A high strength and toughness heat treatment method and system for Ti-Al-Mo titanium alloy forgings

Abstract

The application discloses a high-strength and high-toughness heat treatment method and system for Ti-Al-Mo titanium alloy forgings, relates to the technical field of metal material heat treatment, and aims to solve the technical problem that the prior art cannot obtain stable, uniform and high-strength and high-toughness microstructure of Ti-Al-Mo alloy; the high-strength and high-toughness heat treatment method for the Ti-Al-Mo titanium alloy forgings comprises the following steps: obtaining a Ti-Al-Mo forging blank; heating the forging blank at a rate of 5-15 DEG C / min, and decreasing the single temperature rise by 100-50 DEG C in the heating process; after reaching the target temperature each time, the forging blank is kept for 2-6 minutes; the forging blank is heated to 800-900 DEG C and kept for 2-4 hours, and then air-cooled; the forging blank is heated at a rate of 2-10 DEG C / min, and the single temperature rise is decreased by 115-75 DEG C in the heating process; after reaching the target temperature each time, the forging blank is kept for 2-4 minutes; the forging blank is heated to 550-700 DEG C and kept for 2-18 hours, and then air-cooled.

Description

Technical Field

[0001] This invention relates to the field of heat treatment technology for metallic materials, and more specifically, to a high-strength and toughening heat treatment method and system for Ti-Al-Mo titanium alloy forgings. Background Technology

[0002] Ti-Al-Mo alloys are a novel type of α- and β-phase titanium alloys. Due to their potential combination of high strength and high toughness, they have broad application prospects in high-end load-bearing structural components such as aerospace and shipbuilding. As equipment design develops towards higher thrust-to-weight ratios, higher reliability, and longer service life, the requirements for material microstructure uniformity, mechanical properties, and processing adaptability are increasing.

[0003] Large-sized forgings, due to their thick cross-sections, large volumes, and the uneven temperature, strain distribution, and residual stress accumulation during hot working and cooling, suffer from problems affecting the uniformity of the material's microstructure, the stability of its mechanical properties, and the machining accuracy of the components. Existing solution-aging heat treatment processes for titanium alloys are designed based on their specific compositions and phase transformation characteristics. When these existing heat treatment processes are directly applied to novel Ti-Al-Mo alloys with different compositions and phase transformation behaviors, it is difficult to obtain a stable, uniform microstructure with a good balance of strength and toughness, thus failing to meet the requirements for precise performance control in load-bearing components. Summary of the Invention

[0004] The purpose of this invention is to provide a high-strength and toughening heat treatment method and system for Ti-Al-Mo titanium alloy forgings, to solve the technical problem that existing technologies cannot obtain a stable, uniform microstructure with a balance of strength and toughness in Ti-Al-Mo alloys. Therefore, this invention achieves this through the following solution.

[0005] In a first aspect, the present invention provides a high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, comprising: Obtain Ti-Al-Mo titanium alloy forgings; The forging billet is heated at a rate of 5~15℃ / min, with the temperature rise decreasing from 100~50℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~6 minutes until the forging billet is heated to 800~900℃ and held for 2~4 hours, then air-cooled to room temperature. The forging billet is heated at a rate of 2~10℃ / min, with the temperature rise decreasing from 115~75℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~4 minutes until the forging billet is heated to 550~700℃ and held for 2~18 hours, then air-cooled to room temperature.

[0006] Compared with the prior art, the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention controls the temperature range of each holding treatment and controls the heating rate to achieve the target temperature of a single temperature rise before holding. After the holding treatment, an ideal basketweave structure with fine and uniform lamellar distribution can be obtained. The volume fraction of the primary α phase is strictly controlled at 65.9%~77.9%, and the average width of the α lamellars is 1.04μm~2.8μm. This achieves the best balance between the strength and toughness of the Ti-Al-Mo alloy, significantly improves the impact toughness of the alloy, and maintains high strength (tensile strength ≥1025MPa, yield strength ≥966MPa) and good plasticity. Specifically, in the first heat treatment, by heating the forging billet at a rate of 5~15℃ / min, with each temperature rise decreasing from 100~50℃ during the heating process, and holding for 2~6 minutes after each target temperature is reached, a slightly spheroidized primary α phase and a fine-sized, uniformly distributed β phase at the α grain boundaries can be obtained. Heating the forging billet to 800~900℃ and holding for 2~4 hours further spheroidizes and equiaxes the primary α phase, while the coarsening of the β phase is suppressed, resulting in a finer β phase. After the first heat treatment, a large amount of lamellar "α+β" structures dominated by fine lamellar α phase and residual β phase, and a small amount of equiaxed primary α phase are obtained. Further, in the second heat treatment… In the heat treatment, the forging billet is heated at a rate of 2~10℃ / min, with the temperature rise decreasing from 115~75℃ in a single step. After reaching the target temperature each time, it is held for 2~4 minutes, resulting in a more uniform composition of the lamellar structure. The forging billet is heated to 550~700℃ and held for 2~18 hours, causing finer α particles to precipitate from the β phase between the α lamellars in the forging billet, making the lamellar structure clearer. After the second heat treatment, a microstructure with interwoven lamellar α phases arranged in a basket-net pattern is obtained. Through the above technical solution of the present invention, the technical problem that the prior art cannot obtain a stable, uniform microstructure with a good balance of strength and toughness in Ti-Al-Mo alloys is solved.

[0007] Furthermore, in the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention, after obtaining the Ti-Al-Mo titanium alloy forging billet, the method further includes: The forging blank is surface treated to remove oil, rust and forging residue oxide layer from its surface.

