Preparation method of high-uniformity large-size TA19 titanium alloy bar

Abstract

The application discloses a high-uniformity large-size TA19 titanium alloy rod preparation method and belongs to the technical field of high-quality titanium alloy material manufacturing technology. The process route of the application comprises two times of blooming, three times of upsetting, one time of pre-forming and one time of forming processes. The first time is three times of forging deformation above the beta phase transformation point, so that the original structure is completely broken, and the fine and uniform microstructure is ensured. The second time is one time of forging deformation below the beta phase transformation point and one time of remelting forging above the beta phase transformation point, and the temperature is accurately controlled during the remelting forging, so that the beta grain is prevented from being too large, and the transverse and longitudinal uniformity of the microstructure is ensured. The prepared TA19 titanium alloy rod with a diameter of 400 mm meets the index requirements in various performances, the transverse and longitudinal structures and performances of the rod are identical, the uniformity is good, and the performance is more excellent.

Description

TECHNICAL FIELD

[0001] The application belongs to the technical field of high-quality titanium alloy material manufacturing, and relates to manufacturing of TA19 titanium alloy, in particular to a high-uniformity large-specification TA19 titanium alloy rod preparation method. BACKGROUND

[0002] TA19 titanium alloy is a near-alpha type heat-resistant titanium alloy with good comprehensive performance, has the advantages of high specific strength, good creep performance and high-temperature endurance performance, and is widely used for manufacturing annular parts such as compressor discs and engine casings of an aero-engine. However, with the development needs of the overall, lightweight and integrated aero-engine, the commonly used specification TA19 titanium alloy rod cannot meet the aero-engine with large equipment, and therefore the development of TA19 large-specification rod is needed.

[0003] However, the alloy contains many alloying elements with high content, and the content of beta stabilizing elements is low, which leads to poor hot working process performance and narrow processing window, and the forging below the phase transition point is prone to cracking. In order to prevent crack propagation, the crack is polished, and the polishing loss is large, which not only prolongs the production cycle, but also increases the energy consumption, causes great waste of production cost, and seriously affects the product quality and yield. In addition, for large-specification rods with a diameter of 400 mm or more, the conventional forging method has many fire times, and is prone to unevenness of horizontal and vertical microstructures. SUMMARY

[0004] In view of the deficiencies in the prior art, the purpose of the present application is to provide a high-uniformity large-specification TA19 titanium alloy rod preparation method, which solves the technical problems of unevenness of horizontal and vertical microstructures of TA19 titanium alloy with a diameter of 400 mm or more due to poor hot working process performance and narrow processing window of TA19 titanium alloy, and large polishing amount and high production cost of the conventional forging method.

[0005] In order to solve the above technical problems, the technical scheme is adopted as follows:

[0006] A high-uniformity large-specification TA19 titanium alloy rod preparation method, which comprises the following steps:

[0007] Step 1: two-fire breakdown forging is performed to obtain a square billet:

[0008] Step 1.1, first open forging: at 130-160℃ above the beta phase transition point of TA19 titanium alloy, heat preservation for 6-10h, upsetting and drawing forging deformation; after forging, hot charge is recycled, the recycling temperature is 80-110℃ above the beta phase transition point of TA19 titanium alloy, heat preservation time is 2-5h, after discharging, upsetting and drawing forging deformation is carried out; after forging, hot charge is recycled, the recycling temperature is 30-60℃ above the beta phase transition point of TA19 titanium alloy, heat preservation time is 2-5h, after discharging, upsetting and drawing forging deformation is carried out.

[0009] Step 1.2, second open forging: at 20-50℃ below the beta phase transition point of TA19 titanium alloy, heat preservation for 6-10h, at least two times of upsetting and drawing forging deformation is carried out, and the upsetting and drawing deformation amount is controlled at 30-40% each time; after forging, hot charge is recycled, the recycling temperature is 30-60℃ above the beta phase transition point of TA19 titanium alloy, heat preservation time is 4-6h, after discharging, upsetting and drawing forging deformation is carried out.

