CN112045128A - Free forging method of TB6 titanium alloy large-size bar - Google Patents
Free forging method of TB6 titanium alloy large-size bar Download PDFInfo
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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Abstract
The invention provides a free forging method of a TB6 titanium alloy large-size bar, which adopts a large-size TB6 titanium alloy ingot with the diameter of phi 520-720 mm as a raw material, and the forging method comprises the following process routes: upsetting and drawing after ingot casting high-temperature homogenization treatment → upsetting and drawing in an alpha + beta phase region for the first time → upsetting and drawing after beta recrystallization treatment for the first time → upsetting and drawing in an alpha + beta phase region for the 2 nd time → upsetting and drawing after beta recrystallization treatment for the 2 nd time → upsetting and drawing in an alpha + beta phase region for the 3 rd time. The invention can produce large alpha + beta two-phase region tissue bar material without abnormal growth and large crystal grain, without beta spot, with good tissue uniformity, less forging and forging times, excellent performance, diameter phi 120-phi 400mm, solves the technical difficulty in the industry, has sufficient mechanical property, and is suitable for industrial production.
Description
Technical Field
The invention relates to the technical field of titanium alloy bar forging, in particular to a free forging processing technology with short process and strong process controllability, which is used for large bars produced by TB6 titanium alloy large-scale cast ingots, solves the problems of abnormal growth of local crystal grains of TB6 alloy and beta spots of finished bars in the forging process, and can be used for preparing key structural members such as airplane fuselages, wings, landing gears and the like, wherein the main specification of the bars is phi 120-phi 400 mm.
Background
The TB6 titanium alloy has the nominal composition of Ti-10V-2Fe-3Al, and is a near-beta type titanium alloy with high strength, high toughness and high hardenability. The TB6 titanium alloy contains about 2% of Fe element, the distribution coefficient of the Fe element is small, so that beta spots (the beta spots refer to a region with primary alpha phase less than 5% after heat treatment at 25 ℃ below the beta transition temperature or at 775 ℃ and are more than or equal to 0.76mm in any direction, the fluctuation of the Fe element is less than 0.3%, so that the beta spots can not be generated) are easily formed in the smelting and processing processes, and the larger the used ingot casting specification is, the higher the probability of generating the beta spots of the finished bar is. At present, large-scale ingots (the diameter of the ingot is more than or equal to 520mm and the weight of the ingot is more than or equal to 1.5 tons) are adopted to produce large-scale bars (the diameter of the bar is more than or equal to 120 mm), the problem of beta spots always exists, so that the TB6 titanium alloy cannot be applied in large scale in China, which is a technical difficulty accepted in the industry; the TB6 titanium alloy is a near-beta alloy, the size of the crystal grain of the alloy is extremely sensitive to the forging process parameters such as recrystallization temperature, heating time, deformation speed and the like, the process forging range is extremely narrow, and the unreasonable process design is easy to cause abnormal growth of local crystal grains to cause uneven tissue, which is another difficulty in the forging process.
With the rapid development of the aviation industry in China, the consumption of the TB6 titanium alloy is increased rapidly, and on the premise of solving the technical problem, the production cost is considered to ensure the economy of large-scale production, so that the optimal matching of quality and cost is realized. Aiming at the background situation, the research on the free forging processing technology of the phi 120-phi 400mm bar is developed, the technical difficulty is solved, the free forging processing technology with short flow and strong process controllability is provided, the large-scale production of the TB6 titanium alloy large-specification bar is realized, and the requirement of the development of the aviation industry is met.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a free forging method of a TB6 titanium alloy large-size bar, so that a large-size alpha + beta two-phase region tissue bar which has no abnormal growth and large crystal grains, no beta spots, good tissue uniformity, less forging fire number (short process and low forging cost), excellent performance and a diameter of phi 120-phi 400mm is produced, the technical difficulty in the industry is solved, the mechanical property is abundant, and the method is suitable for industrial production.
In order to achieve the purpose, the raw material of the invention is large-size TB6 titanium alloy ingot (the weight of the ingot is more than or equal to 1.5 tons) with phi of 520-720 mm, and the process route of the forging method is as follows: upsetting and drawing after ingot casting high-temperature homogenization treatment → upsetting and drawing in an alpha + beta phase region for the first time → upsetting and drawing after beta recrystallization treatment for the first time → upsetting and drawing in an alpha + beta phase region for the 2 nd time → upsetting and drawing after beta recrystallization treatment for the 2 nd time → upsetting and drawing in an alpha + beta phase region for the 3 rd time.