[0008] Furthermore, in the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention, after two heat treatments, the Ti-Al-Mo titanium alloy forms a basketweave structure with a primary α phase volume fraction of 65.9~77.9% and an average lamellar α width of 1.04μm~2.8μm; after heat treatment, the Ti-Al-Mo titanium alloy has a room temperature tensile strength greater than or equal to 1025MPa, a yield strength greater than or equal to 966MPa, an elongation greater than or equal to 15.5%, a reduction of area greater than or equal to 25%, and an impact absorption energy greater than or equal to 56J.

[0009] Secondly, the present invention provides a high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings, comprising the following methods: The data acquisition module is used to acquire temperature and stress change data at different locations of the forging billet during the heat treatment process, and obtain multi-dimensional and multi-physical quantity synchronous monitoring data through sensors; The real-time feedback module includes a database submodule, an online analysis submodule, a prediction submodule, and a feedback control submodule. The database submodule manages historical and simulation data of the heat treatment process, forming a process knowledge base. The historical and simulation data include the microstructure evolution of materials under different temperature conditions and their corresponding mechanical property indicators. The online analysis and prediction submodules are used to predict the current material microstructure and key performance indicators through simulation models and real-time temperature data, and to complete the analysis of input process parameters and the invocation of corresponding calculation models. The feedback control submodule is used to dynamically adjust key parameters in the heat treatment equipment based on the real-time prediction results. These key parameters include heating power, holding time, and cooling rate.

[0010] Furthermore, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, preset process data is imported into the database submodule; the preset process data includes the temperature threshold, time interval, cooling method, microstructure characteristics and performance indicators of the heat treatment; After the heat treatment process is started, the data acquisition module continuously captures dynamic data during the process, including the current real-time temperature and strain parameters. The acquired data is transmitted in real time to the real-time feedback module to provide dynamic input for subsequent analysis.

[0011] Furthermore, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, the data acquired by the data acquisition module is preferentially compared and analyzed with the data in the database sub-module; the data resources stored in the database sub-module include initially imported process benchmark data, historical process / result data of similar processes, microstructure, properties, and process parameter information. If there is no correlation after comparison, the data continues to be transmitted to the online analysis sub-module and the prediction sub-module.

[0012] Furthermore, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, the data transmission to the online analysis submodule and the prediction submodule includes: After the data is transmitted to the online analysis submodule and the prediction submodule, online simulation is performed to obtain analysis and prediction results. These results are then used to further supplement the database submodule to enrich the data pool. The online analysis submodule dynamically analyzes the microstructure and performance development status under the current process, and predicts the evolution direction of microstructure and performance in subsequent processes through online simulation by the prediction submodule, forming a judgment result on whether it meets expectations.

[0013] Furthermore, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, the step of determining whether the formation meets the expected results includes: When the assessment results indicate that the organizational morphology / performance is developing in accordance with the expected goals, the process continues to be executed under the current conditions. At the same time, the data acquisition module continues to collect data to maintain the closed loop of the process. If the assessment results indicate that the organizational structure / performance is not developing in accordance with the expected goals, the feedback control submodule will be triggered.

[0014] Furthermore, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, after the trigger feedback control submodule, it includes: The feedback control submodule generates targeted process adjustment parameters based on the associated data in the database submodule and the deviation information obtained from the online analysis submodule, and feeds the process adjustment parameters back to the actual heat treatment process to complete the dynamic correction of process conditions. The process adjustment parameters include temperature adjustment range, time increment / decrement duration, and cooling method. Attached Figure Description

[0015] The accompanying drawings, which are included to provide a further understanding of the invention and form part of this invention, illustrate exemplary embodiments of the invention and are used to explain the invention, but do not constitute an undue limitation of the invention. In the drawings: Figure 1This is a schematic diagram of the EBSD results of the Ti-Al-Mo titanium alloy after heat treatment in Example 1 of the present invention; in: Figure 1 (a) is the phase distribution diagram at a low magnification of 50 micrometers; Figure 1 (b) is the inverse pole figure at a low magnification of 50 micrometers; Figure 1 (c) is the phase distribution diagram at a magnification of 20 micrometers; Figure 1 (d) is the inverse pole figure at a magnification of 20 micrometers; Figure 2 This is a schematic diagram of the dimensions of the impact specimen in Embodiment 1 of the present invention; Figure 3 This is a schematic diagram of the dimensions of the tensile specimen in Embodiment 1 of the present invention; Figure 4 The image shows a SEM image of the impact fracture surface of a Ti-Al-Mo titanium alloy after heat treatment according to Example 1 of this invention; wherein: Figure 4 (a) shows the impact fracture morphology at a low magnification of 50 micrometers; Figure 4 (b) is Figure 4 (a) A magnified view of the central region at 10 micrometers magnification; Figure 5 The image shows a SEM photograph of the tensile fracture surface of a Ti-Al-Mo titanium alloy after heat treatment according to Example 1 of this invention; wherein: Figure 5 (a) shows the impact fracture morphology at a low magnification of 50 micrometers; Figure 5 (b) is Figure 5 (a) A magnified view of the central region at 10 micrometers magnification; Figure 6 This is a schematic diagram of the principle of a high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to the present invention. Figure 7 This is a schematic diagram of the connection of the high-strength and toughening heat treatment system for the Ti-Al-Mo titanium alloy forgings of the present invention. Figure 8 This is a schematic diagram showing the real-time comparison of online simulation and target performance in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention.

[0016] Figure label: 1. Forging billet; 2. Heating furnace; 3. Thermocouple; 4. Data acquisition module; 5. Real-time feedback module. Detailed Implementation

[0017] To make the technical problems to be solved, the technical solutions, and the beneficial effects of the present invention clearer, the present invention will be further described in detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the present invention and are not intended to limit the present invention.

