CN110273118B - Heat treatment process of titanium alloy - Google Patents
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Abstract
The invention discloses a heat treatment process of a titanium alloy, belonging to the technical field of material science. The method mainly comprises the following steps: the first reheating treatment heating temperature T is (T)β‑50)℃≤T≤(Tβ+60) deg.C, holding time t ═ eta °1*max，maxIs the maximum cross-sectional thickness, eta, of the titanium alloy forging1Taking the heating coefficient as 0.6-1.5 min/mm, and discharging the forged piece after the heat preservation is finished, and carrying out air cooling, oil cooling or water cooling to the room temperature; the heating temperature T of the second heat treatment is more than or equal to 650 ℃ and less than 780 ℃, and the heat preservation time T is (eta)2*max)/2，maxIs the maximum cross-sectional thickness, eta, of the titanium alloy forging2Taking the heating coefficient as 0.3-1.2 min/mm, and discharging the forged piece after heat preservation and air cooling to room temperature; and the heating temperature T of the third heat treatment is more than or equal to 480 ℃ and less than 650 ℃, the heat preservation time is more than or equal to 240min and less than or equal to 600min, and the forged piece is taken out of the furnace after the heat preservation is finished and is cooled to the room temperature by air. The process solves the problem of large difference of the structure performance of the edge part and the core part of the forged piece after the solution aging of the near-beta type, metastable-beta type and fully stable beta type titanium alloys, and is particularly suitable for preparing the large-section/variable-section titanium alloy forged piece with high strength and uniform structure performance.
Description
Technical Field
The invention belongs to the technical field of material science, and relates to a heat treatment process of a titanium alloy.
Background
Titanium and titanium alloy have specific strength high, high temperature resistant, corrosion-resistant, can weld excellent characteristic such as, have extensive application in modern industry and national defense field such as aerospace, chemical industry, ocean, especially in the aviation field, titanium alloy quantity and one piece weight or projected area have become one of the important signs that measure the aircraft advancement.
In order to meet the urgent demand of the new generation of advanced airplanes on weight reduction, more definite requirements are put forward on the strength and comprehensive performance of the titanium alloy material, the development of the high-strength or ultra-high-strength titanium alloy material and the application technology become the common efforts of researchers at home and abroad, and simultaneously, the development of the high-strength or ultra-high-strength titanium alloy material and the application technology also become the common efforts of the researchers at home and abroadIs an important mark for the scientific and technical development of titanium alloy materials. Among titanium alloys classified by phase group, near- β type and metastable- β type titanium alloys are most suitable for development and development of high-toughness or ultra-high-toughness titanium alloys because of their excellent heat treatment strengthening effect, high hardenability, good workability, and the like. In the research aspect of high-toughness titanium alloy, the titanium alloy represented by Ti-15-3 (with the domestic corresponding mark of TB5), Ti-1023 (with the domestic corresponding mark of TB6), beta 21s (with the domestic corresponding mark of TB8), BT22 (with the domestic corresponding mark of TC18) developed by the former Soviet Union and Ti-5553 and Ti-55531 which are improved and designed is the most widely applied. For example, in the field of aviation application, the strength level of a TB6 titanium alloy forging (the thickness is less than or equal to 100mm) under the condition of solution aging is more than 1105MPa, and the fracture toughness level is 60 MPa.m1/2The strength level of TC18 titanium alloy forging (the thickness is less than or equal to 250mm) under the double annealing condition is 1080 MPa-1230 MPa, and the fracture toughness level is 60 MPa-m1/2The above. In the research aspect of ultrahigh strength and toughness titanium alloy, the great development is made in China in recent years, the Beijing aviation material research institute develops the near-beta type TB17 titanium alloy with the independent intellectual property right in China, the alloy forging has high strength-plasticity-toughness matching after solution aging heat treatment, can be used as a key bearing component for aviation, and can also be popularized and applied in the fields of aerospace, weapon civil and the like.
