be 450 ℃, then heating to 950 ℃ at the speed of 4 ℃/min and preserving heat for 280min, then carrying out upsetting and drawing finish forging, and carrying out air cooling to obtain a forging piece with the thickness of 220 mm; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2.3-2.5): 1, the single-pass deformation is 35-40%, and the single-fire cumulative deformation is 87%;
step six, rolling in one fire: heating and preserving the forge piece obtained in the fifth step at 940 ℃ for 280min, wherein the preserving time is calculated from the time when the forge piece enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out one-fire rolling for 8 times by using a hot rolling mill to obtain a one-fire rolling plate blank with the thickness of 80 mm; the single-pass deformation of the first four passes of the one-fire rolling is 22-25%, and the single-pass deformation of the last three passes of the one-fire rolling is 12-18%;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat for 155min at 940 ℃, calculating the preserving heat time from the time when the first-heat rolling plate blank enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 6-pass second-heat rolling by adopting a hot rolling mill to obtain a second-heat rolling plate blank with the thickness of 25 mm; the first three secondary deformation of the two-fire rolling is 20-25%, and the second secondary deformation is 15-18%; and the second-fire rolling adopts reversing rolling, so that the direction of the second-fire rolling is perpendicular to the direction of the first-fire rolling in the sixth step.
Step eight, slab processing: and annealing the two-fire rolling plate blank obtained in the step seven at 900 ℃ for 1.5h, and then sequentially grinding and shearing to obtain the TA15 titanium alloy medium plate with the average grain size of 20 mu m and the thickness of 25 mm.
Fig. 2 is a microstructure diagram of the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example, and as can be seen from fig. 2, the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example has an average grain size of 20 μm and a uniform structure.
The strain rate of the TA15 titanium alloy fine-grain medium-thickness plate prepared by the embodiment is 1 multiplied by 10-4The 850 ℃ high-temperature tensile test is carried out under the condition of/s, and the result shows that the longitudinal elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 421%, and the transverse elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 348%, which indicates that the TA15 titanium alloy fine-grain medium-thickness plate prepared in the embodiment has excellent superplastic property.
Example 3
The embodiment comprises the following steps:
step one, smelting: according to the design components of a target alloy, carrying out automatic material mixing, electrode pressing and assembly welding on 0-grade sponge titanium and a middle alloy in sequence, then carrying out three times of vacuum consumable arc melting to obtain a TA15 titanium alloy cast ingot with the diameter of 560mm multiplied by 2000mm (diameter multiplied by length), wherein the vacuum degree in a vacuum consumable arc melting furnace in the first time of vacuum consumable arc melting is 0.09Pa, the vacuum degree in the vacuum consumable arc melting furnace in the second time of vacuum consumable arc melting is 0.07Pa, the vacuum degree in the vacuum consumable arc melting furnace in the third time of vacuum consumable arc melting is 0.03Pa, then carrying out split cleaning after peeling and grinding on the TA15 titanium alloy cast ingot, and then carrying out smooth transition grinding with the depth-to-width ratio of 1:13 and the depth of 9 mm;
step two, cogging and forging: loading the cleaned TA15 titanium alloy ingot in the first step into an electric furnace, controlling the charging temperature of the TA15 titanium alloy ingot to be 790 ℃, preserving the heat for 196min at the charging temperature, then heating to 1160 ℃, preserving the heat for 310min, then carrying out upsetting-drawing cogging forging by adopting a 3150t quick forging machine, and carrying out air cooling to obtain a square-bar-shaped primary forging blank with the section size of 460mm × 460mm (width × height); the T isβThe beta-phase transformation temperature of TA15 titanium alloy is 980 ℃, and the ratio of height to diameter adopted by upsetting, cogging and forging is (2.2-2.4): 1; the single-pass deformation of the upsetting, cogging and forging is 27-30%, and the single-fire accumulated deformation is 82%;