[0018] It should be noted that when a component is referred to as being "fixed to" or "set on" another component, it can be directly on or indirectly on that other component. When a component is referred to as being "connected to" another component, it can be directly connected to or indirectly connected to that other component.

[0019] Furthermore, the terms "first" and "second" are used for descriptive purposes only and should not be construed as indicating or implying relative importance or implicitly specifying the number of indicated technical features. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of this invention, "a plurality of" means two or more, unless otherwise explicitly specified. "Several" means one or more, unless otherwise explicitly specified.

[0020] Large-sized forgings, due to their thick cross-sections, large volumes, and the uneven temperature, strain distribution, and residual stress accumulation during hot working and cooling, suffer from problems affecting the uniformity of the material's microstructure, the stability of its mechanical properties, and the machining accuracy of the components. Existing solution-aging heat treatment processes for titanium alloys are designed based on their specific compositions and phase transformation characteristics. When these existing heat treatment processes are directly applied to novel Ti-Al-Mo alloys with different compositions and phase transformation behaviors, it is difficult to obtain a stable, uniform microstructure with a good balance of strength and toughness, thus failing to meet the requirements for precise performance control in load-bearing components.

[0021] To address the above technical problems, in a first aspect, the present invention provides a high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, comprising: Obtain Ti-Al-Mo titanium alloy forgings; The forging billet is heated at a rate of 5~15℃ / min, with the temperature rise decreasing from 100~50℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~6 minutes until the forging billet is heated to 800~900℃ and held for 2~4 hours, then air-cooled to room temperature. The forging billet is heated at a rate of 2~10℃ / min, with the temperature rise decreasing from 115~75℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~4 minutes until the forging billet is heated to 550~700℃ and held for 2~18 hours, then air-cooled to room temperature.

[0022] When using this technical solution, the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention controls the temperature range of each holding treatment and controls the heating rate to achieve the target temperature of a single temperature rise before holding. After the holding treatment, an ideal basketweave structure with fine and uniform lamellar distribution can be obtained. The volume fraction of the primary α phase is strictly controlled at 65.9%~77.9%, and the average width of the α lamellars is 1.04μm~2.8μm. This achieves the best balance between the strength and toughness of the Ti-Al-Mo alloy, significantly improves the impact toughness of the alloy, and maintains high strength (tensile strength ≥1025MPa, yield strength ≥966MPa) and good plasticity. Specifically, in the first heat treatment, the forging billet is heated at a rate of 5-15℃ / min, with the temperature rise decreasing from 100-50℃ per increment during the heating process. After each time the target temperature is reached, it is held for 2-6 minutes. This process yields a slightly spheroidized primary α phase and a fine-sized, uniformly distributed β phase at the α grain boundaries. Heating the forging billet to 800-900℃ and holding it for 2-4 hours further spheroidizes and equiaxes the primary α phase, while the coarsening of the β phase is suppressed, resulting in a finer β phase. After the first heat treatment, a large amount of lamellar "α+β" structures dominated by fine lamellar α phase and residual β phase, along with a small amount of other phases, are obtained. The initial α phase is formed on the axial side; further, in the second heat treatment, the forging billet is heated at a rate of 2~10℃ / min, and the temperature rise during the heating process decreases from 115~75℃ in a single step. After reaching the target temperature each time, it is held for 2~4 minutes, and the composition of the lamellar structure is more uniform. The forging billet is heated to 550~700℃ and held for 2~18 hours. The β phase between the α lamellars in the forging billet precipitates finer α particles, making the lamellar structure clearer. After the second heat treatment, a structure in which the dominant lamellar α phase is interwoven and arranged in a basket-net pattern is obtained. For example, the above titanium alloy forging billet can be a square billet with specifications of 250 mm × 250 mm × 250 mm, 250 mm × 160 mm × 160 mm or 250 mm × 160 mm × 90 mm. The titanium alloy is Ti62F alloy in the Ti-Al-Mo system.

[0023] The technical solution of the present invention solves the technical problem that the prior art cannot obtain a stable, uniform microstructure with a good balance of strength and toughness in Ti-Al-Mo alloys.

[0024] As one possible implementation, during the first holding period, the heating rate can be 5°C / min, 10°C / min, or 15°C / min, and the single temperature rise during the heating process can be 100°C, 70°C, or 50°C. After reaching the target temperature, the holding time can be 2 minutes, 4 minutes, or 6 minutes, and the final holding temperature can be 800°C, 850°C, or 900°C, with a holding time of 2 hours, 3 hours, or 4 hours. For example, during the first holding period, the heating rate is 5°C / min, and during the heating process, the temperature is held for 2 minutes for every 100°C increase until the forging billet temperature reaches 800~900°C, and then held for 2~4 hours. In this case, the temperature field of the entire forging billet is extremely uniform and almost no thermal stress is generated, resulting in finer and more uniform β grains. As another example, during the first holding period, the heating rate is 10°C / min, and during the heating process, the temperature rise is held for 2 minutes for every 100°C increase until the forging billet temperature reaches 800~900°C, and then held for 2~4 hours. The forging billet is held at 70°C for 4 minutes until it reaches 800-900°C, then held for 2-4 hours. This method shortens the total heating time while still ensuring good microstructure uniformity, allowing the primary α-phase to be uniformly embedded in the homogeneous β-matrix. Alternatively, during the first holding period, the temperature is increased at a rate of 15°C / minute. For forging billets below 500°C, a single temperature increase is 100°C, followed by a 2-minute holding at the target temperature. For forging billets above 500°C, a single temperature increase is 50°C, followed by a 6-minute holding at the target temperature, until the forging billet reaches 800-900°C, then held for 2-4 hours. The core objective in this method is to achieve temperature homogenization below 500°C, and to control the uniformity of phase transformation and the homogeneity of the β-phase composition above 500°C, avoiding rapid local dissolution of the α-phase and drastic fluctuations in the β-phase composition caused by excessive temperature jumps.