The specific technical scheme of the invention is to provide a free forging method of a TB6 titanium alloy large-size bar, which is realized by the following steps:
(1) cogging, upsetting and pulling after ingot casting high-temperature homogenization treatment
The heating temperature of the high-temperature homogenization treatment is 1150-1300 ℃, the total heat preservation time is 2880-9000 min (the longer the time or the higher the temperature is, the better the component homogenization effect is), the heat frequency is controlled to be 1-2, the total forging ratio is controlled to be 5.00-10.00, the upsetting rate is controlled to be 5-30 mm/s, and hot material returning or air cooling is adopted after forging;
(2) first alpha + beta phase region upsetting
The heating temperature is 30-70 ℃ below the phase transition point, the heat preservation time is [ (0.50-0.85) multiplied by the minimum cross-sectional size of the blank ] min, the heat frequency is controlled to be 1 heat, the total forging ratio is controlled to be 1.90-4.00, the upsetting rate is controlled to be 5-20 mm/s, and after forging, the hot material is returned to the furnace for carrying out primary beta recrystallization treatment and then forging;
(3) upsetting and drawing after first beta recrystallization treatment
The heating temperature of the first beta recrystallization treatment is 60-120 ℃ above the phase transition point, the heat preservation time is [ (0.30-0.60) multiplied by the minimum cross-sectional dimension of the blank +60 ] min, the heat frequency is controlled to be 1 fire, the total forging ratio is controlled to be 1.20-1.50, the upsetting rate is controlled to be 5-30 mm/s, and air cooling is adopted after forging;
(4) 2 nd upsetting of alpha + beta phase zone
The heating temperature is 30-70 ℃ below the phase transition point, the heat preservation time is [ (0.50-0.85) multiplied by the minimum cross-sectional size of the blank ] min, the heat frequency is controlled to be 1 heat, the total forging ratio is controlled to be 1.90-4.00, the upsetting rate is controlled to be 5-20 mm/s, and after forging, the hot material is returned to the furnace to carry out 2 nd beta recrystallization treatment and then forging is carried out;
(5) upsetting and drawing after the 2 nd beta recrystallization treatment
The heating temperature of the 2 nd beta recrystallization treatment is 60-100 ℃ above the transformation point, the heat preservation time is [ (0.30-0.60) multiplied by the minimum cross-sectional dimension of the blank +60 ] min, the heat frequency is controlled to be 1 fire, the total forging ratio is controlled to be 1.20-1.50, the upsetting rate is controlled to be 5-30 mm/s, and air cooling is adopted after forging;
(6) 3 rd time of alpha + beta phase region upsetting-drawing forming
The heating temperature is 35-70 ℃ below the phase transition point, the heat preservation time is (0.50-0.85) multiplied by the minimum cross-sectional size of the blank min, the heat times are controlled to be 3-6 heats, the upsetting rate is controlled to be 5-20 mm/s, the total forging ratio is controlled to be 7.00-12.00, and hot material is returned to the furnace or cooled in air after forging.
Compared with the prior forging technology, the invention has the following innovations and beneficial effects:
1. the method adopts long-time high-temperature homogenization treatment for cogging, and the requirement of the heat preservation time of the method is firstly created to be more than or equal to 2880min, so that Fe element is fully diffused and homogenized, the upsetting rate of an alpha + beta phase region is controlled to be 5-20 mm/s, the local overheating in the forging process is prevented, and the problem that the bar does not have beta spots is effectively solved;
2. the invention adopts two beta recrystallization heat treatments, fully ensures the uniformity of crystal grains, controls the forging ratio of upsetting and drawing and the upsetting speed after the heat treatment, effectively refines the crystal grains and does not generate local abnormal growth crystal grains;
3. compared with the conventional forging process, the method disclosed by the invention has the advantages that the technical difficulty is solved, and the total forging heat number is less (the total heat number is controlled to be between 8 and 12 fires, and the cold charge heat number is controlled to be between 5 and 7 fires after the hot charge is returned to the furnace), so that the forging process is shorter, the production cost is effectively reduced, and the large-scale industrial production delivery can be realized.