step three, upsetting-drawing forging of a beta phase region: putting the square-rod-shaped primary forging stock obtained in the step two into an electric furnace, controlling the charging temperature of the square-rod-shaped primary forging stock to be 790 ℃, preserving the heat for 143min at the charging temperature, then heating to 1060 ℃ and preserving the heat for 260min, then adopting a 2000t quick forging machine to carry out beta-phase region upsetting forging, and obtaining a square-rod-shaped secondary forging stock with the section size of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2-2.3): 1; the single-pass deformation of the beta-phase region upsetting-drawing forging is 32-40%, and the single-fire accumulated deformation is 87%; the drawing forging process of the beta phase region upsetting forging adopts a deformation mode of diagonal chamfering, and the deformation amount is 36-39%;
step four, upsetting, drawing and forging the alpha + beta two-phase region: loading the square-rod-shaped secondary forging stock obtained in the third step into an electric furnace, controlling the charging temperature of the square-rod-shaped secondary forging stock to be 600 ℃, then heating to 950 ℃ at the speed of 5 ℃/min and preserving heat for 270min, then carrying out primary upsetting forging in an alpha + beta two-phase region by using a 2000t quick forging machine, obtaining a square-rod-shaped tertiary forging stock with the cross section size of 460mm multiplied by 460mm (width multiplied by height) after water cooling, loading the square-rod-shaped tertiary forging stock into the electric furnace, controlling the charging temperature of the square-rod-shaped tertiary forging stock to be 450 ℃, then heating to 950 ℃ at the speed of 3 ℃/min and preserving heat for 260min, then carrying out secondary upsetting forging in the alpha + beta two-phase region by using a 2000t quick forging machine, and obtaining a square-rod-shaped forging stock with the cross section size of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the first upsetting-drawing forging of the alpha + beta two-phase region is (2.2-2.5): 1, the single-pass deformation is 32-40%, and the single-fire cumulative deformation is 86%; the height-diameter ratio adopted by the second upsetting-drawing forging of the alpha + beta two-phase region is (2.2-2.4): 1, the single-pass deformation is 35-40%, and the single-fire cumulative deformation is 88%;
step five, finish forging and forging: putting the square-rod-shaped four-stage forging blank obtained in the fourth step into an electric furnace, controlling the charging temperature of the square-rod-shaped four-stage forging blank to be 500 ℃, then heating to 950 ℃ at the speed of 5 ℃/min, preserving heat for 260min, then carrying out upsetting and final forging, and obtaining a forging with the thickness of 210mm after air cooling; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2.2-2.4): 1, the single-pass deformation is 33-36%, and the single-fire cumulative deformation is 85%;
step six, rolling in one fire: heating and preserving the forge piece obtained in the fifth step at 940 ℃ for 258min, calculating the preserving time from the time when the forge piece enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 6-pass one-fire rolling by adopting a hot rolling mill to obtain a 60 mm-thick one-fire rolling plate blank; the single-pass deformation of the first four passes of the one-fire rolling is 20-25%, and the single-pass deformation of the last three passes of the one-fire rolling is 10-16%;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat for 125min at 930 ℃, calculating the preserving heat time from the time when the first-heat rolling plate blank enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 4-pass second-heat rolling by adopting a hot rolling mill to obtain a 18 mm-thick second-heat rolling plate blank; the first three secondary deformation of the two-fire rolling is 22-26%, and the second secondary deformation is 12-18%; the second-fire rolling adopts reversing rolling, so that the direction of the second-fire rolling is vertical to the direction of the first-fire rolling in the sixth step;
step eight, slab processing: and annealing the two-fire rolling plate blank obtained in the step seven at the temperature of 850 ℃ for 1h, and then sequentially grinding and shearing to obtain the TA15 titanium alloy medium plate with the average grain size of 17 mu m and the thickness of 18 mm.
Fig. 3 is a microstructure diagram of the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example, and as can be seen from fig. 3, the TA15 titanium alloy fine-grained medium-thickness plate prepared in this example has an average grain size of 17 μm and a uniform structure.
The strain rate of the TA15 titanium alloy fine-grain medium-thickness plate prepared by the embodiment is 1 multiplied by 10-4The result of a 930 ℃ high-temperature tensile test under the condition of/s shows that the longitudinal elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 421%, and the transverse elongation of the TA15 titanium alloy fine-grain medium-thickness plate is 379%, which indicates that the TA15 titanium alloy fine-grain medium-thickness plate prepared in the embodiment has excellent superplastic performance.