[0025] As one possible implementation, during the first heat preservation process, the heating rate can be 2℃ / min, 6℃ / min, or 10℃ / min, and the single temperature rise during the heating process can decrease from 115℃, 95℃, or 75℃. After each time the target temperature is reached, the heat preservation time is 2 minutes, 3 minutes, or 4 minutes. The final heat preservation temperature can be 550℃, 650℃, or 700℃, and the heat preservation time can be 2 hours, 10 hours, or 18 hours. For example, during the second heat preservation process, the heating rate is 2℃ / min, and during the heating process, the temperature is held for 2 minutes for every 115℃ increase until the temperature of the forging billet reaches 550~700℃, and then held for 2~18 hours. In this case, the temperature of the entire forging billet core and surface is uniform and there is no significant temperature gradient change. As another example, during the second heat preservation process, the heating rate is 6℃ / min, and during the heating process, the temperature is held for 2 minutes for every 115℃ increase until the temperature of the forging billet reaches 550~700℃, and then held for 2~18 hours. The forging billet is held at 95°C for 3 minutes until it reaches 550-700°C, then held for 2-18 hours. This method avoids prolonged exposure to low-temperature regions that are not conducive to phase transformation and promotes compositional uniformity. In another example, during the second holding period, the temperature is increased at a rate of 10°C / minute. For forging billets below 300°C, the single temperature rise is 115°C, followed by a 2-minute holding period after reaching the target temperature. For forging billets above 300°C, the single temperature rise is 75°C, followed by a 4-minute holding period after reaching the target temperature, until the forging billet reaches 550-700°C, then held for 2-18 hours. This method ensures that all β-metastable phases within the low-temperature to high-temperature range can decompose within their optimal temperature window, preventing insufficient decomposition of some phases due to excessively rapid heating. This results in secondary α-precipitates with extremely narrow size distribution and high dispersion.

[0026] As one possible implementation, the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention further includes, after obtaining the Ti-Al-Mo titanium alloy forging billet, performing surface treatment on the forging billet to remove oil, rust, and forging residue oxide layer from its surface. Using this technical solution avoids the penetration of elements such as carbon and sulfur from the oil into the alloy surface at high temperatures, preventing localized compositional deviations, while ensuring surface cleanliness.

[0027] In one possible implementation, the high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings of the present invention, after two heat treatments, forms a basketweave structure in the Ti-Al-Mo titanium alloy with a primary α phase volume fraction of 65.9% to 77.9% and an average lamellar α width of 1.04 μm to 2.8 μm. After heat treatment, the Ti-Al-Mo titanium alloy has a room temperature tensile strength greater than or equal to 1025 MPa, a yield strength greater than or equal to 966 MPa, an elongation greater than or equal to 15.5%, a reduction of area greater than or equal to 25%, and an impact absorption energy greater than or equal to 56 J. For example, the volume fraction of the primary α phase in the basketweave structure can be 65.9%, 75%, or 77.9%, and the average lamellar α width can be 1.04 μm, 2.5 μm, or 2.8 μm.

[0028] Secondly, the present invention provides a high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings, comprising: The data acquisition module is used to acquire temperature and stress change data at different locations of the forging billet during the heat treatment process, and obtain multi-dimensional and multi-physical quantity synchronous monitoring data through sensors; The real-time feedback module includes a database submodule, an online analysis submodule, a prediction submodule, and a feedback control submodule. The database submodule manages historical and simulation data of the heat treatment process, forming a process knowledge base. The historical and simulation data include the microstructure evolution of materials under different temperature conditions and their corresponding mechanical property indicators. The online analysis and prediction submodules are used to predict the current material microstructure and key performance indicators through simulation models and real-time temperature data, and to complete the analysis of input process parameters and the invocation of corresponding calculation models. The feedback control submodule is used to dynamically adjust key parameters in the heat treatment equipment based on the real-time prediction results. These key parameters include heating power, holding time, and cooling rate.

[0029] In the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, temperature and stress data at different locations of the forging billet are acquired by sensors. This allows for real-time monitoring of the thermal gradient and stress distribution of the workpiece during heat treatment, providing a data foundation for overcoming the uneven heating problem caused by workpiece size and shape in traditional heat treatment. The system can dynamically adjust key parameters such as heating power, holding time, and cooling rate based on real-time predicted microstructure and performance conditions. This effectively suppresses local overheating / overcooling, reduces residual stress and deformation, and ensures that the entire forging achieves a uniform and stable microstructure and mechanical properties, significantly improving the yield of batches of products. Consistency and reliability: The above technical solution utilizes a process knowledge base that integrates historical and simulation data. Through the online analysis submodule, it calls the model to correlate real-time temperature data with the microstructure evolution laws such as material phase transformation and grain growth, and predicts the current material microstructure state (such as α / β phase ratio, grain size, etc.) in real time. The feedback control submodule actively adjusts the process parameters based on the deviation between the predicted performance indicators (such as strength and toughness) and the target values, so that the heat treatment process can be precisely guided to obtain a microstructure that is conducive to obtaining the ideal "strength-toughness" combination. This overcomes the limitations of the traditional "trial and error method" or fixed process, thereby maximizing the material potential of Ti-Al-Mo alloys.