[0010] Step two, three times of upsetting and drawing of the square billet is carried out to obtain the upset and drawn square billet:

[0011] The first time of upsetting and drawing includes: at 20-50℃ below the beta phase transition point of TA19 titanium alloy, heat preservation for 6-10h, upsetting and drawing forging deformation is carried out; after forging, hot charge is recycled, the recycling temperature is 20-50℃ below the beta phase transition point of TA19 titanium alloy, heat preservation time is 2-4h; after discharging, upsetting and drawing forging deformation is carried out; after forging, hot charge is recycled, the recycling temperature is 20-50℃ below the beta phase transition point of TA19 titanium alloy, heat preservation time is 2-4h, after discharging, upsetting and drawing forging deformation is carried out; during the upsetting and drawing, the square billet is wrapped with asbestos.

[0012] The specific process of the second and third times of upsetting and drawing is completely the same as that of the first time of upsetting and drawing.

[0013] Step three, one time of pre-forming forging of the upset and drawn square billet is carried out to obtain the pre-formed square billet:

[0014] At below the beta phase transition point, elongation forging is carried out, and the elongation forging conditions are: at 20-40℃ below the beta phase transition point of TA19 titanium alloy, heat preservation for 4-7h; the upsetting and drawing deformation amount is controlled at 25%-35% each time, the pressing speed during elongation is controlled at 25-35mm / s, the pressing amount is controlled at 75-150mm, and the feeding amount is controlled at 300-400mm; after forging, hot charge is recycled, the recycling temperature is 20-40℃ below the beta phase transition point of TA19 titanium alloy, heat preservation time is 1-3h, after discharging, diagonal elongation is carried out.

[0015] Step four, one time of forming forging of the pre-formed square billet is carried out:

[0016] The TA19 titanium alloy is kept at 20-40 DEG C below the beta phase transition point for 4-6 hours, and is formed by drop-rounding; during drop-rounding, the pressing speed is 25-30 mm / s, the pressing reduction is 10-20 mm, and the feeding amount is 50-150 mm; after drop-rounding, the hot material is re-melted, the re-melting temperature is 20-40 DEG C below the beta phase transition point of the TA19 titanium alloy, and the holding time is 0.5-2 hours.

[0017] The preparation method as described above is suitable for the TA19 titanium alloy bar with a diameter of greater than or equal to 400 mm.

[0018] Compared with the prior art, the present application has the beneficial technical effects that:

[0019] (I) The present application adopts two-pass blooming forging, the first pass is three times of forging deformation above the beta phase transition point, so that the original structure is completely broken, ensuring that the microstructure is small and uniform; the second pass is one time of forging deformation below the beta phase transition point and re-melting forging above the beta phase transition point, and the temperature is accurately controlled during re-melting forging, preventing the beta grains from being too large, and ensuring the transverse and longitudinal uniformity of the microstructure.

[0020] (II) The process route of the present application includes two-pass blooming, three-pass open-die forging, one-pass pre-forming and one-pass forming processes, the number of passes and lengths of drawing are small, the properties of the finally prepared large-size TA19 titanium alloy bar with a diameter of 400 mm all meet the index requirements, the transverse and longitudinal structure and properties of the bar are uniform, and the properties are more excellent. The present application optimizes the bar processing technology, improves the quality of the bar and the material utilization rate, and has important significance for improving the performance of an aero-engine and reducing the risk of engine accidents. BRIEF DESCRIPTION OF DRAWINGS

[0021] Figure 1 The macroscopic morphology graph of the TA19 titanium alloy bar prepared in Example 1 under a low-power lens. Figure 1 Fig. 2 is a macroscopic morphology graph of the TA19 titanium alloy bar prepared in Example 1 under a high-power lens.

[0022] Figure 2 The microstructure graph of the TA19 titanium alloy bar prepared in Example 1 under a high-power lens. Figure 2 Fig. 2 is a macroscopic morphology graph of the TA19 titanium alloy bar prepared in Example 1 under a high-power lens.

[0023] The technical solutions of the present application are further described below in combination with embodiments. DETAILED DESCRIPTION

[0024] It should be noted that all the materials used in the present application are known in the art, for example, TA19 titanium alloy is a known titanium alloy in the art, and its composition is: Al 6.0 wt%, Sn 2.0 wt%, Zr 4.0 wt%, Mo 2.0 wt%, Si 0.12 wt%, and the balance is Ti, and its beta phase transition point (T β ) is 990-1020℃; T β below 1005℃, and T β above 1005℃.

[0025] In accordance with the above technical solutions, specific embodiments of the present application are given below, and it should be noted that the present application is not limited to the following specific embodiments, and any equivalent variations made on the basis of the technical solutions of the present application fall within the scope of the present application.

