Efficient homogenizing forging method for large-specification titanium alloy cast ingot

Abstract

The invention discloses an efficient homogenizing forging method for a large-size titanium alloy cast ingot, which comprises the following steps of: 1, preserving heat at 150-250 DEG C above a phase transformation point, and forging to ensure that the height-diameter ratio of a forging stock is less than 2.5; 2, forging after remelting and heat preservation; thirdly, forging is conducted after heat preservation is conducted at the temperature 50-150 DEG C above the phase transformation point; fourthly, forging is conducted after heat preservation is conducted at the temperature 20-40 DEG C below the phase transformation point; 5, preserving heat at 10-40 DEG C above the phase transformation point, and cooling with water; and 6, carrying out heat preservation at the temperature of 20-40 DEG C below the phase transformation point, and then forging. According to the method, the height-diameter ratio is suitable for deformation through slow-pressing upsetting and shaping, excessive growth of crystal grains in the deformation process is restrained, and partial stress concentration in the deformation process is released in time, so that it is guaranteed that the crystal grains are broken, and meanwhile cast ingots do not crack; by chamfering, flattening or drawing out, the forging stock uniformly deforms at multiple angles, small deformation of the contact part of the forging stock and the anvil surface and cracking of the side surface of the forging stock under the action of tensile stress are avoided, and the method is suitable for the technical field of titanium alloy material processing.

Description

Technical Field

[0001] The invention belongs to the technical field of titanium alloy material processing, and in particular relates to a high-efficiency homogenization forging method for large-size titanium alloy ingots. Background Art

[0002] Titanium alloys have been widely used in aviation, aerospace, ships, weapons, petroleum, chemical industry, medical and other fields due to their high specific strength, high temperature resistance, corrosion resistance, weldability and other excellent properties. With the implementation of major projects in the fields of aviation, aerospace, ships, etc., the performance requirements of materials are constantly increasing, and the material specifications are also increasing. For example, the demand for large-sized wide and thick plates, super-large-sized titanium alloy bars (diameter greater than 300mm), etc. is growing, which requires the material billet specifications to continue to increase. However, the larger the billet specifications, the more difficult it is to process the material, the poorer the forging uniformity, and the more difficult it is to homogenize the organization.

[0003] In order to ensure uniformity, conventional processing requires cutting the ingot into smaller pieces and then performing multiple uniform deformations to ensure the forgeability and uniformity of the material structure, but it cannot meet the use requirements of large forgings; at the same time, due to the reduction of the billet and the increase in the number of furnaces, the processing cost of the material will increase, and the organizational properties of each billet will also be different. Therefore, it is more conducive to reducing costs and improving the uniformity of the forging structure to use large-sized ingots for direct forging. At present, the height-to-diameter ratio of large-sized titanium alloy ingots generally exceeds 2.5, while the height-to-diameter ratio is required not to exceed 2.5 during conventional forging; a larger height-to-diameter ratio is prone to billet bending or double drumming during the upsetting process, and a larger cross-sectional area will also increase the deformation dead zone, resulting in uneven organizational deformation during the billet forging process. Summary of the invention

[0004] The purpose of the present invention is to overcome the deficiencies in the above-mentioned prior art and provide a high-efficiency homogenization forging method for large-size titanium alloy ingots. The forging method obtains a forging blank with a height-to-diameter ratio suitable for deformation by performing slow pressure upsetting and shaping, and can inhibit excessive growth of grains during deformation, and timely release part of the stress concentration that occurs during deformation, so as to ensure that the ingot does not crack while the grains are broken; by adopting the process of chamfering flattening and chamfering elongation during forging, the forging blank can be uniformly deformed at multiple angles, avoiding the small or no deformation of the contact part between the forging blank and the anvil surface during the deformation process, and the cracking or uneven deformation of the side of the forging blank under the action of tensile stress, solving the problem of billet bending or double drumming and uneven deformation during forging of large-size ingots.