[0030] As one possible implementation, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, preset process data is imported into the database submodule. This preset process data includes the temperature threshold, time interval, cooling method, microstructure characteristics, and performance indicators for heat treatment. After the heat treatment process starts, the data acquisition module continuously captures dynamic data during the process, including the current real-time temperature and strain parameters. The acquired data is transmitted in real-time to the real-time feedback module to provide dynamic input for subsequent analysis. Using this technical solution, high-precision identification of heat treatment process information is ensured in a dynamically changing environment, thereby continuously producing high-performance Ti-Al-Mo titanium alloy forgings.

[0031] In one possible implementation, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, the data acquired by the data acquisition module is first compared and analyzed with the data in the database sub-module. The data resources stored in the database sub-module include initially imported process benchmark data, historical process / result data of similar processes, microstructure, properties, and process parameter information. If there is no correlation after comparison, the data continues to be transmitted to the online analysis sub-module and the prediction sub-module. By adopting the above technical solution, a hierarchical and efficient processing architecture is established, allowing real-time acquired data to be quickly matched with historical process benchmarks and successful cases in the database. If a high correlation exists, verified optimization parameters are directly called for control, greatly shortening the system response time and ensuring the immediacy and stability of process execution, especially suitable for standardized processing of batch products. When the data belongs to abnormal operating conditions, the system can switch to the online analysis and prediction model for in-depth calculation, ensuring the ability to cope with complex or unknown situations. This mechanism not only optimizes the allocation of computing resources, but also makes the system a continuously learning intelligent agent. Every successful processing will be transformed into new experience data, continuously enriching the process knowledge base. This will improve production efficiency, ensure product strength and toughness matching, and drive the process technology to continuously evolve towards a more precise and autonomous direction.

[0032] As one possible implementation, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, the data transmission to the online analysis submodule and the prediction submodule includes: after the data is transmitted to the online analysis submodule and the prediction submodule, online simulation is performed to obtain analysis and prediction results, which are then used to further supplement the database submodule to enrich the data pool; wherein: the online analysis submodule dynamically analyzes the microstructure and performance development status under the current process, and predicts the evolution direction of microstructure and performance in subsequent process processes through online simulation by the prediction submodule, forming a judgment result on whether it meets expectations. With this technical solution, the online analysis submodule analyzes the current microstructure and performance status in real time, while the prediction submodule, based on this, uses a simulation model to deduce the evolution trend under subsequent process paths, enabling the system not only to know the current state but also to predict the future. Based on the comparison between the prediction results and the preset target, the system can determine in advance whether the process is deviating from the expected trajectory, making the feedback control predictive. The system can proactively adjust parameters (such as intervening in advance to change the cooling rate) before performance defects actually occur, forming a complete intelligent closed loop of "perception-analysis-decision-learning" to drive the system to continuously evolve and cope with different situations.

[0033] As one possible implementation, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, after determining whether the formation meets the expected results, the process includes: if the determination result indicates that the microstructure / properties are developing towards the expected target, the process continues to execute under the current conditions, and the data acquisition module maintains data acquisition to maintain a closed-loop process; if the determination result indicates that the microstructure / properties are not developing towards the expected target, a feedback control submodule is triggered. Using this technical solution, it can be ensured that the heat treatment process always proceeds along the optimal path, thereby achieving the goal of high strength and toughness in Ti-Al-Mo titanium alloy forgings.

[0034] As one possible implementation, in the high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings of the present invention, after the trigger feedback control submodule, the system includes: the feedback control submodule generating targeted process adjustment parameters based on the associated data in the database submodule and the deviation information obtained from the online analysis submodule, and feeding the process adjustment parameters back to the actual heat treatment process to complete the dynamic correction of the process conditions; wherein, the process adjustment parameters include the temperature adjustment range, the time increase / decrease duration, and the cooling method. Using this technical solution, the actual process curve can be continuously "pulled back" to the theoretically optimal path, ensuring that the optimal process can be applied to high-strength and toughening heat treatment without damage and with high fidelity.

[0035] To better understand the present invention, the following specific embodiments further illustrate the content of the present invention, but the content of the present invention is not limited to the following embodiments.

[0036] Unless otherwise specified, all raw materials used in the following examples are commercially available.

[0037] In the following embodiments, the titanium alloy used is Ti62F alloy, which is a Ti-Al-Mo titanium alloy.

[0038] Example 1 This embodiment provides a high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, including: Step 1: Obtain a Ti62F titanium alloy square forging billet with dimensions of 250 mm × 250 mm × 250 mm. Step 2: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. The forging billet is heated at a rate of 5℃ / minute. During the heating process, the temperature rises by 100℃ at a time. After reaching the target temperature each time, the temperature is held for 2 minutes until the forging billet is heated to 880℃. The temperature is then held for 2 hours and air-cooled to room temperature. Step 3: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. The forging billet is heated at a rate of 2℃ / minute. During the heating process, the temperature rises by 115℃ at a time. After reaching the target temperature each time, the temperature is held for 2 minutes until the forging billet is heated to 670℃. The temperature is then held for 4 hours and air-cooled to room temperature.