[0026] Embodiment 1

[0027] This embodiment gives a method for preparing high-uniformity large-size TA19 titanium alloy rod, which is used to prepare titanium alloy rod with a diameter of 400mm, and specifically comprises the following steps:

[0028] Step one, two times of blooming forging is performed to obtain square billets with fine beta structure:

[0029] Step 1.1, first time of blooming forging: TA19 titanium alloy ingot is forged at a temperature above the beta phase transition point. The first blooming temperature is T β above 150℃, and the temperature is kept for 7h, and four times of upsetting and drawing are performed, with deformation amounts of 37%, 30%, 36% and 36% respectively; after forging, the hot material is returned to the furnace, and the return-to-furnace temperature is T β above 100℃, and the temperature is kept for 3h, and four times of upsetting and drawing are performed after the furnace is discharged, and the direction is changed during the drawing process to better break the grains and obtain uniform structure, and the deformation amount of each upsetting and drawing is controlled to be 36%; after forging, the hot material is returned to the furnace, and the return-to-furnace temperature is T β above 50℃, and the temperature is kept for 3h, and two times of upsetting and drawing are performed after the furnace is discharged, and inverted octagonal square is performed after the second drawing to reduce the deformation dead zone, and the deformation amount of each upsetting and drawing is controlled to be 36%, and the forged material is air-cooled and polished; the pressing speed of the forging process is controlled to be 40mm / s, the reduction amount is controlled to be 120mm, and the feed amount is controlled to be 450mm; beta structure with a grain size distribution of 5-15mm is obtained.

[0030] Step 1.2, second heating open-die forging: low temperature forging below the β phase transition point, heating temperature is T β The following 30℃, 8h, two upsetting and drawing forging was carried out, and the square billet was wrapped with heat preservation asbestos during the upsetting and drawing process to prevent surface temperature reduction from causing cracking, and the deformation amount of each upsetting and drawing was controlled at 36%. After forging, hot material was recycled, and the recycling temperature was T β The above 50℃, 5h, one upsetting and drawing forging was carried out after discharging, and inverted octagonal square was carried out after the elongation to reduce the deformation dead zone, the deformation amount of each upsetting and drawing was controlled at 36%, and the square was air-cooled after forging and polished; the pressing speed during the forging process was controlled at 40mm / s, the reduction amount was controlled at 120mm, and the feed amount was controlled at 450mm; the β organization with grain size distribution of 2-4mm was obtained.

[0031] Step two, the square billet obtained in step one was subjected to three heating open-die forging to obtain the square billet after open-die forging:

[0032] The first heating low temperature forging below the β phase transition point, heating temperature is T β The following 30℃, 8h, one upsetting and drawing forging was carried out, and the square billet was wrapped with heat preservation asbestos during the upsetting and drawing process to prevent surface temperature reduction from causing cracking, and the deformation amount of each upsetting and drawing was controlled at 36%; after forging, hot material was recycled, and the recycling temperature was T β The following 30℃, 3h, one upsetting and drawing forging was carried out after discharging, and the square billet was wrapped with heat preservation asbestos during the upsetting and drawing process, and the deformation amount of each upsetting and drawing was controlled at 36%; after forging, hot material was continuously recycled, and the recycling temperature was T β The following 30℃, 3h, one upsetting and drawing forging was carried out after discharging, and inverted octagonal square was carried out after the elongation to reduce the deformation dead zone, the deformation amount of each upsetting and drawing was controlled at 36%, and the square was air-cooled after forging and polished; the pressing speed during the forging process was controlled at 30mm / s, the reduction amount was controlled at 120mm, and the feed amount was controlled at 450mm; the forging process of the second and third heating was the same as that of the first heating.

[0033] Step three, one heating pre-forming forging was carried out on the square billet after open-die forging obtained in step two:

[0034] The square billet with eight square cross section was subjected to low temperature elongation forging below the β phase transition point, and the heating temperature was T β The following 30℃, 5h, diagonal elongation forging was carried out, and the deformation amount of each upsetting and drawing was controlled at 30%, the pressing speed was controlled at 30mm / s, the reduction amount was controlled at 100mm, and the feed amount was controlled at 350mm; after forging, hot material was recycled, and the recycling temperature was T βThe following 30℃, 2h, after the furnace diagonal length, and after the end of the length of the eight square, each upsetting deformation control in 25%, pressing speed control in 30mm / s, reduction control in 70mm, feed control in 300mm, air cooling after forging, polishing.