Drawings
FIG. 1 is a macroscopic structure of a 200mm diameter bar prepared according to a first embodiment of the present invention;
FIG. 2 is a microstructure of a 200mm diameter bar prepared according to a first embodiment of the present invention;
FIG. 3 is a macrostructure of a bar of a 200mm gauge prepared in comparative example I, which is to be compared with example I of the present invention;
FIG. 4 is a macroscopic structure of a bar with a diameter of 350mm prepared in the second embodiment of the present invention;
FIG. 5 is a microstructure of a 350mm diameter bar prepared according to example two of the present invention;
FIG. 6 is a microstructure of a 350mm diameter bar prepared in comparative example II in comparison with example II of the present invention.
Detailed Description
The invention will now be further described with reference to the accompanying drawings and 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 equivalent or similar arrangement without departing from the spirit of the invention is intended to fall within the scope of the invention. And hereinafter: "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
The free forging method of the TB6 titanium alloy large-size bar in the embodiment is realized by the following steps:
(1) cogging, upsetting and pulling after ingot casting high-temperature homogenization treatment
Selecting a cast ingot with the specification of phi 680mm, wherein the phase transformation point (Tbeta) is 800 ℃. The 1 st fire high-temperature homogenization temperature is 1200 ℃, the heat preservation time is 3300min, the 2 nd upsetting is 2 mm, the forging ratio is 2.48, and air cooling is adopted after forging; the 2 nd fire high temperature homogenization temperature is 1200 ℃, the heat preservation time is 3300min, the 2 nd upsetting 2 is performed with the drawing and forging to 600mm, the forging ratio is 2.24, and air cooling is adopted after forging;
(2) first alpha + beta phase region upsetting
The heating temperature of the No. 3 fire is selected to be beta-45 ℃, the heat preservation time is selected to be 450min, the 2 upsetting is carried out, the temperature is pulled to 600mm, the forging ratio is selected to be 2.66, and the forged hot material is returned to the furnace to forge the No. 4 fire;
(3) upsetting and drawing after first beta recrystallization treatment
The 4 th fire beta recrystallization treatment temperature is selected to be Tt beta +120 ℃, the heat preservation time is selected to be 330min, the 1 heading is 1, the drawing is carried out to □ 545mm, the forging ratio is selected to be 1.30, and air cooling is adopted after forging;
(4) 2 nd upsetting of alpha + beta phase zone
The heating temperature of the 5 th fire is selected to be beta-45 ℃, the heat preservation time is selected to be 450min, the 2 nd upsetting is carried out for 2 mm to 600mm, the forging ratio is selected to be 2.30, and the forged hot material is returned to the furnace to forge the 6 th fire;
(5) upsetting and drawing after the 2 nd beta recrystallization treatment
The 6 th fire beta recrystallization treatment temperature is selected to be Ttbeta +80 ℃, the heat preservation time is selected to be 330min, the 1 heading is 1, the drawing is carried out to □ 545mm, the forging ratio is selected to be 1.30, and air cooling is adopted after forging;
(6) 3 rd time of alpha + beta phase region upsetting-drawing forming
The heating temperature of the No. 7 fire is selected to be Tss-45 ℃, the heat preservation time is selected to be 420min, the upsetting time of 1 is 3 mm, the forging ratio is 2.16, and air cooling is adopted after forging. The 8 th heating temperature is selected to be Tt beta-45 ℃, the heat preservation time is selected to be 420min, 3-drawing is carried out until □ 320mm, the forging ratio is selected to be 2.00, and air cooling is adopted after forging. The 9 th heating temperature is selected to be Tt beta-45 ℃, the heat preservation time is 240min, 2 is pulled to 250mm, the forging ratio is 1.96, and air cooling is adopted after forging. The 10 th heating temperature is selected to be beta-45 ℃, the heat preservation time is selected to be 150min, 2 drawing is carried out until phi is 215mm, the forging ratio is selected to be 1.34, and air cooling is adopted after forging.
Comparative example 1
The procedure of example one was repeated except that the 2 nd beta recrystallization followed by upsetting was not performed.
FIG. 1 is a macroscopic structure diagram of a bar material with a diameter of 200mm prepared by forging according to this example, which shows that there is no visible metallurgical defect at macroscopic level, and the structure is uniform and is in the form of fuzzy crystals. FIG. 2 is a macroscopic picture of the microstructure of a 200mm diameter bar produced by the forging process of comparative example one (without the 2 nd beta recrystallization heat treatment), showing visually abnormal growth of grains at macroscopic level and a non-uniform microstructure. Fig. 3 shows the microstructures of the edge and the core of the bar prepared by the first forging of this example, which shows that the microstructures of the edge and the core are very uniform and have no β spot region.