[0039] The performance of the heat-treated Ti62F titanium alloy in this embodiment was tested. Specifically, the room temperature impact performance test was conducted on an NI750 pendulum impact testing machine, with a hammer radius of 2 mm, an impact energy of 750 J, and an ambient temperature of 23 ℃. The impact specimens were prepared according to GB / T 229-2020, using a standard U-notch, with specific dimensions as shown in the figure. Figure 2 As shown. The impact test adopted a single pendulum impact method, with the specimen placed horizontally between two supports and the impact end facing the center of the notch. Before the test, all specimens were equilibrated at room temperature without additional heat treatment or surface finishing. The room temperature tensile test was performed on a SUNS-UTM5105X tensile testing machine, and the tensile specimens were prepared according to GB / T 228.1-2021, with specific dimensions as shown. Figure 3 As shown. Room temperature mechanical properties such as tensile strength, yield strength, and elongation were obtained through room temperature tensile tests, with the test rate controlled at 1 mm / min. The measured impact toughness of Ti62F titanium alloy was 64 J, tensile strength was 1036 MPa, yield strength was 970 MPa, elongation was 17.5%, and reduction of area was 35%. Figure 1 This is an EBSD image of the heat-treated Ti62F titanium alloy in this embodiment. The low-magnification EBSD image shows a uniformly distributed primary α phase (yellow) and β transformation microstructure (red), with good overall homogeneity and no harmful phase precipitation. The high-magnification EBSD image clearly shows a fine lamellar structure, with a lamellar width of approximately 1.44 μm, and no abnormal grain growth. Furthermore, Figure 4 The image shows a SEM image of the impact fracture surface of the Ti62F titanium alloy after heat treatment in this embodiment. It can be seen that the fracture surface has a large number of small dimples and a small number of large dimples, and the tear ridges are more obvious, showing excellent toughness. Figure 5 The image shows a tensile fracture surface of the Ti62F titanium alloy after heat treatment in this embodiment. It can be seen that the dimples in the fracture surface are relatively large and their boundaries are clearer. There is a clear large dimple containing a small dimple morphology, which is a typical plastic fracture morphology. This is due to sufficient solid solution, uniform distribution of aging precipitates, and the absence of harmful phases such as non-strengthening phases.

[0040] Example 2 This embodiment provides a high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, including: Step 1: Obtain a Ti62F titanium alloy square forging billet with dimensions of 250 mm × 250 mm × 250 mm. Step 2: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. The forging billet is heated at a rate of 10℃ / minute. During the heating process, the temperature rises by 75℃ at a time. After reaching the target temperature each time, the temperature is held for 4 minutes until the forging billet is heated to 880℃. The temperature is then held for 4 hours and air-cooled to room temperature. Step 3: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. The forging billet is heated at a rate of 6℃ / minute. During the heating process, the temperature rises by 95℃ at a time. After reaching the target temperature each time, the temperature is held for 3 minutes until the forging billet is heated to 650℃. The temperature is then held for 4 hours and air-cooled to room temperature.

[0041] The performance of the heat-treated Ti62F titanium alloy in this embodiment was tested; the impact toughness of the Ti62F titanium alloy was measured to be 56 J, the tensile strength was 1059 MPa, the yield strength was 992 MPa, the elongation was 16.5%, and the reduction of area was 32%.

[0042] Example 3 This embodiment provides a high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, including: Step 1: Obtain a Ti62F titanium alloy square forging billet with dimensions of 250 mm × 250 mm × 250 mm. Step 2: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. During the heating process, the forging billet is heated at a rate of 5℃ / minute. For forging billets below 500℃, the single temperature rise is 100℃. After reaching the target temperature, hold for 2 minutes. Adjust the heating rate to 10℃ / minute. For forging billets above 500℃, the single temperature rise is 50℃. After reaching the target temperature, hold for 6 minutes. Continue until the temperature of the forging billet reaches 880℃, then hold for 2 hours. Air cool to room temperature. Step 3: Place the forging billet in the heating furnace. The initial temperature of the forging billet is 25℃. The temperature is increased at a rate of 10℃ / minute. During the heating process, the single temperature rise of the forging billet below 300℃ is 115℃. After reaching the target temperature, hold it for 2 minutes. Adjust the heating rate to 6℃ / minute. The single temperature rise of the forging billet above 300℃ is 75℃. After reaching the target temperature, hold it for 4 minutes. Continue until the temperature of the forging billet reaches 650℃, and then hold it for 18 hours. Air cool to room temperature.

[0043] The performance of the heat-treated Ti62F titanium alloy in this embodiment was tested; the impact toughness of the Ti62F titanium alloy was measured to be 57J, the tensile strength was 1025MPa, the yield strength was 966MPa, the elongation was 15.5%, and the reduction of area was 30%.

[0044] Example 4 The high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings provided in this embodiment is basically the same as that in Embodiment 1. The difference is that the final heating temperature in step 2 of this embodiment is 840℃, and the final heating temperature in step 3 is 650℃.

[0045] The performance of the heat-treated Ti62F titanium alloy in this embodiment was tested; the impact toughness of Ti62F titanium alloy was measured to be 58J, the tensile strength was 1042MPa, the yield strength was 982MPa, the elongation was 16%, and the reduction of area was 25%.