Example 4
The embodiment comprises the following steps:
step one, smelting: according to the design components of a target alloy, carrying out automatic material mixing, electrode pressing and assembly welding on 0-grade sponge titanium and a middle alloy in sequence, then carrying out three times of vacuum consumable arc melting to obtain a TA15 titanium alloy cast ingot with the diameter of 560mm multiplied by 2000mm (diameter multiplied by length), wherein the vacuum degree in a vacuum consumable arc melting furnace in the first time of vacuum consumable arc melting is 0.07Pa, the vacuum degree in the vacuum consumable arc melting furnace in the second time of vacuum consumable arc melting is 0.05Pa, the vacuum degree in the vacuum consumable arc melting furnace in the third time of vacuum consumable arc melting is 0.01Pa, then carrying out split cleaning after peeling and grinding on the TA15 titanium alloy cast ingot, and then carrying out smooth transition grinding, wherein the depth-to-width ratio of the smooth transition grinding is 1:14, and the depth is 10 mm;
step two, cogging and forging: putting the TA15 titanium alloy ingot cleaned in the step one into an electric furnace, and controlling the ingot castingThe charging temperature of the ingot is 800 ℃, the ingot is kept at the charging temperature for 176min, then the ingot is heated to 1040 ℃ and kept at 320min, then a 2000t quick forging machine is adopted for upsetting, drawing, cogging and forging, and after air cooling, a square bar-shaped primary forging stock with the section size of 460mm multiplied by 460mm (width multiplied by height) is obtained; the T isβThe beta-phase transformation temperature of TA15 titanium alloy is 980 ℃, and the ratio of height to diameter adopted by upsetting, cogging and forging is (2.3-2.5): 1; the single-pass deformation of the upsetting, cogging and forging is 27-30%, and the single-fire accumulated deformation is 84%;
step three, upsetting-drawing forging of a beta phase region: putting the square-rod-shaped primary forging stock obtained in the step two into an electric furnace, controlling the charging temperature of the square-rod-shaped primary forging stock to be 810 ℃, preserving heat for 150min at the charging temperature, then heating to 1140 ℃, preserving heat for 265min, then adopting a 2000t quick forging machine to carry out beta-phase region upsetting forging, and obtaining a square-rod-shaped secondary forging stock with the section size of 460mm multiplied by 460mm (width multiplied by height) after air cooling; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2.2-2.5): 1; the single-pass deformation of the beta phase region upsetting-drawing forging is 30-37%, and the single-fire accumulated deformation is 87%; the drawing forging process of the beta phase region upsetting forging adopts a deformation mode of diagonal chamfering, and the deformation amount is 35-37%;
step four, upsetting, drawing and forging the alpha + beta two-phase region: loading the square-rod-shaped secondary forging blank obtained in the third step into an electric furnace, controlling the charging temperature of the square-rod-shaped secondary forging blank to be 550 ℃, then heating to 952 ℃ at the speed of 4 ℃/min and preserving heat for 265min, then carrying out primary upsetting forging in an alpha + beta two-phase region by using a 2000t quick forging machine, cooling by water to obtain a square-rod-shaped tertiary forging blank with the cross section size of 460mm multiplied by 460mm (width multiplied by height), loading the square-rod-shaped tertiary forging blank into the electric furnace, controlling the charging temperature of the square-rod-shaped tertiary forging blank to be 480 ℃, then heating to 945 ℃ at the speed of 5 ℃/min and preserving heat for 265min, then carrying out secondary upsetting forging in the alpha + beta two-phase region by using a 2000t quick forging machine, and cooling by air to obtain a square-rod-shaped forging blank with the cross section size of 460mm multiplied by 460mm (width multiplied by height); the height-diameter ratio adopted by the first upsetting-drawing forging of the alpha + beta two-phase region is (2-2.2): 1, the single-pass deformation is 28-35%, and the single-fire cumulative deformation is 88%; the height-diameter ratio adopted by the second upsetting-drawing forging of the alpha + beta two-phase region is (2.3-2.5): 1, the single-pass deformation is 35-40%, and the single-fire cumulative deformation is 87%;