[0005] To achieve the above object, the technical solution adopted by the present invention is: a high-efficiency homogenization forging method for large-size titanium alloy ingots, characterized in that the forging method comprises the following steps:

[0006] Step 1, heating an ingot with a height-to-diameter ratio greater than 2.5 to 150° C. to 250° C. above the phase transition point, and then performing a first forging to obtain a first forging blank with a height-to-diameter ratio less than 2.5; the first forging process includes slow pressing and upsetting deformation, and shaping during the slow pressing and upsetting deformation process;

[0007] Step 2, returning the first forging blank obtained in step 1 to the furnace for heat preservation and then performing a second forging to obtain a second forging blank;

[0008] Step 3, heating the second forging blank obtained in step 2 to 50°C to 150°C above the phase transformation point and then performing a third forging to obtain a third forging blank; the third forging process is: repeating the processes of chamfering and flattening along the height direction, shaping, upsetting along the height direction, and chamfering and lengthening along the length direction for 2 times;

[0009] Step 4, the third forging blank obtained in step 3 is kept at 20°C to 40°C below the phase transformation point and then subjected to a fourth forging to obtain a fourth forging blank;

[0010] Step 5, the fourth forging blank obtained in step 4 is kept at 10°C to 40°C above the phase transformation point and then water-cooled;

[0011] Step 6: After the fourth forging blank is water-cooled in step 5, it is kept at 20°C to 40°C below the phase transformation point, and then subjected to the fifth forging and shaping to obtain a forging with uniform structure.

[0012] The present invention sets the first forging and the first fire to be a relatively high temperature deformation of 150℃ to 250℃ above the phase transformation point. Under this temperature condition, the cast structure has good fluidity, high plasticity, low deformation resistance, and is easy to deform. Especially for large-sized ingots with coarse grain size, the deformed ingots are not easy to crack at this temperature; because the coarse grains are broken to a certain extent after the first forging, the internal structure is improved and the plasticity of the material is improved, so the temperature of the subsequent forging process is gradually reduced. By controlling the temperature to be 10℃ to 40℃ above the phase transformation point and then water cooling, the purpose is to homogenize the structure of the previous forging, and after water cooling, fine lamellar structure can be obtained, a certain distortion energy can be stored, and dynamic recrystallization is ensured in the subsequent forging process to obtain fine equiaxed grains.

[0013] The invention obtains a forging blank with a height-to-diameter ratio suitable for deformation by performing slow pressure upsetting and shaping, and can inhibit excessive growth of crystal grains during deformation and timely release partial stress concentration occurring during deformation, so as to ensure that the ingot does not crack while the crystal grains are broken; the heat loss during the previous deformation process is supplemented by remelting and heat preservation, so as to facilitate subsequent upsetting and drawing forging; then, the material is ensured to have good fluidity by controlling the temperature above the phase transition point, and multi-angle uniform deformation forging is performed in combination with chamfering flattening and chamfering drawing, which can reduce the contact area between the forging blank and the forging anvil and reduce the deformation dead zone, and can improve the deformation uniformity of the edges and corners and the forging blank, so as to avoid the small deformation or no deformation of the contact part between the forging blank and the anvil surface during the deformation process, and the cracking or uneven deformation of the side surface of the forging blank under the action of tensile stress, specifically:

[0014] Chamfering and flattening along the height direction can reduce the contact area between the blank and the forging anvil in the subsequent upsetting process, and reduce the deformation dead zone; chamfering and stretching along the length direction can avoid the deformation at the corners and the contact surface with the forging anvil from being inconsistent with the deformation of the core, and avoid repeated upsetting and stretching.

[0015] The above-mentioned high-efficiency homogenization forging method for a large-size titanium alloy ingot is characterized in that the pressing rate of the slow upsetting deformation in step 1 is 30 mm / s to 40 mm / s, and the pressing amount is 15% to 30%; the insulation time t1 is calculated by the following formula:

[0016] t1=η1×D1;

[0017] Wherein, t1 is the holding time, in min; D1 is the cross-sectional diameter of the ingot in step 1, in mm; η1 is the heating coefficient, in the range of 0.7 to 0.9.

[0018] The above-mentioned high-efficiency homogenization forging method for large-size titanium alloy ingots is characterized in that the second forging in step 2 is to perform 2 to 3 times of upsetting deformation, and the drawing process of the upsetting deformation includes chamfering deformation.

[0019] The above-mentioned high-efficiency homogenization forging method for a large-size titanium alloy ingot is characterized in that the pressing amount of the chamfering and flattening in the height direction in step 3 is 10% to 15%, and the pressing rate is 30 mm / s to 40 mm / s; the upsetting ratio of the upsetting in the height direction is 1.2 to 1.6; the pressing amount of the chamfering and stretching in the length direction is 10% to 20%; the holding time t2 is calculated by the following formula:

[0020] t2=η2×D2;

[0021] Among them, t2 is the insulation time, the unit is min; D2 is the minimum cross-sectional average thickness of the second forging blank in step three, the unit is mm; η2 is the heating coefficient, the value range is 0.6 to 0.8.

[0022] The above-mentioned high-efficiency homogenization forging method for a large-size titanium alloy ingot is characterized in that the upsetting deformation in the fourth forging in step 4 is not less than 2 times, and the cumulative deformation of the single upsetting deformation is not less than 85%; the insulation time t3 is calculated by the following formula:

[0023] t3 = η3 × D3;

[0024] Wherein, t3 is the holding time, in min; D3 is the minimum cross-sectional average thickness of the third forging blank described in step 4, in mm; η3 is the heating coefficient, in the range of 0.6 to 0.8.

[0025] The present invention ensures that the accumulated deformation of a single upsetting deformation is not less than 85%, thereby ensuring that the forging blank does not crack while ensuring that the deformation of a single upsetting deformation is large enough.

[0026] The above-mentioned high-efficiency homogenization forging method for a large-size titanium alloy ingot is characterized in that the insulation time t2 in step 5 is calculated by the following formula:

[0027] t4 = η4 × D4;

[0028] Wherein, t4 is the holding time, in min; D4 is the minimum cross-sectional average thickness of the fourth forging blank described in step 5, in mm; η4 is the heating coefficient, in the range of 0.6 to 0.8.

[0029] The above-mentioned high-efficiency homogenization forging method for large-size titanium alloy ingots is characterized in that the upsetting deformation in the fifth forging in step six is ​​not less than 2 times, and the cumulative deformation amount of the single upsetting deformation is not less than 80%.

[0030] The present invention is used to ensure that the forging blank is fully deformed by setting the number of upsetting deformations and the cumulative deformation amount of a single upsetting deformation to be not less than 80%.

[0031] The above-mentioned high-efficiency homogenization forging method for a large-size titanium alloy ingot is characterized in that the insulation time t5 in step 6 is calculated by the following formula:

[0032] t5 = η5 × D5;

[0033] Wherein, t5 is the holding time, in min; D5 is the minimum cross-sectional average thickness of the fourth forging blank described in step 6, in mm; η5 is the heating coefficient, in the range of 0.6 to 0.8.

[0034] Compared with the prior art, the present invention has the following advantages:

[0035] 1. The present invention obtains a forging blank with a height-to-diameter ratio suitable for deformation by performing slow upsetting, and can inhibit excessive growth of crystal grains during deformation and timely release partial stress concentration occurring during deformation, thereby controlling the deformation amount within a certain range to ensure that crystal grains are broken without cracking; shaping is performed during the slow upsetting process to ensure the straightness of the ingot, thereby facilitating continued upsetting deformation until the height-to-diameter ratio of the ingot is suitable for forging; and then, by adopting the processes of chamfering and chamfering during the forging process, the forging blank is uniformly deformed at multiple angles, thereby avoiding that the contact portion between the forging blank and the anvil surface is less deformed or not deformed during the deformation process, and that the side surface of the forging blank is cracked or deformed unevenly under the action of tensile stress, thereby avoiding the phenomenon of bending or double-drum formation of large-size ingots during subsequent forging.

[0036] 2. The present invention avoids the reduction of billet size caused by the use of split-material forging in the prior art and the differences in organizational properties between billets by forging a large-sized ingot as a whole.

[0037] 3. The present invention can homogenize the two-phase region structure after forging in the β region by forging below the phase transformation point, keeping warm above the phase transformation point, and then water cooling, thereby providing a forging blank with uniform structure for subsequent forging. At the same time, the needle-shaped martensite produced after water cooling can be broken in the forging process to produce fine equiaxed grains, thereby optimizing the performance while homogenizing the forging blank structure.

[0038] 4. The present invention determines the holding time by the cross-sectional size of the ingot or the forging blank at each stage. The heat progress during the holding period is 1 mm per minute. Therefore, the basic heating time is taken as 0.5 times of the cross-sectional size. Then, the heating coefficient is increased based on the basic heating time according to the blank conditions and the cross-sectional size to ensure that the ingot or the forging blank at each stage is fully heated.

[0039] The technical solution of the present invention is further described in detail below through the accompanying drawings and embodiments. BRIEF DESCRIPTION OF THE DRAWINGS

[0040] Figure 1 This is a physical diagram of the forging process of the chamfering and flattening process of the present invention.

[0041] Figure 2 This is a physical diagram of the forging process of the chamfering and flattening followed by upsetting process of the present invention.

[0042] Figure 3 This is a microstructure diagram of the surface of the rod obtained in Example 1 of the present invention.

[0043] Figure 4 This is a microstructure diagram of the center portion of the rod obtained in Example 1 of the present invention.

[0044] Figure 5 This is a microstructure diagram of the surface of the plate obtained in Example 2 of the present invention.

[0045] Figure 6 This is a microstructure diagram of the central part of the plate obtained in Example 2 of the present invention.

[0046] Figure 7 This is a microstructure diagram of the surface of the rod obtained in Example 3 of the present invention.

[0047] Figure 8 This is a microstructure diagram of the center portion of the rod obtained in Example 3 of the present invention. DETAILED DESCRIPTION

[0048] Example 1

[0049] The TA16 ingot of this embodiment has a size of Φ248mm×875mm and a height-to-diameter ratio of 3.5 after peeling and riser cutting. The forging method of the ingot comprises the following steps:

[0050] Step 1, the ingot is heated to 1160°C and kept for 180min before the first forging is performed. First, the first upsetting is performed along the height direction at a pressing rate of 40mm / s and a pressing amount of 15%, and then the second upsetting is performed at a pressing rate of 30mm / s and a pressing amount of 30%. The ingot is shaped along the axial direction to make it straight, and then the third upsetting is performed along the height direction at a pressing rate of 40mm / s and a pressing amount of 25% to obtain an ingot with a diameter of 354mm. The forged billet is then stretched to obtain a square billet (first forged billet) with a size of 265mm×265mm and a height-to-diameter ratio of 2.26;

[0051] Step 2, the first forging blank obtained in step 1 is returned to the furnace, heated to 1160°C and kept warm for 80 minutes, and then subjected to three upsetting and drawing deformations, and air-cooled to obtain a second forging blank with a size of 265mm×265mm×600mm; the drawing process includes chamfering deformation, the cumulative deformation amount of the single upsetting and drawing deformation is not less than 85%, and the final forging temperature of the three upsetting and drawing deformations is not less than 800°C;

[0052] Step 3, heating the second forging blank obtained in step 2 to 1060°C and keeping it for 160 minutes, and then performing the third forging: performing chamfering and flattening with a reduction of 10% and a reduction rate of 40 mm / s in the height direction, shaping in the axial direction, upsetting with an upsetting ratio of 1.6 in the height direction, and chamfering and stretching with a feed amount of 1.0 and a reduction of 10% in the length direction, and then shaping into a square billet; then performing chamfering and flattening with a reduction of 10% in the height direction, shaping, upsetting with an upsetting ratio of 1.3 in the height direction, and chamfering and stretching with a feed amount of 0.5 and a reduction of 10% in the length direction, and then shaping into a square billet (the third forging blank) with a size of 265 mm×265 mm; the feed amount is the ratio of the feed length of the forging anvil to the height of the forging blank;

[0053] Step 4: The third forging blank obtained in step 3 is subjected to three upsetting deformations after being kept at 890° C. for 160 min, and the cumulative deformation amount of a single upsetting deformation is not less than 85%, so as to obtain a square billet (fourth forging blank) with a size of 265 mm×265 mm;

[0054] Step 5, the fourth forging blank obtained in step 4 is kept at 950° C. for 160 min and then water-cooled;

[0055] Step 6: After the fourth forging blank is water-cooled in step 5, it is kept at 890°C for 160 minutes and then subjected to two upsetting deformations, with the cumulative deformation of a single upsetting being no less than 80%, and a Φ180 mm bar is obtained after shaping.

[0056] The surface and center of the rod obtained in this embodiment were subjected to microstructural analysis. Figure 3 and Figure 4 As shown, the microstructures in different regions of the rod are evenly distributed and are composed of equiaxed α phase and partially transformed β, and the grain sizes of the equiaxed α phase in different regions are uniform.

[0057] Example 2

[0058] The TC4 ingot of this embodiment has a size of Φ500mm×1500mm after peeling and riser cutting, and a height-to-diameter ratio of 3.0. The forging method of the ingot comprises the following steps:

[0059] Step 1, the ingot is heated to 1120°C and kept warm for 450min before the first forging is performed. First, the first upsetting is performed along the height direction at a pressing rate of 30mm / s and a pressing amount of 20%, and then the shaping is performed along the height direction. Then, the second upsetting is performed at a pressing rate of 40mm / s and a pressing amount of 15%. Subsequently, the third upsetting is performed along the height direction at a pressing rate of 30mm / s and a pressing amount of 15%. After elongation, a square billet (first forging billet) with a size of 550mm×550mm and a height-to-diameter ratio of 2.5 is obtained;

[0060] Step 2, the first forging blank obtained in step 1 is returned to the furnace, heated to 1120°C and kept warm for 280 minutes, and then subjected to three upsetting and drawing deformations, and air-cooled to obtain a square billet (second forging blank) with a size of 550 mm×550 mm; the drawing process includes chamfering deformation, the cumulative deformation amount of the single upsetting and drawing deformation is not less than 85%, and the final forging temperature of the three upsetting and drawing deformations is not less than 800°C;

[0061] Step 3, heating the second forging blank obtained in step 2 to 1030° C. and keeping the temperature for 440 min before performing the third forging: performing chamfering and flattening with a reduction of 15% and a reduction rate of 30 mm / s in the height direction, shaping in the axial direction, upsetting with an upsetting ratio of 1.2 in the height direction, and chamfering and stretching with a feed amount of 0.5 and a reduction of 20% in the length direction, and then shaping into a square billet; then performing chamfering and flattening with a reduction of 10% in the height direction, shaping, upsetting with an upsetting ratio of 1.7 in the height direction, and chamfering and stretching with a feed amount of 1.0 and a reduction of 20% in the length direction, and then shaping into a square billet (the third forging blank) with a size of 550 mm×550 mm; the feed amount is the ratio of the feed length of the forging anvil to the height of the forging blank;

[0062] Step 4: The third forging blank obtained in step 3 is kept at 930° C. for 440 min and then subjected to three upsetting deformations, wherein the cumulative deformation amount of a single upsetting deformation is not less than 85%, to obtain a square billet (fourth forging blank) with a size of 550 mm×550 mm;

[0063] Step 5, the fourth forging blank obtained in step 4 is kept at 980° C. for 440 min and then water-cooled;

[0064] Step 6: After water cooling in step 5, the fourth forging blank is kept at 930°C for 440 minutes and then subjected to two upsetting deformations, with the cumulative deformation of a single upsetting being not less than 80%, and a plate with a size of 200mm×600mm×800mm is obtained after shaping.

[0065] The surface and center of the plate obtained in this embodiment were subjected to microstructural analysis. Figure 5 and Figure 6 As shown in the figure, the α grain size on the surface of the plate is elongated, but the overall structure is relatively uniform; the deformation in the center of the plate is more uniform, dynamic recrystallization occurs, and the grain size is small and uniform.

[0066] Example 3

[0067] The TC4 ingot of this embodiment has a size of Φ320mm×1100mm after peeling and cutting the riser, a height-to-diameter ratio of 3.2, and an alloy phase transition point of 980°C. The forging method of the ingot comprises the following steps:

[0068] Step 1, the ingot is heated to 1150°C and kept for 220 minutes before the first forging is performed. First, the first upsetting is performed along the height direction at a pressing rate of 30 mm / s and a pressing amount of 15%. Then, the second upsetting is performed at a pressing rate of 30 mm / s and a pressing amount of 15%. The ingot is shaped along the axial direction to make it straight. Then, the third upsetting is performed along the height direction at a pressing rate of 40 mm / s and a pressing amount of 20%. The first forging billet with a diameter of 420 mm and a height-to-diameter ratio of 1.5 is obtained.

[0069] Step 2, the first forging blank obtained in step 1 is returned to the furnace, heated to 1150°C and kept warm for 120 minutes, and then subjected to two upsetting and drawing deformations, and air-cooled to obtain a second forging blank with a size of 340 mm×340 mm×765 mm; chamfering deformation and drawing are performed during the drawing process, the cumulative deformation amount of the single upsetting and drawing deformation is not less than 85%, and the final forging temperature of the upsetting and drawing deformation is not less than 800°C;

[0070] Step 3, heating the second forging blank obtained in step 2 to 1050° C. and keeping the temperature for 210 min, and then performing the third forging: performing chamfering with a reduction of 15% and a reduction rate of 40 mm / s in the height direction, shaping along the axial direction, upsetting with an upsetting ratio of 1.5 in the height direction, and chamfering with a feed amount of 0.8 and a reduction of 15% in the length direction, and then shaping into a square billet; then performing chamfering with a reduction of 10% in the height direction, shaping, upsetting with an upsetting ratio of 1.3 in the height direction, and chamfering with a feed amount of 0.5 and a reduction of 15% in the length direction, and then shaping into a square billet (the third forging blank) with a size of 340 mm×340 mm;

[0071] Step 4: The third forging blank obtained in step 3 is subjected to three upsetting deformations after being kept at 950° C. for 200 min, and the cumulative deformation amount of a single upsetting deformation is not less than 85%, so as to obtain a square billet (fourth forging blank) with a size of 340 mm×340 mm;

[0072] Step 5, the fourth forging blank obtained in step 4 is kept at 990° C. for 200 min and then water-cooled;

[0073] Step 6: After water cooling in step 5, the fourth forging blank is kept at 950° C. for 270 minutes and then subjected to two upsetting deformations, with the cumulative deformation of a single upsetting being no less than 80%, and a large-size bar of Φ350 mm is obtained after shaping.

[0074] The surface and center of the rod obtained in this embodiment were subjected to microstructural analysis. Figure 7 and Figure 8 As shown, the microstructures in different regions of the rod are evenly distributed and are composed of equiaxed α phase and partially transformed β phase, and the grain sizes of the equiaxed α phase in different regions are relatively uniform.

[0075] The above description is only a preferred embodiment of the present invention and does not limit the present invention in any way. Any simple modification, change and equivalent structural transformation made to the above embodiment based on the technical essence of the present invention still falls within the protection scope of the technical solution of the present invention.

Claims

1. An efficient homogenization forging method for large-size titanium alloy ingots, characterized in that: The forging method comprises the following steps: Step 1, heating an ingot with a height-to-diameter ratio greater than 2.5 to 150° C. to 250° C. above the phase transition point, and then performing a first forging to obtain a first forging blank with a height-to-diameter ratio less than 2.5; the first forging process includes slow pressing and upsetting deformation, and shaping during the slow pressing and upsetting deformation process; Step 2, returning the first forging blank obtained in step 1 to the furnace for heat preservation and then performing a second forging to obtain a second forging blank; Step 3, heating the second forging blank obtained in step 2 to 50°C to 150°C above the phase transformation point and then performing a third forging to obtain a third forging blank; the third forging process is: repeating the processes of chamfering and flattening along the height direction, shaping, upsetting along the height direction, and chamfering and lengthening along the length direction for 2 times; Step 4, the third forging blank obtained in step 3 is kept at 20°C to 40°C below the phase transformation point and then subjected to a fourth forging to obtain a fourth forging blank; Step 5, the fourth forging blank obtained in step 4 is kept at 10°C to 40°C above the phase transformation point and then water-cooled; Step 6: After the fourth forging blank is water-cooled in step 5, it is kept at 20°C to 40°C below the phase transformation point, and then subjected to the fifth forging and shaping to obtain a forging with uniform structure.

2. The high-efficiency homogenization forging method for a large-size titanium alloy ingot according to claim 1, characterized in that: The pressing rate of the slow pressing and upsetting deformation in step 1 is 30 mm / s to 40 mm / s, and the pressing amount is 15% to 30%; the insulation time t1 is calculated by the following formula: t1=η1×D1; Wherein, t1 is the holding time, in min; D1 is the cross-sectional diameter of the ingot in step 1, in mm; η1 is the heating coefficient, in the range of 0.7 to 0.

9.

3. The high-efficiency homogenization forging method for a large-sized titanium alloy ingot according to claim 1, characterized in that: In step 2, the second forging is performed by performing 2 to 3 times of upsetting and drawing deformation, and the drawing process of the upsetting and drawing deformation includes chamfering deformation.

4. The high-efficiency homogenization forging method for a large-sized titanium alloy ingot according to claim 1, characterized in that: In step 3, the pressing amount of the chamfering and flattening along the height direction is 10% to 15%, and the pressing rate is 30 mm / s to 40 mm / s; the upsetting ratio of the upsetting along the height direction is 1.2 to 1.6; the pressing amount of the chamfering and stretching along the length direction is 10% to 20%; the insulation time t2 is calculated by the following formula: t2=η2×D2; Among them, t2 is the insulation time, the unit is min; D2 is the minimum cross-sectional average thickness of the second forging blank in step three, the unit is mm; η2 is the heating coefficient, the value range is 0.6 to 0.

8.

5. The high-efficiency homogenization forging method for a large-sized titanium alloy ingot according to claim 1, characterized in that: In step 4, the fourth forging process includes not less than 2 times of upsetting deformation, and the cumulative deformation of the single upsetting deformation is not less than 85%; the holding time t3 is calculated by the following formula: t3 = η3 × D3; Wherein, t3 is the holding time, in min; D3 is the minimum cross-sectional average thickness of the third forging blank described in step 4, in mm; η3 is the heating coefficient, in the range of 0.6 to 0.

8.

6. The high-efficiency homogenization forging method for a large-sized titanium alloy ingot according to claim 1, characterized in that: The insulation time t4 described in step 5 is calculated by the following formula: t4=η4×D4; Wherein, t4 is the holding time, in min; D4 is the minimum cross-sectional average thickness of the fourth forging blank described in step 5, in mm; η4 is the heating coefficient, in the range of 0.6 to 0.

8.

7. The high-efficiency homogenization forging method for a large-sized titanium alloy ingot according to claim 1, characterized in that: In step 6, the fifth forging process includes upsetting and drawing deformation for no less than 2 times, and the cumulative deformation amount of the single upsetting and drawing deformation is no less than 80%.

8. The high-efficiency homogenization forging method for large-size titanium alloy ingots according to claim 1, characterized in that: The insulation time t5 described in step 6 is calculated by the following formula: t5 = η5 × D5; Wherein, t5 is the holding time, in min; D5 is the minimum cross-sectional average thickness of the fourth forging blank described in step 6, in mm; η5 is the heating coefficient, in the range of 0.6 to 0.8.

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