Example two
The free forging method of the TB6 titanium alloy large-size bar in the embodiment is realized by the following steps:
(1) cogging, upsetting and pulling after ingot casting high-temperature homogenization treatment
Selecting a cast ingot with the specification of phi 680mm, wherein the phase transformation point (Tbeta) is 795 ℃. The 1 st fire high temperature homogenization temperature is 1250 ℃, the heat preservation time is 2880min, the 1 st drawing and forging is carried out until the diameter is 610mm, the forging ratio is 1.17, and air cooling is adopted after forging; the 2 nd fire high temperature homogenization temperature is 1250 ℃, the heat preservation time is 2880min, the 2 nd upsetting 2 is forged to 600mm, the forging ratio is 7.84, and air cooling is adopted after forging;
(2) first alpha + beta phase region upsetting
The heating temperature of the No. 3 fire is selected to be Tss-40 ℃, the heat preservation time is selected to be 420min, the 2 upsetting is carried out, the temperature is pulled to 580mm, the forging ratio is selected to be 2.31, and the forged hot material is returned to the furnace to forge the No. 4 fire;
(3) upsetting and drawing after first beta recrystallization treatment
The 4 th fire beta recrystallization treatment temperature is selected to be Tt beta +120 ℃, the heat preservation time is selected to be 330min, the 1 heading is 1, the drawing is carried out to □ 530mm, the forging ratio is selected to be 1.30, and air cooling is adopted after forging;
(4) 2 nd upsetting of alpha + beta phase zone
The heating temperature of the 5 th fire is selected to be beta-40 ℃, the heat preservation time is selected to be 450min, the 2 nd upsetting is carried out for 2 min until 580mm, the forging ratio is selected to be 2.03, and the forged hot material is returned to the furnace to forge the 6 th fire;
(5) upsetting and drawing after the 2 nd beta recrystallization treatment
The 6 th heat beta recrystallization treatment temperature is selected to be Ttbeta +80 ℃, the heat preservation time is selected to be 330min, the 1 heading is 1, the drawing is carried out to □ 580mm, the forging ratio is selected to be 1.30, and air cooling is adopted after forging;
(6) 3 rd time of alpha + beta phase region upsetting-drawing forming
The heating temperature of the No. 7 fire is selected to be Tss-40 ℃, the heat preservation time is selected to be 450min, the 2 heading is 2 mm to 580mm, the forging ratio is 2.50, and air cooling is adopted after forging. The 8 th heating temperature is selected to be Tss-40 ℃, the heat preservation time is selected to be 450min, the 1 heading is 3 mm, the forging ratio is 2.28, and air cooling is adopted after forging. The 9 th heating temperature is selected to be beta-40 ℃, the heat preservation time is selected to be 330min, the temperature is 3 mm to be 380mm, the forging ratio is selected to be 1.68, and air cooling is adopted after forging. The 10 th heating temperature is selected to be beta-40 ℃, the heat preservation time is selected to be 270min, 1 drawing is carried out until phi 365mm, the forging ratio is selected to be 1.08, and air cooling is adopted after forging.
Comparative example No. two
The procedure is as in example two except that the high temperature homogenization treatment is not performed before the upsetting.
FIG. 4 is a macroscopic structure diagram of a bar of 350mm diameter prepared by forging according to example two, which shows that there is no visible metallurgical defect at macroscopic level, and the structure is uniform and fuzzy. Fig. 5 shows the microstructures of the edge and the core of the corresponding bar material prepared by forging according to example two, and it can be seen that the microstructures of the edge and the core are very uniform and have no β spot region. Fig. 6 shows the microstructures of the corresponding edge and the center of the bar with the phi 350mm specification prepared by the forging process of the comparative example II (without using high-temperature homogenization treatment), and it can be seen that the primary alpha phase content of the edge and the primary alpha phase content of the center are obviously different, and the beta spot area appears in the center.