step five, finish forging and forging: loading the square-rod-shaped four-stage forging blank obtained in the fourth step into an electric furnace, controlling the charging temperature of the square-rod-shaped four-stage forging blank to be 600 ℃, then heating to 945 ℃ at the speed of 3 ℃/min, preserving the temperature for 265min, then carrying out upsetting and final forging, and air cooling to obtain a forging piece with the thickness of 200 mm; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2-2.1): 1, the single-pass deformation is 30-34%, and the single-fire cumulative deformation is 85%;
step six, rolling in one fire: heating and preserving the forge piece obtained in the fifth step at 935 ℃ for 250min, calculating the preserving time from the time when the forge piece enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 7-pass one-fire rolling by adopting a hot rolling mill to obtain a 50 mm-thick one-fire rolling plate blank; the single-pass deformation of the first four passes of the one-fire rolling is 20-24%, and the single-pass deformation of the last three passes is 8-15%;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat for 100min at 925 ℃, calculating the preserving heat time from the time when the first-heat rolling plate blank enters a heating furnace and the furnace temperature of the heating furnace is stable, and then carrying out 5-pass second-heat rolling by adopting a hot rolling mill to obtain a second-heat rolling plate blank with the thickness of 10 mm; the first three secondary deformation of the two-fire rolling is 20-24%, and the second secondary deformation is 18-20%; the second-fire rolling adopts reversing rolling, so that the direction of the second-fire rolling is vertical to the direction of the first-fire rolling in the sixth step;
step eight, slab processing: and annealing the two-fire rolling plate blank obtained in the step seven at 860 ℃ for 1.2h, and then sequentially grinding and shearing to obtain the TA15 titanium alloy medium plate with the average grain size of 17 mu m and the thickness of 10 mm.
The strain rate of the TA15 titanium alloy fine-grain medium-thickness plate prepared by the embodiment is 1 multiplied by 10-4The result of a 880 ℃ high-temperature tensile test carried out under the condition of/s shows that the TA15 titanium alloy fine-grain medium plateThe longitudinal elongation of the material is 435%, and the transverse elongation of the material is 385%, which shows that the TA15 titanium alloy fine-grain medium-thickness plate prepared by the embodiment has excellent superplastic property.
The above description is only for the preferred embodiment of the present invention, and is not intended to limit the present invention in any way. Any simple modification, change and equivalent changes of the above embodiments according to the technical essence of the invention are still within the protection scope of the technical solution of the invention.
Claims (10)
1. A processing method of a fine-grain superplasticity TA15 titanium alloy medium-thick plate is characterized by comprising the following steps:
step one, smelting: according to the design components of the target alloy, mixing, electrode pressing and assembly welding are sequentially carried out on 0-grade titanium sponge and the intermediate alloy, then TA15 titanium alloy cast ingot is obtained through three times of vacuum consumable arc melting, and local defects on the surface of the TA15 titanium alloy cast ingot are cleaned;
step two, cogging and forging: putting the TA15 titanium alloy ingot cleaned in the step one into an electric furnace and putting the ingot into the electric furnace for Tβ+160℃~TβHeating and preserving heat at the temperature of +180 ℃, then adopting a rapid forging machine of more than 2000t to perform upsetting, drawing, cogging and forging, and performing air cooling to obtain a primary forging stock; the T isβThe beta-phase transformation temperature of the TA15 titanium alloy is given as the unit, and the ratio of height to diameter adopted by the upsetting-cogging forging is (2-2.5): 1;