[0035] Step four, the square billet after preforming forging of step three is formed by one time forming forging:

[0036] The cross section of the bar is eight square, which is formed by low temperature drop round forming below the beta phase transition point, the heating temperature is T β The following 30℃, 5h, drop round each upsetting deformation control in 12%, pressing speed control in 30mm / s, reduction control in 15mm, feed control in 100mm, in the process, in order to prevent the temperature from being too low and causing cracking, the hot material is allowed to be recycled, the recycling temperature is TA19 titanium alloy beta phase transition point below 30℃, the recycling time is 1.5h; Air cooling after forging, polishing.

[0037] Effect verification of example 1:

[0038] Figure 1 TA19 titanium alloy prepared by the preparation method The macrostructure of the cross section of the head and tail of the large size bar can be seen that there is no crack, folding, pore, metal or non-metallic inclusion, segregation, tail shrinkage and other visible metallurgical defects, and there is no obvious visual clear grain, which is uniform and fuzzy.

[0039] Figure 2 TA19 titanium alloy prepared by the preparation method The high magnification structure of the cross section of the head and tail of the large size bar, the edge of the longitudinal section, R / 2 and the core position can be seen that the high magnification structure is composed of equiaxed alpha phase and a small amount of lamellar primary alpha phase, the high magnification structure is uniform, and there is no overheated structure abnormality and continuous alpha network structure on the original beta grain boundary.

[0040] Table 3 is TA19 titanium alloy prepared by the preparation method The mechanical properties of the large size bar cross section R / 2 position horizontal and longitudinal sampling can be seen that the detection results meet the requirements of the aviation standard, the uniformity is good and has a certain amount of surplus.

[0041] Table 3, the mechanical properties of the bar cross section R / 2 position horizontal and longitudinal sampling

[0042]

[0043] Comparative example 1 (different upsetting forging temperature of step 1.1):

[0044] The present comparative example gives a preparation method of high uniformity large size TA19 titanium alloy bar, which is basically the same as example 1, the difference is only that the first upsetting forging temperature of step 1.1 is different.

[0045] In the present comparative example, step 1.1 includes: the first upsetting temperature is T β The above 200℃, 7h, 4 times of upsetting and drawing deformation, the deformation amount is: 37%, 30%, 36%, 36%; after forging, the hot material is recycled, the recycling temperature is T β The above 150℃, 3h, after discharging, 4 times of upsetting and drawing deformation, and in the drawing process, the reversing is increased to better break the grains and obtain uniform organization, the upsetting and drawing deformation amount is controlled at 36% each time; after forging, the hot material is recycled, the recycling temperature is T β The above 80℃, 3h, after discharging, 4 times of upsetting and drawing deformation, and in the drawing process, the reversing is increased to better break the grains and obtain uniform organization, the upsetting and drawing deformation amount is controlled at 36% each time; after forging, the hot material is recycled, the recycling temperature is T

[0046] In the present comparative example, because the deformation is at a higher temperature, the original organization is not completely broken, the density is low, and the microstructure is not uniform, so the finally prepared titanium alloy bar has a non-uniform microstructure, which is difficult to meet the technical requirements.

[0047] Comparative example 2 (the forging process of step 1.2 is different):

[0048] The present comparative example gives a preparation method of high uniformity large size TA19 titanium alloy bar, which is basically the same as example 1, the difference is only that the first upsetting forging temperature of step 1.1 is different.

[0049] In the present comparative example, step 1.2 includes: low temperature forging below the beta phase transition point, the heating temperature is T β The above 30℃, 8h, one upsetting and drawing deformation, and in the upsetting and drawing process, the square billet is wrapped with heat preservation asbestos to prevent cracking caused by surface temperature reduction, the upsetting and drawing deformation amount is controlled at 36% each time. After forging, the hot material is recycled, the recycling temperature is T β The above 50℃, 5h, one upsetting and drawing deformation, and in the drawing process, the square billet is wrapped with heat preservation asbestos to prevent cracking caused by surface temperature reduction, the upsetting and drawing deformation amount is controlled at 36% each time. After forging, the hot material is recycled, the recycling temperature is T

[0050] In the present comparative example, since only one upsetting and drawing deformation is experienced at 30°C below the phase transition point, the deformation amount is insufficient, resulting in that the β grains cannot be recrystallized when deformed at 50°C above the phase transition point, and the microstructure of the titanium alloy bar finally prepared is non-uniform, microtexture exists, and the performance difference between the bar in the transverse and longitudinal directions is large, which is difficult to meet the technical requirements.