In designing and developing new alloys, [ Mo ] equivalent methods have become the most commonly accepted titanium alloy design guidelines for scientific researchers. The current research result shows that when a high-strength and high-toughness or ultra-high-strength and high-toughness titanium alloy material is designed and developed, the [ Mo ] equivalent is selected near a critical value, namely the alloy has the best heat treatment strengthening effect when the alloy is in a near-beta type and a metastable-beta type, and the influence of alloy elements on an alpha phase and a beta phase is comprehensively considered, so that the diversity and the complexity of the phase transition of the near-beta type and the metastable-beta type titanium alloy are brought. From the strengthening mechanism, the size, amount and morphology of the beta-phase time-effect precipitated second phase determine the final strength of the alloy. Basic research on beta-type titanium alloy proves that alloy components, treatment temperature and time, cooling rate and the like all have important influence on the appearance, size, quantity and distribution of a precipitated second phase in a beta-phase matrix. For example, when aging treatment is carried out at a lower temperature (about 350 ℃), the omega phase with a nano-scale is mainly precipitated, the omega phase is mainly in an oval shape in a Ti-Mo based alloy system, the omega phase is mainly in a square shape in a Ti-Cr based alloy system and is uniformly dispersed in a matrix, and the alloy shows high strength and low plasticity. When the aging treatment is carried out at a higher temperature, the alpha phases with different sizes are mainly precipitated, and the alpha phases and the matrix keep the Bergen phase relationship, so that the strength of the alloy is reduced, but the plasticity is obviously improved. Meanwhile, the thermodynamic and kinetic research results further show that the aging response of the beta-type titanium alloy is very quick, and the second phase nucleation in the beta matrix reaches the second level and grows along with the second phase nucleation. Researchers have proposed a heat treatment design idea of taking an omega phase as an alpha phase precursor phase according to the characteristics of omega phase precipitation so as to obtain a microstructure in which an alpha phase with a micro-nano scale is uniformly distributed on a beta matrix. Researchers in China design a multi-stage solid solution aging process for obtaining a microstructure with multi-scale alpha phase mixture according to the alpha phase precipitation characteristics.
Experience and research prove that the difference of microstructure and mechanical property always exists in the edge area and the central area of the near-beta type and metastable-beta type titanium alloy forgings, even if the section thickness of the forgings is lower than the hardenability thickness of the alloy, the section thickness of the forgings is also unavoidable, and the difference of the microstructure property is more obvious along with the increase of the section thickness. The basic reason for this phenomenon is that because the near-beta type and metastable-beta type titanium alloys are sensitive to heat treatment parameters, when the forged piece is cooled by high-temperature heat treatment, the difference between the temperature field and the stress field of the edge region and the core region of the forged piece is obvious, so that the phase change dynamics of different positions of the forged piece is influenced, and finally, the phase composition and the microstructure morphology difference of the edge region and the core region of the forged piece are caused. Therefore, along with the strength improvement, the cross section increase and the shape complexity of the near-beta type and metastable-beta type titanium alloy forgings, the problem of structural property difference of the forgings at different positions is more and more obvious, and how to ensure the structural property uniformity of the forgings while obtaining high strength becomes a difficult problem to be solved by scientific researchers.
Although the dominant heat treatment processes of beta titanium alloys of different alloy types are different, the current heat treatment processes related to the titanium alloys can be mainly summarized as follows: ordinary annealing, double annealing, single solid solution plus single (level) aging, double solid solution plus single (level) aging, single solid solution plus double (level) aging, double solid solution plus double (level) aging, furnace cooling after single solid solution or converter cooling plus single (level) aging, etc. The current research results show that when a forging with high strength requirement (1200MPa level and above) and good structural property uniformity needs to be prepared, the heat treatment process has certain limitations. The reason is that when the common annealing heat treatment process is adopted, the advantage of beta-type titanium alloy aging strengthening is not fully exerted, and the strength of the forged piece is often lower as a whole. By adopting the solution-aging heat treatment process listed above, along with the increase of the section thickness of the forging or the increasing of the shape of the forging, the difference of the structural properties of the edge region and the center region of the forging is obviously increased, so that the strength of the center region of the forging is usually low, and the strength and the plasticity of the edge region are extremely low. If a heat treatment process of furnace cooling or converter cooling plus aging or solid solution temperature reduction after solid solution is adopted, although the difference of the structural properties of the edge region and the core region of the forging is improved, the overall strength of the forging cannot be improved at the expense of the strength. Therefore, in order to prepare titanium alloy forgings with high strength and uniform structure properties, a new heat treatment process suitable for beta-type titanium alloy needs to be designed.