step three, upsetting-drawing forging of a beta phase region: putting the primary forging stock obtained in the step two into an electric furnace and putting the primary forging stock into the electric furnace for Tβ+60℃~TβHeating and preserving heat at the temperature of 80 ℃, then adopting a rapid forging machine or a press machine with the temperature of more than 2000t to perform beta-phase region upsetting forging, and performing air cooling to obtain a secondary forging stock; the height-diameter ratio adopted by the beta phase region upsetting-drawing forging is (2-2.5): 1;
step four, upsetting, drawing and forging the alpha + beta two-phase region: putting the secondary forging stock obtained in the third step into an electric furnace and putting the secondary forging stock into the electric furnace for Tβ-25℃~TβHeating and insulating at-30 deg.C, performing first upsetting-drawing forging in alpha + beta two-phase region by using rapid forging machine or press of 2000t or more, and cooling to obtain three-stage forging stockContinuing to put the three-stage forging stock at Tβ-25℃~TβHeating and preserving heat at the temperature of minus 30 ℃, then adopting a rapid forging machine or a press machine with the temperature of more than 2000t to perform secondary upsetting-drawing forging in an alpha + beta two-phase region, and obtaining a four-stage forging stock after air cooling; the height-diameter ratios adopted by the first upsetting forging of the alpha + beta two-phase region and the second upsetting forging of the alpha + beta two-phase region are (2-2.5): 1;
step five, finish forging and forging: putting the four-stage forging stock obtained in the fourth step into an electric furnace and putting the four-stage forging stock into the electric furnace for Tβ-30℃~TβHeating and preserving heat at the temperature of minus 40 ℃, then carrying out upsetting finish forging, and carrying out air cooling to obtain a forged piece; the height-diameter ratio adopted by the upsetting-drawing finish forging is (2-2.5): 1, the thickness of the forging is 200 mm-220 mm;
step six, rolling in one fire: heating and insulating the forge piece obtained in the fifth step, and then carrying out first-pass rolling for 6-8 passes by using a hot rolling mill to obtain a first-pass rolling plate blank; the thickness of the one-fire rolling plate blank is 50 mm-80 mm;
step seven, rolling with two hot rolls: shearing and blanking the first-heat rolling plate blank obtained in the sixth step, heating and preserving heat, and then carrying out 4-6-pass second-heat rolling by using a hot rolling mill to obtain a second-heat rolling plate blank; the thickness of the second-fire rolling plate blank is 10 mm-25 mm;
step eight, slab processing: annealing the two-fire rolled plate blank obtained in the step seven, and then sequentially polishing and shearing to obtain a TA15 titanium alloy medium plate; the thickness of the TA15 titanium alloy medium plate is 10 mm-25 mm, the average grain size is not more than 20 mu m, the transverse elongation of the TA15 titanium alloy medium plate is more than 420% at the temperature of 850-930 ℃, and the longitudinal elongation of the TA15 titanium alloy medium plate is more than 340%.
2. The method of claim 1, wherein in the first and second vacuum consumable arc melting processes of the third vacuum consumable arc melting in the first step, the degree of vacuum in the vacuum consumable arc melting furnace is less than 1.0 x 10-1Pa, vacuum consumable arc melting in the third vacuum consumable arc melting processThe hollowness is less than 5.0 multiplied by 10-2Pa; in the first step, smooth transition grinding is carried out on the cleaned TA15 titanium alloy ingot, and the depth-to-width ratio of the smooth transition grinding is not more than 1:10, and the depth is not more than 10 mm.
3. The processing method of the fine grain superplasticity TA15 titanium alloy medium and thick plate material as claimed in claim 1, wherein said heating and heat-preserving in step two is step heating, and said step heating process is: controlling the charging temperature of TA15 titanium alloy ingot to be 790-810 ℃, and keeping the temperature t at the charging temperature1min, then heating to Tβ+160℃~Tβ+180 ℃ and incubation t2min, wherein, t1= (numerical value of TA15 titanium alloy ingot diameter/3-10) min- (numerical value of TA15 titanium alloy ingot diameter/3 +10) min, t2= (TA15 titanium alloy ingot diameter/2 +30) min- (TA15 titanium alloy ingot diameter/2 +40) min, the TA15 titanium alloy ingot diameter unit is mm; the single-pass deformation of upsetting, cogging and forging is 25-30%, and the single-fire accumulated deformation is not less than 80%.