Table 1 shows the variation of the fluctuation of Fe element composition after the high temperature homogenization treatment, and it can be seen that the fluctuation of Fe element is reduced from 0.37% to 0.12% after the high temperature homogenization treatment, so that the occurrence of β spot region can be effectively prevented after the high temperature homogenization treatment:
TABLE 1 compositional fluctuations of bars of 350mm diameter (change of Fe element after homogenization treatment at high temperature)
Claims (8)
1. A free forging method of a TB6 titanium alloy large-size bar is characterized in that a TB6 titanium alloy ingot is subjected to cogging and upsetting after high-temperature homogenization treatment; then carrying out first alpha + beta phase region upsetting; then carrying out first beta recrystallization treatment and upsetting and drawing; then, carrying out upsetting on the alpha + beta phase region for the 2 nd time; then carrying out 2 nd beta recrystallization treatment and then upsetting and drawing; finally, the alpha + beta phase region is upset and drawn for the 3 rd time.
2. The free forging method of the TB6 titanium alloy large-size bar according to claim 1, wherein in the step of cogging and upsetting after the high-temperature homogenization treatment, the heating temperature of the high-temperature homogenization treatment is controlled to be 1150-1300 ℃, and the total heat preservation time is not less than 2880 min.
3. The free forging method of TB6 titanium alloy large-size bars according to claim 2, which comprises the following steps:
(1) cogging, upsetting and pulling after ingot casting high-temperature homogenization treatment
The heating temperature of the high-temperature homogenization treatment is 1150-1300 ℃, the total heat preservation time is 2880-9000 min, the number of fire is controlled to be 1-2 fire, and the total forging ratio is controlled to be 5.00-10.00;
(2) first alpha + beta phase region upsetting
The heating temperature is 30-70 ℃ below the phase transition point, the heat preservation time is [ (0.50-0.85) multiplied by the minimum cross-sectional size of the blank ] min, the fire frequency is controlled to be 1 fire, and the total forging ratio is controlled to be 1.90-4.00;
(3) upsetting and drawing after first beta recrystallization treatment
The heating temperature of the first beta recrystallization treatment is 60-120 ℃ above the phase transition point, the heat preservation time is [ (0.30-0.60) multiplied by the minimum cross-sectional dimension of the blank +60 ] min, the heat frequency is controlled to be 1 fire, and the total forging ratio is controlled to be 1.20-1.50;
(4) 2 nd upsetting of alpha + beta phase zone
The heating temperature is 30-70 ℃ below the phase transition point, the heat preservation time is [ (0.50-0.85) multiplied by the minimum cross-sectional size of the blank ] min, the fire frequency is controlled to be 1 fire, and the total forging ratio is controlled to be 1.90-4.00;
(5) upsetting and drawing after the 2 nd beta recrystallization treatment
The heating temperature of the 2 nd beta recrystallization treatment is 60-100 ℃ above the transformation point, the heat preservation time is [ (0.30-0.60) multiplied by the minimum cross-sectional dimension of the blank +60 ] min, the fire frequency is controlled to be 1 fire, and the total forging ratio is controlled to be 1.20-1.50;
(6) 3 rd time of alpha + beta phase region upsetting-drawing forming
The heating temperature is 35-70 ℃ below the phase transition point, the heat preservation time is (0.50-0.85) multiplied by the minimum cross-sectional dimension of the blank min, the fire frequency is controlled to be 3-6 fires, and the total forging ratio is controlled to be 7.00-12.00.
4. The free forging method of the TB6 titanium alloy large-size bar according to claim 3, wherein in the step of cogging and upsetting after the ingot casting high-temperature homogenization treatment, the upsetting rate is controlled to be 5-30 mm/s, and hot material returning or air cooling is adopted after forging.
5. The free forging method of the TB6 titanium alloy large-size bar according to claim 3, wherein in the first alpha + beta phase region upsetting step and the 2 nd alpha + beta phase region upsetting step, the upsetting rate is controlled to be 5 mm/s-20 mm/s, and after forging, the hot material is returned to the furnace for the next beta recrystallization treatment and then forging is carried out.
6. The free forging method of TB6 titanium alloy large-size bars, according to claim 3, wherein in the upsetting step after the first beta recrystallization and the upsetting step after the 2 nd beta recrystallization, the upsetting rate is controlled to be 5 mm/s-30 mm/s, and air cooling is adopted after forging.
7. The free forging method of the TB6 titanium alloy large-size bar according to claim 3, wherein in the 3 rd upsetting and drawing step of the alpha + beta phase region, the upsetting rate is controlled to be 5-20 mm/s, and hot material returning or air cooling is adopted after forging.
8. A TB6 large-sized bar of titanium alloy produced by the free forging method of TB6 large-sized bar of titanium alloy as claimed in any one of the above claims.
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