Disclosure of Invention
The invention aims to design and provide a novel heat treatment process of titanium alloy aiming at the limitations of the existing metastable beta type, near beta type and fully stable beta type titanium alloy heat treatment processes, so that a titanium alloy large-section/variable-section forging with high strength and uniform structure performance is prepared.
The technical scheme adopted by the invention for solving the technical problems is as follows:
(1) and (5) carrying out first reheating treatment. Putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is (T)β-50)℃≤T≤(Tβ+60)℃，TβIs prepared fromThe metallurgical transformation temperature is measured, the resistance furnace starts to calculate the heat preservation time after reaching the set heating temperature T again, and the heat preservation time T is equal to eta1×max，maxIs the maximum cross-sectional thickness of the titanium alloy forging with the unit of mm and eta1Taking the heating coefficient as 0.6-1.5 min/mm, and keeping the temperature t unit as min;
(2) discharging the titanium alloy forging subjected to the heat preservation in the step (1) out of the furnace, and carrying out air cooling, oil cooling or water cooling to room temperature;
(3) and (5) second heat treatment. Putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is more than or equal to 650 ℃ and less than 780 ℃, calculating the heat preservation time after the resistance furnace reaches the set heating temperature T again, and the heat preservation time T is (eta)2×max)/2，maxIs the maximum cross-sectional thickness of the titanium alloy forging with the unit of mm and eta2Taking the heating coefficient as 0.3-1.2 min/mm, and keeping the temperature t unit as min;
(4) discharging the titanium alloy forge piece subjected to heat preservation in the step (3) out of the furnace and air-cooling to room temperature;
(5) and (3) carrying out third heat treatment. Putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is greater than or equal to 480 ℃ and less than 650 ℃, and calculating the heat preservation time after the resistance furnace reaches the set heating temperature T again, wherein the heat preservation time is greater than or equal to 240min and less than or equal to 600 min;
(6) and (5) discharging the titanium alloy forge piece subjected to heat preservation in the step (5) out of the furnace, and air-cooling to room temperature.
The maximum temperature deviation of the effective working area in the resistance furnace is not more than +/-5 ℃.
The process is suitable for the heat treatment of near-beta type, metastable beta type and fully-stable beta type titanium alloys.
The invention has the advantages and beneficial effects that:
(1) the solid solution temperature T in the first reheat treatment is (T)β-50)℃≤T≤(Tβ+60) DEG C, the proper tissue type can be obtained according to different design and use requirements of the material, and the forging piece is at the phase transformation point TβBy the above treatment, the material having excellent damage tolerance can be obtainedLamellar structure, forging at transformation point TβThe following treatments can provide a two-phase structure having more excellent fatigue properties; the cooling mode during the first reheating treatment is set to air cooling, oil cooling and water cooling, and the adequate metastable beta phase is reserved by selecting a proper cooling medium according to the depth of the alloy which can be quenched and the thickness of the section of the forged piece, so that the strength of the central part area during the subsequent aging treatment of the forged piece is ensured.
(2) The second heat treatment is the innovation and key point of the process, the traditional heat treatment thought is overturned, and the basic principle that the forgings are not heat-penetrated is taken, so that the process is mainly based on the following two points: firstly, the thermodynamic characteristic of rapid response of beta-type titanium alloy during aging provides conditions for locally controlling nucleation, precipitation and growth of a secondary alpha phase; secondly, by combining a heat treatment numerical simulation technology, the thermodynamic loss of the edge area of the forge piece caused by the excessively high cooling speed during the solution cooling of the first reheating treatment is compensated by determining and accurately controlling the medium-temperature overaging temperature and the heat preservation time. The second heat treatment ensures that the integral metastable beta phase content of the forging is consistent, and the secondary alpha phase has the same size, thereby realizing the uniformity of the integral structure performance of the forging.
(3) The heating temperature T of the third heat treatment is more than or equal to 480 ℃ and less than 650 ℃, the heat preservation time is more than or equal to 240min and less than or equal to 600min, and the forging is subjected to long-term aging heat preservation to fully precipitate a more fine and dispersed secondary alpha phase integrally, so that the strength of the forging is ensured, the structure is also stabilized, and the forging with high strength, uniform structure and stable performance is obtained.