4. The processing method of the fine grain superplasticity TA15 titanium alloy medium and thick plate material as claimed in claim 1, wherein said heating and heat preservation in step three is step heating, and the step heating process is: firstly, controlling the charging temperature of a primary forging stock to be 790-810 ℃ and preserving heat t at the charging temperature3min, then heating to Tβ+60℃~Tβ+80 ℃ and incubation t4min, wherein, t3= (numerical value of maximum cross-section of primary forging stock/3-10) min — (numerical value of maximum cross-section of primary forging stock/3 +10) min, t4= (= value of maximum size of section of primary forging stock/2 +30) min- (+ value of maximum size of section of primary forging stock/2 +40) min, unit of maximum size of section of primary forging stock is mm; the single-pass deformation of the beta-phase region upsetting-drawing forging is 25-40%, and the single-fire accumulated deformation is not less than 85%; the drawing forging process of the beta phase region upsetting forging adopts a diagonal chamfering deformation mode, and the deformation amount is 35-40%.
5. The processing method of the fine grain superplastic TA15 titanium alloy medium and thick plate material as claimed in claim 1, wherein the heating and heat preservation process of the first upsetting forging of the α + β two-phase region in the fourth step is as follows: controlling the charging temperature of the secondary forging stock to be 500-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-25℃~Tβ-30 ℃ and incubation t5min; said t is5= (numerical value of the maximum dimension of the section of the secondary forging stock/2 +30) min- (/ numerical value of the maximum dimension of the section of the secondary forging stock/2 +40) min, the unit of the maximum dimension of the section of the secondary forging stock is mm; the single-pass deformation of the alpha + beta two-phase region during the first upsetting-drawing forging is 25% -40%, and the single-fire accumulated deformation is not less than 85%; and the cooling mode after the first upsetting-drawing forging of the alpha + beta two-phase region is water cooling.
6. The processing method of the fine-grained superplasticity TA15 titanium alloy medium and thick plate according to claim 1, wherein the heating and heat preservation process of the second upsetting forging of the α + β two-phase region in the fourth step is as follows: controlling the charging temperature of the three-stage forging stock to be 450-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-30℃~Tβ-40 ℃ and incubation t6min; said t is6= (numerical value of the maximum cross section of the third-stage forging stock/2 +30) min-2 +40 (numerical value of the maximum cross section of the third-stage forging stock) in mm; the single-pass deformation of the second upsetting-drawing forging of the alpha + beta two-phase region is 30-40%, and the single-fire accumulated deformation is not less than 85%.
7. The processing method of the fine-grained superplasticity TA15 titanium alloy medium and thick plate according to claim 1, wherein the specific process of heating and heat preservation in the fifth step is as follows: controlling the charging temperature of the four-stage forging stock to be 450-600 ℃, and then heating to T at the speed of 3-5 ℃/minβ-30℃~Tβ-40 ℃ and incubation t0min; said t is0= (numerical value of maximum cross-section size of the four-stage forging stock/2 +30) min- (maximum cross-section size of the four-stage forging stock)The numerical value of the size/2 +40) min, and the unit of the maximum size of the section of the four-stage forging stock is mm; the single-pass deformation of the upsetting-drawing finish forging is 30-40%, and the single-fire accumulated deformation is not less than 85%.
8. The method for processing the fine grain superplastic TA15 titanium alloy medium and thick plate material as claimed in claim 1, wherein the heating temperature for said one-fire rolling in the sixth step is Tβ-40℃~Tβ-50 ℃ and holding time t7= (numerical value of the thickness of the forging piece/0.8-5) min- (/ numerical value of the thickness of the forging piece/0.8 +5) min, the heat preservation time is calculated from the time when the four-level forging piece enters the heating furnace and the furnace temperature of the heating furnace is stable; in the one-pass rolling process, the single-pass deformation of the 1 st to 3 rd passes is 20-25%, and the other single-pass deformation is not less than 8%.
9. The method for processing the fine grain superplastic TA15 titanium alloy medium and thick plate as claimed in claim 1, wherein the heating temperature of said two-fire rolling in the seventh step is Tβ-50℃~Tβ-60 ℃ and holding time t8= (= value of primary rolled slab thickness/0.5-5) min. - (+ 0.5+5) min, the heat preservation time is calculated from the time when the primary rolled slab enters the heating furnace and the furnace temperature of the heating furnace is stable; the initial single-pass deformation of the two-fire rolling is 20% -26%, the other single-pass deformation is 12% -20%, and the two-fire rolling adopts reversing rolling, so that the direction of the two-fire rolling is perpendicular to the direction of the one-fire rolling in the step six.