[0046] Example 5 Please see Figures 6 to 8 This embodiment provides a high-strength and toughening heat treatment system for Ti62F titanium alloy forgings, utilizing a forging blank 1, a heating furnace 2, and thermocouples 3. The forging blank 1 is placed inside the heating furnace 2, and multiple thermocouples 3 are installed on the forging blank. Taking the heat treatment of Ti62F titanium alloy forging blanks as an example, the heat treatment system includes a data acquisition module 4 and a real-time feedback module 5. The data acquisition module is connected to the thermocouples, and the real-time feedback module is connected to the data acquisition module. The data acquisition module is used to acquire temperature and stress change data at different locations of the forging blank during the heat treatment process, and obtains multi-dimensional and multi-physical quantity synchronous monitoring data through sensors. The real-time feedback module includes interconnected database sub-modules and online analysis sub-modules. The system comprises a database submodule, a prediction submodule, and a feedback control submodule. The database submodule manages historical and simulation data of the heat treatment process, forming a process knowledge base. Historical and simulation data include the microstructure evolution of materials under different temperature conditions and their corresponding mechanical properties. The online analysis and prediction submodules predict the current material microstructure and key performance indicators using simulation models and real-time temperature data, and analyze input process parameters and call corresponding calculation models. The feedback control submodule dynamically adjusts key parameters in the heat treatment equipment based on real-time prediction results. Key parameters include heating power, holding time, and cooling rate. Furthermore, in the heat treatment system of this embodiment, preset process data is imported into the database submodule. The preset process data includes the temperature threshold, time interval, cooling method, microstructure characteristics, and performance indicators of the heat treatment. After the heat treatment process is started, the data acquisition module continuously captures dynamic data during the process. The dynamic data includes the current real-time temperature and strain parameters. The acquired data is transmitted in real time to the real-time feedback module to provide dynamic input for subsequent analysis. Furthermore, in the heat treatment system of this embodiment, the data collected by the data acquisition module is first compared and analyzed with the data in the database submodule. The data resources stored in the database submodule include the initially imported process baseline data, historical process / result data of similar processes, microstructure, performance, and process parameter information. If there is no correlation after comparison, the data continues to be transmitted to the online analysis submodule and the prediction submodule. Furthermore, in the heat treatment system of this embodiment, data transmission to the online analysis submodule and prediction submodule includes: after data transmission to the online analysis submodule and prediction submodule, online simulation is performed to obtain analysis and prediction results, which are then used to further supplement the database submodule to enrich the data pool; wherein: the online analysis submodule dynamically analyzes the microstructure and performance development status under the current process, and predicts the evolution direction of microstructure and performance in subsequent process processes through online simulation by the prediction submodule, forming a judgment result on whether it meets expectations; when the judgment result is that the microstructure / performance is developing towards the expected target (i.e., target performance), the process continues to be executed according to the current conditions, and at the same time, the data acquisition module maintains data acquisition to maintain the process loop; when the judgment result is that the microstructure / performance is not developing towards the expected target, the feedback control submodule is triggered; after the feedback control submodule is triggered, the feedback control submodule generates targeted process adjustment parameters based on the associated data in the database submodule and the deviation information obtained by the online analysis submodule, and feeds the process adjustment parameters back to the actual heat treatment process to complete the dynamic correction of process conditions; wherein, the process adjustment parameters include temperature adjustment range, time increase / decrease duration, and cooling method.

[0047] Furthermore, when the pretreated forging billet is placed in the heat treatment furnace for solution treatment (i.e., the first heat treatment): in the discontinuous dynamic heating stage, the preset heating rate is ≥5℃ / min, the single temperature rise is ≥50℃, and the short-term heat holding time is ≥2min when the single temperature rise is reached. The faster the heating rate, the longer the short-term heat holding time, to ensure that the material reaches a sufficient thermal equilibrium state and avoids the thermal stress concentration caused by overheating and crack initiation, until the solution temperature is ≥800℃; in the heat holding stage, the preset heat holding time is ≥30min after the temperature in the heat treatment furnace stabilizes; in the cooling stage, the preset cooling is furnace cooling or air cooling.

[0048] Furthermore, during the aging treatment (i.e., the second heat treatment) of the solution-treated samples: in the discontinuous dynamic heating stage, the preset heating rate is ≥2℃ / min, the single temperature rise is ≥75℃, and the short holding time upon reaching the single temperature rise is ≥2min. The faster the heating rate, the longer the short holding time, to ensure that the material reaches a sufficient thermal equilibrium state and avoids thermal stress concentration caused by overheating, which could lead to crack initiation, until the aging temperature is ≥500℃; in the heat treatment stage, the preset holding time after the temperature in the heat treatment furnace stabilizes is ≥30min; in the cooling stage, the preset cooling is either furnace cooling or air cooling. Specifically, the preset target properties are: impact toughness ≥50J, tensile strength ≥900MPa, yield strength ≥800MPa, elongation ≥10%, and reduction of area ≥20%.

[0049] Comparative Example 1 The heat treatment method for the Ti-Al-Mo titanium alloy forgings provided in this comparative example is basically the same as that in Example 1. The difference is that in step 2 of this comparative example, the Ti62F titanium alloy forging billet is directly heated from room temperature to 880°C at a heating rate of 5°C / min; in step 3, the Ti62F titanium alloy forging billet is directly heated from room temperature to 670°C at a heating rate of 2°C / min.

[0050] After performance testing of the heat-treated Ti62F titanium alloy in this comparative example, the impact toughness of the Ti62F titanium alloy was measured to be 70 J, the tensile strength was 996 MPa, the yield strength was 937 MPa, the elongation was 16.5%, and the reduction of area was 35%. It can be seen that the toughness of the heat-treated Ti62F titanium alloy in this comparative example is not much different from that of Example 1, but the strength is lower than that of Example 1.

[0051] Comparative Example 2 The heat treatment method for the Ti-Al-Mo titanium alloy forgings provided in this comparative example is basically the same as that in Example 1, except that the heating rate is 2℃ / min in step 2 and 1℃ / min in step 3 of this comparative example.

[0052] After performance testing of the heat-treated Ti62F titanium alloy in this comparative example, the impact toughness of the Ti62F titanium alloy was measured to be 71 J, the tensile strength was 965 MPa, the yield strength was 910 MPa, the elongation was 15%, and the reduction of area was 39%. It can be seen that the toughness of the heat-treated Ti62F titanium alloy in this comparative example is not much different from that of Example 1, but the strength is lower than that of Example 1.