The process is suitable for the heat treatment of near-beta type, metastable-beta type and fully-stable beta type titanium alloys, solves the problem of large difference of the structural properties of the edge part and the core part of the forged piece after the solution aging of the titanium alloys, and is particularly suitable for preparing large-section/variable-section titanium alloy forged pieces with high strength and uniform structural properties.
Drawings
The present invention will be described in further detail with reference to the accompanying drawings and examples.
FIG. 1 is a photograph of the microstructure of the edge and the center region of a TB17 titanium alloy forging of example 1 with a magnification of 10000 times, wherein (a) is the photograph of the microstructure of the edge; (b) photograph of the heart microscopic structure.
FIG. 2 is a photograph of the microstructure of the edge and core regions of a TB17 titanium alloy forging of example 2 with magnification of 50000 times, wherein (a) is the photograph of the microstructure of the edge; (b) photograph of the heart microscopic structure.
The specific implementation mode is as follows:
the invention is further illustrated by the following specific examples:
example 1
The embodiment is a near-beta type TB17 titanium alloy free forging subjected to heat treatment, and the effective thickness is 100 mm.
The specific heat treatment process is as follows:
(1) and (5) carrying out first reheating treatment. Putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T, and heating, wherein the set heating temperature T is a phase transformation point (T)β) And (5) starting to calculate the heat preservation time after the resistance furnace reaches the set heating temperature T again at the temperature of 25 ℃, wherein the heat preservation time T is 120min, and after the heat preservation is finished, discharging the forge piece from the furnace and carrying out air cooling to the room temperature.
(2) And (5) second heat treatment. And (3) putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is 680 ℃, the resistance furnace starts to calculate the heat preservation time after reaching the set heating temperature T again, the heat preservation time T is 30min, and after the heat preservation is finished, the forging is taken out of the furnace and is cooled to the room temperature in an air cooling mode.
(3) And (3) carrying out third heat treatment. And (3) putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is 500 ℃, the resistance furnace starts to calculate the heat preservation time after reaching the set heating temperature T again, the heat preservation time T is 480min, and after the heat preservation is finished, the forging is taken out of the furnace and is cooled to the room temperature in an air cooling mode.
The free forging of example 1 was tested for properties and compared to a conventional solution age heat treated free forging, with the results shown in table 1. It can be seen that when the forging is subjected to common solution aging treatment, the strength of the edge part of the forging is higher, the plasticity is lower, and the mechanical properties of the edge part of the forging are greatly different from those of the center part of the forging; when the process is used for carrying out heat treatment on the forge piece, the structural property uniformity of the edge part and the center part of the forge piece is obviously improved.
TABLE 1 Room temperature mechanical Properties of free forgings (effective thickness 100mm) of TB17 titanium alloy
Example 2
The embodiment is a near-beta type TB17 titanium alloy free forging subjected to heat treatment, and the effective thickness is 200 mm.
The specific heat treatment process is as follows:
(1) and (5) carrying out first reheating treatment. Putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T, and heating, wherein the set heating temperature T is a phase transformation point (T)β) And (3) starting to calculate the heat preservation time after the resistance furnace reaches the set heating temperature T again at the temperature of 20 ℃, wherein the heat preservation time T is 150min, and after the heat preservation is finished, discharging the forge piece from the furnace and air-cooling to the room temperature.
(2) And (5) second heat treatment. And (3) putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is 700 ℃, the resistance furnace starts to calculate the heat preservation time after reaching the set heating temperature T again, the heat preservation time T is 55min, and after the heat preservation is finished, the forging is taken out of the furnace and is cooled to the room temperature in an air cooling mode.
(3) And (3) carrying out third heat treatment. And (3) putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is 510 ℃, the resistance furnace starts to calculate the heat preservation time after reaching the set heating temperature T again, the heat preservation time T is 480min, and after the heat preservation is finished, the forging is taken out of the furnace and is cooled to the room temperature in an air cooling mode.
The free forging of example 2 was tested for properties and compared to a conventional solution age heat treated free forging, with the results shown in table 2. It can be seen that when the forging is subjected to common solution aging treatment, the tensile strength-elongation at the edge of the forging is 1393 MPa-2.6%, the tensile strength-elongation at the center of the forging is 1285 MPa-11.1%, and the structural property difference is large; when the process is used for carrying out heat treatment on the forge piece, the tensile strength-elongation at the edge of the forge piece is 1315 MPa-8.5%, the tensile strength-elongation at the center of the forge piece is 1283 MPa-10.9%, and the uniformity of the structural properties at the edge and the center of the forge piece is obviously improved.
TABLE 2 Room temperature mechanical Properties of free forgings (effective thickness 200mm) of TB17 titanium alloy
Claims (3)
1. The heat treatment process of the titanium alloy is characterized by comprising the following steps:
(1) carrying out first reheating treatment; putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is (T)β-25)℃≤T≤(Tβ-20)℃，TβCalculating the holding time T which is equal to eta after the resistance furnace reaches the set heating temperature T again for the alloy phase transition point temperature1×max，maxIs the maximum cross-sectional thickness of the titanium alloy forging with the unit of mm and eta1The heating coefficient is shown, and the unit of the heat preservation time t is min, eta1The value range of (A) is 0.75-1.2 min/mm;
(2) discharging the titanium alloy forging subjected to heat preservation in the step (1) out of the furnace and cooling, wherein the cooling mode is air cooling or air cooling to room temperature;
(3) second heat treatment; putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the set heating temperature T is more than or equal to 680 ℃ and less than or equal to 700 ℃, calculating the heat preservation time after the resistance furnace reaches the set heating temperature T again, and the heat preservation time T is (eta)2×max)/2，maxIs the maximum cross-sectional thickness of the titanium alloy forging with the unit of mm and eta2Is the coefficient of heating, eta2The value range of (a) is 0.3-1.2 min/mm, and the unit of the heat preservation time t is min;
(4) discharging the titanium alloy forge piece subjected to heat preservation in the step (3) and cooling to room temperature;
(5) a third heat treatment; putting the titanium alloy forging into an effective working area of a resistance furnace which reaches a set heating temperature T for heating, wherein the heating temperature T is more than or equal to 480 ℃ and less than or equal to 500 ℃, and calculating the heat preservation time after the resistance furnace reaches the set heating temperature T again, wherein the heat preservation time is more than or equal to 240min and less than or equal to 480 min;
(6) discharging the titanium alloy forge piece subjected to the heat preservation in the step (5) and cooling to room temperature;
the heat treatment process is suitable for the heat treatment of near-beta type, metastable beta type and fully-stable beta type titanium alloys.
2. The heat treatment process for titanium alloy according to claim 1, wherein: the heating furnace is a resistance furnace.
3. The heat treatment process for titanium alloy according to claim 2, wherein: the temperature difference of the effective working area of the furnace temperature is controlled within +/-5 ℃.
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| CN111451423B (en) * | 2020-03-19 | 2022-04-19 | 中国船舶重工集团公司第七二五研究所 | Manufacturing process method of titanium alloy ultrahigh-pressure-resistant spherical shell blank |
| CN112662974A (en) * | 2020-12-18 | 2021-04-16 | 陕西宏远航空锻造有限责任公司 | Heat treatment method of TC21 alloy forging |
| CN113523012B (en) * | 2021-07-14 | 2022-05-03 | 山西太钢不锈钢股份有限公司 | Hot processing method of niobium-containing high-alloy austenitic heat-resistant stainless steel bar |
| CN114226616B (en) * | 2021-10-29 | 2023-03-14 | 中国航发北京航空材料研究院 | Isothermal forging method of TB17 titanium alloy |
| CN114959529A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section Ti6246 alloy forging |
| CN114959528A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section TC11 alloy forging |
| CN115058673B (en) * | 2022-06-21 | 2023-06-23 | 湖南湘投金天钛业科技股份有限公司 | Heat treatment method for regulating and controlling mechanical property matching and consistency of TC11 titanium alloy |
| CN115927987B (en) * | 2022-12-29 | 2024-07-26 | 北京钢研高纳科技股份有限公司 | Heat treatment method of high-temperature alloy disc shaft forge piece and manufactured disc shaft forge piece |
| CN116005090B (en) * | 2023-01-06 | 2024-08-20 | 中国航空制造技术研究院 | Heat treatment process for improving toughness of 1500 MPa-level titanium alloy |
| CN117324522B (en) * | 2023-09-28 | 2024-04-12 | 陕西鼎益科技有限公司 | Forging forming method for improving flaw detection level of titanium alloy bar |
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