[0051] Comparative Example 3 (different re-forging temperature in step 1.2):

[0052] The present comparative example gives a preparation method of high-uniformity large-size TA19 titanium alloy bar, which is basically the same as that in Example 1, and the only difference is that the second re-forging temperature in step 1.2 is different.

[0053] In the present comparative example, step 1.2 includes: low-temperature forging below the β phase transition point, the heating temperature is T β The above 30°C, the temperature is kept for 8h, two upsetting and drawing forgings are performed, and heat-resistant asbestos is used to wrap the square billet during the upsetting and drawing process to prevent cracking caused by the reduction of the surface temperature, and the deformation amount of each upsetting and drawing is controlled to be 36%. After forging, hot material re-forging is performed, and the re-forging temperature is T β The above 80°C, the temperature is kept for 5h, one upsetting and drawing forging is performed after the billet is discharged, and inverted octagonal square is performed after the elongation is completed to reduce the deformation dead zone, the deformation amount of each upsetting and drawing is controlled to be 36%, and the forged product is air-cooled and polished; the pressing speed during the forging process is controlled to be 40mm / s, the reduction amount is controlled to be 120mm, and the feed amount is controlled to be 450mm.

[0054] In the present comparative example, since the second time is deformed at T β The above 80°C high temperature deformation causes the β grains to grow, the microstructure of the titanium alloy bar finally prepared is non-uniform, microtexture exists, and the performance difference between the bar in the transverse and longitudinal directions is large, which is difficult to meet the technical requirements.

[0055] Comparative Example 4 (insulation cotton is not used in the process of re-forging in step 2):

[0056] The present comparative example gives a preparation method of high-uniformity large-size TA19 titanium alloy bar, which is basically the same as that in Example 1, and the only difference is that the insulation cotton is not used in the process of re-forging in step 2.

[0057] In the present comparative example, step 2 includes: low-temperature forging below the β phase transition point in the first heating, and the heating temperature is T β The above 30°C, the temperature is kept for 8h, one upsetting and drawing forging is performed, and the deformation amount of each upsetting and drawing is controlled to be 36%; after forging, hot material re-forging is performed, and the re-forging temperature is T β The above 30°C, the temperature is kept for 3h, one upsetting and drawing forging is performed after the billet is discharged, and the deformation amount of each upsetting and drawing is controlled to be 36%; after forging, hot material re-forging is continuously performed, and the re-forging temperature is T βThe following 30℃, 3h, after the furnace to carry out a upsetting and drawing forging, and after the drawing end to carry out the inverted octagonal, reduce the deformation dead zone, each upsetting and drawing deformation control in 36%, after forging air cooling, grinding; The pressing speed control in the forging process is 30mm / s, the reduction is controlled at 120mm, and the feed amount is controlled at 450mm; The second and third forging processes are the same as the first time.

[0058] In the present comparative example, since the deformation resistance of TA19 is large, the square billet is not wrapped with heat preservation asbestos during upsetting and drawing, which leads to the reduction of the surface temperature of the billet, the occurrence of cracks during forging, and the increase of the polishing amount of the finally obtained titanium alloy bar and the cost.

[0059] Comparative example 5 (different deformation rate in step three):

[0060] The present comparative example gives a preparation method of high uniformity large specification TA19 titanium alloy bar, which is basically the same as example 1, and the difference is only that the deformation rate in step three is different.

[0061] The square billet with an octagonal cross section is subjected to low-temperature drawing forging below the β phase transition point, and the heating temperature is T β The following 30℃, 5h, diagonal drawing forging is carried out, the upsetting and drawing deformation amount is controlled at 30% each time, the pressing speed is controlled at 20mm / s, the reduction is controlled at 100mm, and the feed amount is controlled at 350mm; After forging, the hot material is recycled, and the recycling temperature is T β The following 30℃, 2h, after the furnace to carry out a diagonal drawing, and after the drawing end to carry out the inverted octagonal, each upsetting and drawing deformation control in 25%, the pressing speed control in 20mm / s, the reduction control in 70mm, the feed amount control in 300mm, after forging air cooling, grinding.