10. The processing method of the fine-grain superplasticity TA15 titanium alloy medium and thick plate material as claimed in claim 1, wherein the annealing treatment in step eight is carried out at 850-900 ℃ for 1-1.5 h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010669587.0A CN111763850B (en) | 2020-07-13 | 2020-07-13 | Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010669587.0A CN111763850B (en) | 2020-07-13 | 2020-07-13 | Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111763850A CN111763850A (en) | 2020-10-13 |
| CN111763850B true CN111763850B (en) | 2021-05-07 |
Family
ID=72725134
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010669587.0A Active CN111763850B (en) | 2020-07-13 | 2020-07-13 | Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111763850B (en) |
Families Citing this family (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112048639A (en) * | 2020-08-27 | 2020-12-08 | 重庆金世利航空材料有限公司 | Preparation method of TA15 titanium alloy ingot |
| CN111922075A (en) * | 2020-10-15 | 2020-11-13 | 西安圣泰金属材料有限公司 | High-strength TA4 pure titanium plate and preparation method thereof |
| CN112391558B (en) * | 2020-11-25 | 2021-12-24 | 长安大学 | Near-beta type titanium alloy with good matching between strength and plasticity and preparation method thereof |
| CN112725713B (en) * | 2020-12-24 | 2021-12-28 | 长安大学 | High-strength and high-plasticity powder metallurgy titanium alloy and processing method thereof |
| CN112692204B (en) * | 2020-12-25 | 2022-09-23 | 西安稀有金属材料研究院有限公司 | Preparation method of large-size corrosion-resistant Ti35 alloy forging |
| CN112959004B (en) * | 2021-02-02 | 2022-09-13 | 湖南湘投金天科技集团有限责任公司 | High-strength titanium alloy end socket and preparation method thereof |
| CN113578959B (en) * | 2021-06-27 | 2022-06-03 | 中国科学院金属研究所 | Preparation method of fine-grain TA15 titanium alloy foil |
| CN113578967B (en) * | 2021-06-27 | 2022-05-31 | 中国科学院金属研究所 | Preparation method of 550-650 ℃ high-temperature titanium alloy foil |
| CN113564397B (en) * | 2021-07-27 | 2022-05-31 | 西北有色金属研究院 | Short-process preparation method of medium-strength high-toughness titanium alloy medium-thickness plate |
| CN114196846B (en) * | 2021-12-17 | 2022-07-15 | 哈尔滨工业大学 | Superplastic discontinuous reinforced titanium-based composite material and superplastic forming method thereof |
| CN114273583B (en) * | 2021-12-23 | 2022-12-09 | 北京钢研高纳科技股份有限公司 | Ti 2 AlNb-based alloy plate and preparation method and application thereof |
| CN114318031A (en) * | 2022-01-07 | 2022-04-12 | 陕西钛普稀有金属材料有限公司 | Preparation method of 4.5mm fine-grain plate |
| CN114472897B (en) * | 2022-01-28 | 2023-06-06 | 有研工程技术研究院有限公司 | Gradient titanium alloy with low adiabatic shear sensitivity and preparation method thereof |
| CN114406169A (en) * | 2022-03-23 | 2022-04-29 | 西安圣泰金属材料有限公司 | Processing method of two-phase titanium alloy large-size plate |
| CN115786747B (en) * | 2022-11-24 | 2024-01-26 | 西北有色金属研究院 | Preparation method of medical high-performance antibacterial titanium alloy plate |
| CN116770116B (en) * | 2023-08-17 | 2023-12-01 | 成都先进金属材料产业技术研究院股份有限公司 | Weak texture TA18 titanium alloy bar and preparation method thereof |
| CN116987992B (en) * | 2023-09-27 | 2024-02-02 | 成都先进金属材料产业技术研究院股份有限公司 | Heating method of large-thickness titanium alloy slab |
Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2988269B2 (en) * | 1994-08-08 | 1999-12-13 | 住友金属工業株式会社 | Method for producing rolled α + β titanium alloy sheet |
| CN101429637B (en) * | 2008-12-02 | 2010-09-08 | 北京航空航天大学 | Biphase titanium alloy thermal treatment method for acquiring two-state organization with raft-shape primary alpha phase |
| US9255316B2 (en) * | 2010-07-19 | 2016-02-09 | Ati Properties, Inc. | Processing of α+β titanium alloys |