[0053] Comparative Example 3 The heat treatment method for the Ti62F titanium alloy forgings provided in this comparative example is basically the same as that in Example 1, except that the heating rate in step 2 of this comparative example is 16°C / min, and the heating rate in step 3 is 11°C / min.

[0054] After performance testing of the heat-treated Ti62F titanium alloy in this comparative example, the impact toughness of the Ti62F titanium alloy was measured to be 62 J, the tensile strength was 1013 MPa, the yield strength was 952 MPa, the elongation was 17%, and the reduction of area was 34%. It can be seen that the toughness of the heat-treated Ti62F titanium alloy in this comparative example is not much different from that of Example 1, but the strength is lower than that of Example 1.

[0055] In the description of the above embodiments, specific features, structures, materials, or characteristics may be combined in any suitable manner in one or more embodiments or examples.

[0056] The above description is merely a specific embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the technical scope disclosed in the present invention should be included within the scope of protection of the present invention. Therefore, the scope of protection of the present invention should be determined by the scope of the claims.

Claims

1. A high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings, characterized in that, include: Obtain Ti-Al-Mo titanium alloy forgings; The forging billet is heated at a rate of 5~15℃ / min, with the temperature rise decreasing from 100~50℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~6 minutes until the forging billet is heated to 800~900℃ and held for 2~4 hours, then air-cooled to room temperature. The forging billet is heated at a rate of 2~10℃ / min, with the temperature rise decreasing from 115~75℃ in a single step during the heating process. After reaching the target temperature each time, it is held for 2~4 minutes until the forging billet is heated to 550~700℃ and held for 2~18 hours, then air-cooled to room temperature.

2. The high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings according to claim 1, characterized in that, After obtaining the Ti-Al-Mo titanium alloy forging billet, the process further includes: The forging blank is surface treated to remove oil, rust and forging residue oxide layer from its surface.

3. The high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings according to claim 1, characterized in that, After two heat treatments, the Ti-Al-Mo titanium alloy forms a basketweave structure with a primary α phase volume fraction of 65.9%~77.9% and an average lamellar α width of 1.04μm~2.8μm. After heat treatment, the Ti-Al-Mo titanium alloy has a room temperature tensile strength greater than or equal to 1025MPa, a yield strength greater than or equal to 966MPa, an elongation greater than or equal to 15.5%, a reduction of area greater than or equal to 25%, and an impact absorption energy greater than or equal to 56J.

4. A high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings, characterized in that, The high-strength and toughening heat treatment method for Ti-Al-Mo titanium alloy forgings according to any one of claims 1 to 3 includes: The data acquisition module is used to acquire temperature and stress change data at different locations of the forging billet during the heat treatment process, and obtain multi-dimensional and multi-physical quantity synchronous monitoring data through sensors; The real-time feedback module includes a database submodule, an online analysis submodule, a prediction submodule, and a feedback control submodule. The database submodule manages historical and simulation data of the heat treatment process, forming a process knowledge base. The historical and simulation data include the microstructure evolution of materials under different temperature conditions and their corresponding mechanical property indicators. The online analysis and prediction submodules are used to predict the current material microstructure and key performance indicators through simulation models and real-time temperature data, and to complete the analysis of input process parameters and the invocation of corresponding calculation models. The feedback control submodule is used to dynamically adjust key parameters in the heat treatment equipment based on the real-time prediction results. These key parameters include heating power, holding time, and cooling rate.

5. The high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to claim 4, characterized in that, By importing preset process data into the database submodule; the preset process data includes the temperature threshold, time range, cooling method, microstructure characteristics and performance indicators of heat treatment; After the heat treatment process is started, the data acquisition module continuously captures dynamic data during the process, including the current real-time temperature and strain parameters. The acquired data is transmitted in real time to the real-time feedback module to provide dynamic input for subsequent analysis.

6. The high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to claim 5, characterized in that, The data acquired by the data acquisition module is first compared and analyzed with the data in the database submodule. The data resources stored in the database submodule include the initially imported process baseline data, historical process / result data of similar processes, organizational morphology, performance, and process parameter information. If there is no correlation after comparison, the data continues to be transmitted to the online analysis submodule and the prediction submodule.

7. The high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to claim 6, characterized in that, The data is transmitted to the online analysis submodule and the prediction submodule, including: After the data is transmitted to the online analysis submodule and the prediction submodule, online simulation is performed to obtain analysis and prediction results. These results are then used to further supplement the database submodule to enrich the data pool. The online analysis submodule dynamically analyzes the microstructure and performance development status under the current process, and predicts the evolution direction of microstructure and performance in subsequent processes through online simulation by the prediction submodule, forming a judgment result on whether it meets expectations.

8. The high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to claim 7, characterized in that, After determining whether the formation of the expected judgment result includes: When the assessment results indicate that the organizational morphology / performance is developing in accordance with the expected goals, the process continues to be executed under the current conditions. At the same time, the data acquisition module continues to collect data to maintain the closed loop of the process. If the assessment results indicate that the organizational structure / performance is not developing in accordance with the expected goals, the feedback control submodule will be triggered.

9. The high-strength and toughening heat treatment system for Ti-Al-Mo titanium alloy forgings according to claim 8, characterized in that, The trigger feedback control submodule includes: The feedback control submodule generates targeted process adjustment parameters based on the associated data in the database submodule and the deviation information obtained from the online analysis submodule, and feeds the process adjustment parameters back to the actual heat treatment process to complete the dynamic correction of process conditions. The process adjustment parameters include temperature adjustment range, time increment / decrement duration, and cooling method.

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