[0062] In the present comparative example, the pressing speed is low, and the bar blank is long, which leads to the increase of the forming time, the reduction of the bar temperature, the occurrence of cracking, the increase of the polishing amount of the final product bar, and the increase of the cost.

[0063] Comparative example 6 (no hot material recycling in step four):

[0064] The present comparative example gives a preparation method of high uniformity large specification TA19 titanium alloy bar, which is basically the same as example 1, and the difference is only that no hot material recycling is carried out in step four.

[0065] In the present comparative example, step four includes: the bar blank with an octagonal cross section is subjected to low-temperature round forming below the β phase transition point, and the heating temperature is T βThe following 30℃, incubation for 5h, each time round pull deformation control in 12%, the pressing speed control in 30mm / s, the pressing amount control in 15mm, the feed amount control in 100mm, in the process, do not carry out the hot material reheat; after forging air cooling, polishing.

[0066] In the present comparative example, due to long processing time, and not allowed to reheat, resulting in the bar in the later lower temperature forming, surface cracks, increase the polishing amount, cost increase.

Claims

1. A method of producing high uniformity large size TA19 titanium alloy bar, characterized by, The method comprises the following steps: Step one, two open forging is carried out to obtain square billet: Step 1.1, first open forging: 130-160℃ above the beta phase transition point of TA19 titanium alloy for 6-10h, upsetting and drawing forging deformation is carried out; after forging, hot material is recycled, the recycling temperature is 80-110℃ above the beta phase transition point of TA19 titanium alloy, the holding time is 2-5h, after discharging, upsetting and drawing forging deformation is carried out; after forging, hot material is recycled, the recycling temperature is 30-60℃ above the beta phase transition point of TA19 titanium alloy, the holding time is 2-5h, after discharging, upsetting and drawing forging deformation is carried out; Step 1.2, second open forging: 20-50℃ below the beta phase transition point of TA19 titanium alloy for 6-10h, at least two times of upsetting and drawing forging deformation is carried out, and the upsetting and drawing deformation amount is controlled to be 30-40% each time; after forging, hot material is recycled, the recycling temperature is 30-60℃ above the beta phase transition point of TA19 titanium alloy, the holding time is 4-6h, after discharging, upsetting and drawing forging deformation is carried out; Step two, three open forgings are carried out on the square billet to obtain the square billet after open forging: The first open forging comprises: 20-50℃ below the beta phase transition point of TA19 titanium alloy for 6-10h, upsetting and drawing forging deformation is carried out; after forging, hot material is recycled, the recycling temperature is 20-50℃ below the beta phase transition point of TA19 titanium alloy, the holding time is 2-4h; after discharging, upsetting and drawing forging deformation is carried out; after forging, hot material is recycled, the recycling temperature is 20-50℃ below the beta phase transition point of TA19 titanium alloy, the holding time is 2-4h, after discharging, upsetting and drawing forging deformation is carried out; The specific process of the second and third open forgings is completely same as that of the first open forging; Step three, one open forging is carried out on the square billet after open forging to obtain the square billet after open forging: Drawing forging is carried out below the beta phase transition point, and the drawing forging condition is: 20-40℃ below the beta phase transition point of TA19 titanium alloy for 4-7h; the upsetting and drawing deformation amount is controlled to be 25%-35% each time, the pressing speed is controlled to be 25-35mm / s, the pressing amount is controlled to be 75-150mm, and the feeding amount is controlled to be 300-400mm; after forging, hot material is recycled, the recycling temperature is 20-40℃ below the beta phase transition point of TA19 titanium alloy, the holding time is 1-3h, and diagonal drawing is carried out after discharging; Step four, one open forging is carried out on the square billet after open forging: Round forming is carried out at 20-40℃ below the beta phase transition point of TA19 titanium alloy for 4-6h; during the round forming, the pressing speed is 25-30mm / s, the pressing amount is 10-20mm, and the feeding amount is 50-150mm; after the round forming, hot material is recycled, the recycling temperature is 20-40℃ below the beta phase transition point of TA19 titanium alloy, and the holding time is 0.5-2h.

2. The method of producing high uniformity large size TA19 titanium alloy bar according to claim 1, wherein During the open forging, the square billet is wrapped with asbestos.

3. The method of claim 1, wherein the high uniformity large size TA19 titanium alloy bar is produced by the steps of: The preparation method is suitable for TA19 titanium alloy rods with a diameter of greater than or equal to 400mm. ​

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