| CN102978437A (en) * | 2012-11-23 | 2013-03-20 | 西部金属材料股份有限公司 | Alpha plus beta two-phase titanium alloy and method for processing same |
| US9777361B2 (en) * | 2013-03-15 | 2017-10-03 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
| JP2016128171A (en) * | 2013-04-01 | 2016-07-14 | 新日鐵住金株式会社 | Titanium hot rolling slab being hard to cause surface flaw and its manufacturing method |
| CN104625627B (en) * | 2014-12-23 | 2016-11-16 | 西安欧中材料科技有限公司 | A kind of preparation method of plasma rotating electrode titanium alloy electrode rod |
| US10502252B2 (en) * | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
| CN106425327B (en) * | 2016-11-30 | 2018-04-13 | 西北有色金属研究院 | A kind of preparation method of big specification TC4 titanium alloy rings |
| CN109930100A (en) * | 2019-03-29 | 2019-06-25 | 中国科学院金属研究所 | A kind of damage tolerance titanium alloy plate rolling and mating heat treatment process |
-
2020
- 2020-07-13 CN CN202010669587.0A patent/CN111763850B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN111763850A (en) | 2020-10-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111763850B (en) | Processing method of fine-grain superplasticity TA15 titanium alloy medium-thick plate | |
| CN102513479B (en) | Production process for large-diameter fine isometric crystal tissue titanium alloy bar | |
| CN111286686B (en) | Short-process preparation method of TC4 titanium alloy large-size bar with fine equiaxial structure | |
| CN105506525B (en) | Preparation method of Ti2AlNb-based alloy large-size uniform fine-grain bar | |
| CN104762576B (en) | The preparation method of TC18 titanium alloy the whole network basket tissue medium format overlength bar | |
| CN112676503B (en) | Forging processing method for TC32 titanium alloy large-size bar | |
| CN109454188A (en) | Ti55531 titanium alloy large size bar free forging method | |
| CN112981174B (en) | Preparation method of high-strength high-plasticity titanium alloy wire | |
| CN109234554B (en) | Preparation method of high-temperature titanium alloy bar | |
| CN104789912B (en) | A kind of preparation method of the tungsten material of cavity liner tantalum 5 | |
| CN111394637B (en) | Ti2AlNb alloy and preparation method of bar thereof | |
| CN101935776B (en) | Beta titanium alloy material and preparation method thereof | |
| CN110125317B (en) | Forming method of high-strength stainless steel hot-rolled ring piece | |
| CN112338119B (en) | Method for forging near-alpha type high-temperature titanium alloy large-size bar | |
| CN114367611A (en) | Magnesium alloy revolving body structural part and preparation process thereof | |
| CN112718864A (en) | Production method for improving deep drawing performance of titanium strip coil for nuclear power plate heat exchanger | |
| CN114657417B (en) | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof | |
| CN110205572B (en) | Preparation method of two-phase Ti-Al-Zr-Mo-V titanium alloy forged rod | |
| CN105441713A (en) | A titanium alloy seamless tube and a manufacturing method thereof | |
| CN110144533A (en) | A method of regulation coarse second phase of 2219 aluminium alloy rings | |
| CN114101556A (en) | Processing method for preparing TB8 titanium alloy sheet in short process | |
| CN115747689B (en) | High-plasticity forging method for Ti-1350 ultrahigh-strength titanium alloy large-size bar | |
| CN107282687A (en) | A kind of preparation method of Ti6Al4V titanium alloys fine grain bar | |
| CN116555607A (en) | Preparation method of TA15 titanium alloy large-size bar | |
| CN115178598A (en) | Hot processing method for improving high-temperature tensile strength of titanium alloy rolled bar |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |