A high-performance TC4 titanium alloy forging method

Abstract

The application discloses a forging method of high-performance TC4 titanium alloy, which aims at balancing the contradiction between accumulated deformation energy storage and grain growth inhibition in the prior art, and sequentially carries out blank pretreatment, gradient heating, sectional forging, heating water cooling, re-heating upsetting, elongation forming, post-forging water cooling and finishing detection.The core of the method is to obtain a high-energy sub-stable organization through heating water cooling, and then drive sufficient static recrystallization in subsequent secondary forging at a lower temperature.The method effectively solves the problems of coarse grains and uneven structure, can stably obtain a uniform equiaxed fine-grained structure with an average grain size of 5-8 microns, and makes the forgings have high strength, high plasticity and excellent fatigue performance, and the process has strong controllability and is suitable for large-scale production of high-performance components in the fields of aviation, aerospace and medical devices.

Description

Technical Field

[0001] This invention relates to the field of titanium alloy forging technology, and in particular to a forging method for high-performance TC4 titanium alloy. Background Technology

[0002] The mechanical properties of TC4 titanium alloy (Ti-6Al-4V) are closely related to the morphology and size of its microstructure. Ideal high-performance forgings typically require a uniform, fine equiaxed α+β dual-phase microstructure. To obtain such a microstructure, the key lies in thoroughly breaking down the coarse grains in the as-cast state through thermomechanical treatment and inducing a complete recrystallization process.

[0003] In existing technologies, grain refinement of TC4 titanium alloys is generally achieved through multi-pass or multi-heat forging processes in the α+β two-phase region. However, this field faces a long-standing and unresolved technical challenge: how to effectively accumulate sufficient deformation energy to drive adequate recrystallization while avoiding excessive grain growth caused by repeated high-temperature heating or excessively long total process time.

[0004] Specifically, achieving deep grain refinement often requires a large cumulative deformation. In traditional processes, this is typically achieved by increasing the number of forging passes. However, each reheating to a high forging temperature (such as the upper part of the α+β region), especially when the temperature is close to the β phase transformation point, carries the risk of grain growth. Lowering the heating temperature or shortening the holding time to avoid this risk may lead to a decrease in the billet's plasticity, an increase in deformation resistance, and the energy stored in the previous deformation may be dissipated due to recovery, insufficient to drive complete static recrystallization. The final result is a partially recrystallized or recovered mixed microstructure, with unsatisfactory uniformity and refinement. Furthermore, if the post-forging cooling method is inappropriate (such as air cooling), the phase transformation occurring during cooling may form coarse α-lamellae, which can also offset some of the forging refinement effect.

[0005] Therefore, existing technologies have not yet provided a TC4 titanium alloy forging process that can efficiently and synergistically resolve the contradiction between accumulating high energy storage and suppressing grain growth within a single or limited thermal cycle. Developing a method to maximize and stably maintain microstructure refinement within a limited thermal cycle has become a critical technical challenge that urgently needs to be overcome in this field. Summary of the Invention

[0006] To address the shortcomings of existing technologies, this invention aims to provide a forging method for high-performance TC4 titanium alloy, solving the problems existing in the prior art. Specifically, after the initial forging, instead of direct high-temperature reheating, a short-term solution treatment slightly above the β phase transformation point is performed followed by immediate water cooling. This approach achieves high-density crystal defects through rapid phase transformation, providing a driving force for recrystallization far exceeding that accumulated by traditional deformation. Furthermore, the metastable structure formed by water cooling (such as α' martensite) is highly susceptible to recrystallization during subsequent secondary heating and forging at lower temperatures (α+β region). This process transforms the main grain refinement mechanism from relying on multiple high-temperature large deformations to utilizing a single phase transformation energy storage to drive low-temperature recrystallization. This effectively accumulates the recrystallization driving force while significantly reducing the risk of grain growth caused by multiple high-temperature exposures, achieving deep refinement and homogenization of the microstructure within a limited thermal cycle.

[0007] To achieve the above objectives, this invention provides a forging method for high-performance TC4 titanium alloy. The core concept of this method lies in using a systematic, coordinated, and parameterized multi-stage thermomechanical treatment process to sequentially address a series of key issues, including the initial state of the billet, heating uniformity, grain fragmentation efficiency, microstructure stability, and final performance control. This invention specifically designs a process route involving gradient heating, segmented initial forging, high-temperature homogenization water cooling, secondary precision forging, and final forging water cooling. This aims to achieve sufficient fragmentation of coarse grains in the as-cast state, precise induction of dynamic or static recrystallization, and effective suppression of non-ideal phase transformations, ultimately obtaining high-performance forgings with equiaxed fine grains, high uniformity, and low internal stress. The technical solution of this invention is described in detail below with reference to specific steps: S1 billet pretreatment: TC4 titanium alloy ingots conforming to standards are selected as the billet. The surface of the ingots typically contains defects such as oxide scale, microcracks, porosity, and inclusions. If directly heated and forged, these defects will propagate during subsequent deformation, becoming sources of cracks or inductions for uneven microstructure in the forging. Therefore, pretreatment is necessary. Specifically, at least 1-2 mm of the surface layer of the billet is thoroughly removed by machining or grinding until the surface exhibits a uniform metallic luster. Visual inspection and flaw detection ensure the absence of visible cracks, porosity, and inclusions. This step provides a clean and complete billet interface for subsequent uniform heating and plastic deformation.

[0008] S2 gradient heating: This step aims to eliminate the initial temperature gradient within the billet, prevent thermal stress cracking, and prepare a uniform and refined initial microstructure for subsequent forging. Traditional rapid heating or single-rate heating can easily lead to excessive temperature differences between the billet core and surface, generating huge thermal stress and even causing cracking. This invention employs a multi-stage gradient temperature control strategy: a. Low-temperature homogenization stage: The billet is heated to 600-650℃ at a heating rate of 50-70℃ / h, which is below the significant creep temperature of TC4, and held at this temperature for 0.5-1.5 hours, preferably 1 hour. The main purpose of this stage is to homogenize the overall temperature of the billet and partially eliminate residual casting stress.

[0009] b. Medium-temperature pretreatment stage: Continue heating at a rate of 70-90℃ / h to 850-900℃, allowing it to enter the lower part of the α+β two-phase region, and hold at this temperature for 0.5-1 hour. In this temperature range, the α and β phases coexist. Holding at this temperature helps the Al-rich α phase in the β phase to precipitate uniformly, making the two-phase distribution more uniform, and further reducing the temperature difference between different parts of the billet.

[0010] c. Forging Temperature Heating Stage: Finally, heat to the target forging temperature of 940-960℃ at a heating rate of 80-120℃ / h, placing it in the middle of the α+β two-phase region. This temperature is lower than the β phase transformation point of TC4 (approximately 995℃), effectively preventing rapid grain coarsening caused by entering the full β phase region. The holding time is determined according to the billet size to ensure the core reaches the set temperature.

[0011] The entire gradient heating process is precisely executed by a programmable temperature-controlled furnace, providing ideal billets with uniform structure, no large thermal stress, and uncoarsened grains for subsequent forging.

[0012] S3 segmented forging: This step involves the initial forceful crushing of the as-cast structure. The uniformly heated billet is rapidly transferred to forging equipment such as a hydraulic press within 5 minutes to minimize temperature drop.

[0013] S31 Initial Upsetting: First, free forging upsetting is performed, with the deformation strictly controlled between 20% and 35%, preferably 25% and 30%. This deformation is designed to apply sufficient strain energy to effectively break up the original coarse cast grains and columnar crystals, while inducing preliminary dynamic recovery under the combined action of deformation heat and storage temperature.

[0014] S32 Subsequent drawing: Immediately following this, drawing deformation is performed, with the deformation amount controlled at 25%-35%, preferably 30%. The drawing process changes the strain direction, further breaking down the grains and promoting the homogenization of the microstructure.

[0015] Furthermore, throughout the entire segmented forging process, the billet temperature is monitored in real time using an infrared thermometer to ensure it remains above 900℃, placing it within the optimal plastic deformation temperature window of the α+β two-phase region, with fluctuations controlled within ±10℃. This precise temperature control avoids the risk of a sharp increase in deformation resistance and cracking due to excessively low temperatures, and also prevents abnormal grain growth caused by excessively high temperatures or temperature fluctuations.

[0016] S4 heating water cooling: The billet, after its initial deformation, is returned to the furnace and heated to 1030℃±10℃. This temperature is slightly higher than the β-phase transformation point, causing the microstructure to transform into a single β-phase. The billet is held at this temperature for 1.5-2.5 hours, preferably 1.5-2.0 hours. The purpose of this holding is to allow the alloying elements (Al, V) to diffuse fully and uniformly within the β-phase; secondly, the high temperature releases the deformation energy stored during the initial forging, preparing for the phase transformation during subsequent cooling.

[0017] After the heat preservation period, the billet is quickly transferred to a dedicated spray cooling device for forced, uniform, and rapid water cooling. Water is used as the cooling medium, with a temperature of 25-40℃ to avoid overcooling or undercooling. The water flow rate is 1.2-1.8 m / s, and a multi-nozzle, omnidirectional spray is employed to ensure a surface coverage rate of ≥95%. Cooling continues until the overall billet temperature drops below 300℃. This rapid cooling process serves a dual purpose: first, to inhibit the decomposition of the high-temperature β phase into coarse α-lamellae under slow cooling conditions; second, to utilize rapid undercooling to obtain a metastable, fine-grained microstructure dominated by martensitic α' phase. This microstructure features high-density dislocations and a fine phase structure, providing a highly breakable and energy-storing microstructure basis for the subsequent secondary forging. Uniform spraying avoids microstructural inhomogeneity and quenching stress concentration caused by localized cooling rate differences.

[0018] S5 reheating for upsetting: This step aims to perform secondary crushing and recrystallization on the fine but potentially uneven metastable structure formed after quenching.

[0019] S51 Stress Relief and Reheating: The water-cooled billet is placed in a heating furnace and heated to 950-970℃, preferably 960℃, and held for 2.0-3.0 hours, preferably 2.0-2.5 hours. This heating process eliminates some of the quenching stress generated by water cooling and decomposes the metastable α' phase, transforming it into a more stable α+β lamellar structure. At the same time, the billet is restored to a state with good plasticity.

[0020] S52 Second Upsetting: The reheated billet undergoes a second upsetting process, with deformation controlled at 20%-30%. The main objective of this upsetting is to further break down the fine lamellar layers resulting from the quenched structure and to utilize deformation energy to promote static recrystallization. The forging temperature must also be maintained above 900℃. This step significantly improves the equiaxedness and uniformity of the microstructure.

[0021] S6 drawing and forging water cooling: This step is the final stage for obtaining the final product shape and locking in the fine-grained structure. A "light-pressure, multi-pass" drawing process is employed. The deformation amount in each pass is small, controlled within 8%-12%, and the total deformation amount is achieved through multiple passes, reaching 25%-35%. This process facilitates precise control of the final dimensions and shape of the forging, reducing uneven deformation defects such as internal shear bands. The forming temperature is not lower than 880℃ to ensure final forming is completed within the α+β two-phase region.

[0022] After forming, the forging is immediately cooled using a controlled water cooling method with parameters consistent with step S4 until it reaches room temperature. The purpose of this water cooling is to quickly fix the fine, uniform equiaxed α+β microstructure obtained through the final forging, suppress any phase transformations that may lead to microstructure coarsening or performance degradation during the subsequent air cooling process, and at the same time minimize the thermal stress generated during post-forging cooling.

[0023] The forgings, cooled to room temperature, undergo surface finishing to remove forging flash, oxide scale, and minor defects. The surface roughness Ra after finishing should not exceed 6.3 μm. Finally, the forgings are subjected to comprehensive non-destructive testing and sampling inspections of metallographic and mechanical properties to ensure that their microstructure is uniform equiaxed fine grains and that their mechanical properties meet high-end application standards.

[0024] The purpose of this invention is to provide a forging method for high-performance TC4 titanium alloy, which has the following beneficial effects: First, it overcomes the traditional contradiction between microstructure refinement and grain growth. The heating and water cooling step transforms the driving force for recrystallization from the traditional accumulation of multiple high-temperature deformations to a single, highly efficient solid-state phase change energy storage. This allows the subsequent critical recrystallization process to be powerfully driven to complete at a lower temperature (α+β region) and in a shorter time, thereby achieving a deep and uniform grain refinement effect that is difficult to achieve with traditional processes, while significantly reducing the number of high-temperature exposures and the total duration.

[0025] Secondly, it further spurred a synergistic leap in comprehensive mechanical properties. Thanks to the aforementioned uniform ultrafine equiaxed grain structure, the material's strength and plasticity were simultaneously and significantly improved. Not only did the tensile strength and yield strength reach high levels, but more importantly, the material's plasticity indicators (such as reduction of area) and dynamic load-bearing capacity (such as fatigue limit) were significantly improved, solving the problem that high-strength titanium alloys are often accompanied by insufficient plasticity or fatigue performance, and achieving an optimized match of performance.

[0026] Finally, through process design, this technology effectively controls the total number of heat treatments and production cycle while ensuring the achievement of desired microstructure properties, thereby improving production efficiency and reducing energy consumption. This solution does not rely on special or expensive equipment and can be implemented on conventional heat treatment production lines, demonstrating good technical versatility and significant engineering application value. Detailed Implementation

[0027] The technical solutions in the embodiments of the present invention will be clearly and completely described below. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. All other embodiments obtained by those skilled in the art based on the embodiments of the present invention without creative effort are within the scope of protection of the present invention.

[0028] Example 1: Forging of a compressor disc for an aero-engine S1 billet pretreatment: A TC4 titanium alloy ingot with a diameter of Φ300mm and a height of 400mm was selected. The outer diameter and upper and lower end faces of the ingot were machined using a CNC lathe, with a removal margin of 2mm on each side, thoroughly removing surface oxide scale, cracks, and decarburized layers. Fluorescent penetrant testing (PT) confirmed that the surface was free of defects.

[0029] S2 gradient heating: Load the billet into a chamber resistance heating furnace and control the temperature according to the following program: Phase 1: Increase the temperature from room temperature to 620℃ at a rate of 60℃ / h and hold for 1 hour.

[0030] Second stage: Increase the temperature from 620℃ to 880℃ at a rate of 80℃ / h (deep into the α+β two-phase region) and hold for 0.5 hours.

[0031] The third stage involves heating from 880℃ to 950℃ (below the β phase transformation point) at a rate of 90℃ / h, and holding the temperature for 2 hours according to the billet size to ensure uniform core surface temperature.

[0032] S3 Segment Forging: After the heat treatment is completed, the billet is transferred to an 8000-ton hydraulic press within 3 minutes. First, upsetting is performed, reducing the height from 400mm to 300mm, a deformation of 25%. Immediately afterwards, drawing is performed, using a flat anvil to forge the diameter to approximately Φ350mm, a deformation of approximately 30%. During the forging process, a dual-color infrared thermometer is used for real-time monitoring, and the billet surface temperature is consistently controlled at 940±8℃.

[0033] S4 Heating and Water Cooling: The forged billet is placed back into the heating furnace and heated to 1035℃, held for 1.8 hours. It is then quickly transferred to a ring-shaped spray cooling device. The cooling water temperature is controlled at 30±2℃, and a high-pressure pump and evenly distributed nozzles are used to maintain a stable water flow rate of 1.5 m / s, ensuring the billet is completely covered by water. Spraying continues until the overall billet temperature drops to approximately 250℃.

[0034] S5 Reheat Upsetting: The water-cooled billet is heated to 960℃ and held for 2.2 hours. Then, a second upsetting is performed to compress the billet height from the current size again, with a deformation of about 22%, and a forging temperature of about 920℃.

[0035] S6 Drawing and Forging Water Cooling: The billet is drawn using an anvil to form the prototype of the disc. Then, a "light pressure multi-pass" method is used, with each pass reducing the workpiece by approximately 10%, for a total of 10 passes, resulting in a total deformation of approximately 32% and a final forging temperature of approximately 890℃. After forming, the workpiece is immediately water-cooled using a spray system with the same parameters as in step S4 until the workpiece temperature is below 50℃.

[0036] After cooling, the disc forging blank is turned to remove surface oxide scale and a small amount of flash, achieving a surface roughness Ra of 4.1 μm. Samples are then taken for testing. Example 2: Orthopedic implant rod material for medical devices S1 billet pretreatment: TC4 cast rods with a diameter of 80mm and a length of 200mm are selected. The outer cylindrical layer is removed by centerless grinding, and fluorescent penetrant testing (PT) is performed to ensure that the surface is smooth and free of defects.

[0037] S2 gradient heating: The pretreated billet is placed in a box-type resistance furnace to prevent excessive oxidation. The following gradient heating regime is executed using multi-point thermocouples and a programmable controller: First stage: Heat from room temperature to 600℃ at a precise rate of 55℃ / h. After reaching the target temperature, maintain at 600±5℃ for 1.2 hours.

[0038] Second stage: Continue heating from 600℃ to 860℃ at a rate of 75℃ / h (deepening into the α+β two-phase region). Hold at 860±5℃ for 0.8 hours.

[0039] The third stage involves final heating at a rate of 85℃ / h to the target forging temperature of 940℃ (still in the middle of the α+β two-phase region, below the β phase transformation point). The stock is then held at 940±5℃ for 1 hour to ensure the temperature difference between the core and surface of the bar stock is less than 15℃.

[0040] S3 Segment Forging: After the holding period, the billet is rapidly transferred from the furnace to the worktable of a 2000-ton precision high-speed forging hydraulic press within 30 seconds to minimize temperature drop. Axial upsetting of the billet is performed using a flat anvil. The billet is compressed from an initial height of 200mm to 150mm, with an actual deformation of 25%. This operation begins at an initial temperature of approximately 935°C and ends at approximately 925°C.

[0041] The upsetting process involves drawing the disc-shaped billet. A flat anvil is used for multi-directional radial drawing, aiming to restore and slightly increase the length while further breaking down the microstructure. The final forging produces a regular billet with a diameter of approximately Φ85mm and a length of approximately 200mm. The reduction in area (deformation) for this process is approximately 33%. The forging temperature is maintained within a window of 915±5℃ throughout the process.

[0042] S4 Heating and Water Cooling: The forged billet is placed back into the heating furnace and heated to 1025℃ at a heating rate of 120℃ / h. Once reached, it is held at 1025±5℃ for 1.6 hours. After holding, a robotic arm transfers the billet within 15 seconds and immerses it in a specially designed high-power circulating water quenching tank. The water temperature is strictly maintained at 25±2℃ through a cooling system and heating rods. Multiple high-power agitators are arranged inside the tank to create turbulence around the billet, simulating a uniform high-speed water flow impact of approximately 1.3 m / s, ensuring uniform cooling.

[0043] During this process, the billet is completely submerged and continuously agitated until its overall temperature drops below 200°C, at which point it is removed. The entire quenching process takes approximately 90 seconds. This rapid cooling yields a metastable microstructure dominated by the α' phase of fine lath martensite.

[0044] S5 Reheat Upsetting: The quenched billet is placed in a heating furnace for reheating. The temperature is increased to 955℃ at a rate of 80℃ / h and held at 955±5℃ for 2.5 hours. This process decomposes the metastable α' phase into fine α+β lamellar structures and eliminates most of the quenching stress. After exiting the furnace, a second upsetting is performed at approximately 945℃. The billet height is compressed by approximately 18% from the quenched dimensions (the specific dimensions may be slightly adjusted based on previous steps). Forging ends at approximately 905℃. This step aims to break up the lamellar structures formed during quenching and initiate the recrystallization process.

[0045] S6 drawing and post-forging water cooling: An arc-shaped anvil matching the target bar size is used. A "light pressure, multi-pass" strategy is employed for drawing: the reduction in each pass is strictly controlled between 9% and 11% of the initial height of that pass, with a total of approximately 12 forging passes. The total deformation is approximately 30%. By controlling the forging rhythm and utilizing the deformation heat, the final forging temperature is maintained at 900±10℃.

[0046] Once the bar is formed to a diameter of 25mm, it is immediately immersed in a 25°C high-pressure circulating water quenching tank with the same parameters as in step S4 for rapid and uniform cooling until the overall temperature of the bar drops to room temperature.

[0047] Comparative Example 1: The same billet specifications as in Example 1 were used. After pretreatment, the billet was directly heated to 950°C at a rapid heating rate of 150°C / h, held at that temperature for 2 hours, and then forged. The forging and subsequent cooling steps were the same as in Example 1.

[0048] Comparative Example 2 uses conventional forging with air cooling: the same billet and gradient heating process as Example 2 are employed. The forging process is also the same, but the heating and water cooling in step S4 and the reheating and upsetting in step S5 are omitted. After the initial segmented forging in step S3, the elongation forming in step S6 is performed directly, and air cooling is used instead of water cooling after forging.

[0049] Comparative Example 3: The rest is the same as Example 1, except that it is forged only once, and the water cooling after forging is replaced by air cooling.

[0050] The finished products from the above embodiments and comparative examples were tested, and the test results are detailed in Table 1 below: Table 1 Performance indicators Example 1 Example 2 Comparative Example 1 Comparative Example 2 Comparative Example 3 Average grain size (μm) 8.2 5.5 17.5 (Core) 18.3 Streamlined structure, non-isoaxial Tensile strength Rm (MPa) 958 978 918 (Core) 892 942 (vertical) 878 (horizontal) Yield strength Rp0.2 (MPa) 888 908 848 (core) 832 872 (vertical) 798 (horizontal) Elongation A (%) 15.2 17.1 11.3 (Core) 12.4 15.5 (vertical) 8.2 (horizontal) Reduction of area Z (%) 42.5 50.3 32.8 (Core) 37.6 43.0 (vertical) 22.5 (horizontal) Conclusion: As shown in Table 1, the test data of the embodiments and comparative examples show that the TC4 titanium alloy forgings prepared by the forging method provided by the present invention have a uniform and fine equiaxed crystal microstructure, and therefore exhibit comprehensive and excellent mechanical properties, specifically high tensile strength (≥958 MPa), high yield strength (≥888 MPa) and excellent plasticity (elongation ≥15.2%, reduction of area ≥42.5%), and good isotropic properties.

[0051] The above comparison fully demonstrates that the present invention systematically solves the problems of large grain size, uneven structure and large performance fluctuation through a synergistic process of gradient heating, heating and water cooling + secondary upsetting, and precise temperature control throughout the process, and achieves technical effects that are significantly better than traditional processes.

[0052] Although embodiments of the invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made to these embodiments without departing from the principles and spirit of the invention, the scope of which is defined by the appended claims and their equivalents.

Claims

1. A forging method for high-performance TC4 titanium alloy, characterized in that, Includes the following steps: S1 billet pretreatment: Select TC4 titanium alloy ingot billet with Ti-6Al-4V composition and remove surface defects; S2 gradient heating: The billet is placed in a heating furnace and heated to the forging temperature using a staged gradient heating method; S3 segmented forging: The heated billet undergoes initial upsetting and drawing forging; S4 Heating and Water Cooling: After heating the forged billet to 1030℃±10℃ and holding it at that temperature, it is rapidly cooled by water cooling. S5 Reheat Upsetting: The water-cooled billet is heated and then upset a second time; S6 drawing and water cooling after forging: The billet after secondary upsetting is drawn and then immediately water-cooled to room temperature.

2. The forging method of a high-performance TC4 titanium alloy according to claim 1, characterized in that: The specific process of gradient heating in step S2 is as follows: first, the temperature is raised to 600-650℃ at a rate of 50-70℃ / h and held for 0.5-1.5 hours; then, the temperature is raised to 850-900℃ at a rate of 70-90℃ / h and held for 0.5-1 hour; finally, the temperature is raised to 940-960℃ at a rate of 80-120℃ / h and held for a sufficient period before being removed from the furnace.

3. The forging method of a high-performance TC4 titanium alloy according to claim 1, characterized in that: In step S3, the deformation amount of the first upsetting is controlled at 20%-35%, the deformation amount of the elongation is controlled at 25%-35%, and the temperature fluctuation is controlled within ±10℃ by real-time monitoring with an infrared thermometer during the forging process.

4. The forging method of a high-performance TC4 titanium alloy according to claim 1, characterized in that: In step S4, the heat preservation time is 1.5-2.5 hours; the water cooling adopts a uniform spraying method, the cooling medium is water with a temperature of 25-40℃ and a flow rate of 1.2-1.8 m / s, the spraying coverage is ≥95%, and the cooling termination temperature is below 300℃.

5. The forging method for a high-performance TC4 titanium alloy according to claim 1, characterized in that: In step S5, the secondary heating temperature is 950-970℃, and the holding time is 2.0-3.0 hours; the deformation of the secondary upsetting is controlled at 20%-30%, and the forging temperature is maintained above 900℃.

6. The forging method of a high-performance TC4 titanium alloy according to claim 1, characterized in that: In step S6, the elongation forming adopts a light pressure multi-pass process, with each pass having a deformation amount of 8%-12%, the total deformation amount controlled at 25%-35%, and the forming temperature not lower than 880℃.

7. A forging method for a high-performance TC4 titanium alloy according to claim 1 or 4, characterized in that: The cooling medium parameters in the post-forging water cooling in step S6 are the same as those in the heating water cooling in step S5.

8. The forging method of high-performance TC4 titanium alloy according to claim 1, characterized in that: In step S1, surface defects are removed by machining or grinding to ensure that the surface of the billet is free of cracks, pores and inclusions.