CN114346141B - Multistage hot processing method for preparing weak alpha texture titanium alloy forging - Google Patents
Multistage hot processing method for preparing weak alpha texture titanium alloy forging Download PDFInfo
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- 238000005242 forging Methods 0.000 title claims abstract description 57
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 44
- 238000003672 processing method Methods 0.000 title description 4
- 238000000034 method Methods 0.000 claims abstract description 44
- 230000008569 process Effects 0.000 claims abstract description 23
- 238000001953 recrystallisation Methods 0.000 claims abstract description 16
- 230000015572 biosynthetic process Effects 0.000 claims abstract description 8
- 230000002195 synergetic effect Effects 0.000 claims abstract description 4
- 230000007704 transition Effects 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 16
- 238000004321 preservation Methods 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 11
- 230000009466 transformation Effects 0.000 claims description 9
- 230000002401 inhibitory effect Effects 0.000 claims description 3
- 238000010791 quenching Methods 0.000 claims description 3
- 230000000171 quenching effect Effects 0.000 claims description 3
- 238000004088 simulation Methods 0.000 claims description 3
- 230000003313 weakening effect Effects 0.000 claims description 3
- 230000000630 rising effect Effects 0.000 claims description 2
- 230000002829 reductive effect Effects 0.000 abstract description 6
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 230000000694 effects Effects 0.000 description 4
- 238000010274 multidirectional forging Methods 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 102000001008 Macro domains Human genes 0.000 description 2
- 108050007982 Macro domains Proteins 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 238000010275 isothermal forging Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 229910001040 Beta-titanium Inorganic materials 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000002902 bimodal effect Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 239000003960 organic solvent Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
Abstract
A multistage hot working method for preparing titanium alloy forgings with weak alpha texture belongs to the field of titanium alloy hot working technology, and can solve the problem that titanium alloy hot working process is easy to be carried out into strong alpha texture. The alpha texture of the titanium alloy is weakened by utilizing the synergistic effect of beta texture and beta recrystallization, the formation of an alpha macro region in the thermal deformation process is inhibited, and the tissue uniformity is improved. The invention can prepare the titanium alloy forging with weak {11-20} alpha texture, the {11-20} alpha texture strength is 1.80mud after 30% thermal deformation, the maximum texture strength is about 5.82mud, and compared with the traditional process, the texture strength is greatly reduced. The invention can realize the accurate regulation and control of the tissue texture, has simple process flow and is easy for practical production.
Description
Technical Field
The invention belongs to the field of titanium alloy hot working processes, and particularly relates to a multistage hot working method for preparing a weak alpha texture titanium alloy forging.
Background
The titanium alloy has the advantages of high specific strength, excellent corrosion resistance, good high-temperature performance, good biocompatibility and the like, and is widely applied to the aerospace field, the automobile industry, the ocean industry, the medical industry and the like. Among them, aeroengines are one of the main applications of titanium alloys in the aerospace field. The weight reduction effect and reliability of the aeroengine can be improved by developing high-performance and light titanium alloy parts.
Titanium alloys are mainly used to manufacture components of aircraft engines that are in service in medium temperature regions (about 400 ℃), such as compressor blades, fan blades, seals, and the like. The failure or fracture of the aeroengine parts in use can cause serious consequences, so that the load-holding fatigue life of the titanium alloy is one of important indexes affecting service performance. However, titanium alloys are extremely prone to forming strong alpha textures during hot forming, resulting in reduced tissue uniformity, leading to anisotropic mechanical properties and a dramatic decrease in mechanical properties in certain loading directions. In addition, micro-scale, centimeter-scale microtexture, i.e., "macros," may be formed during thermal processing where the alpha phase grain orientation tends to be consistent. The macro-regions will occur not only in "bi-modal tissue" where the a-phase ratio is large, but also in "lamellar tissue" where the a-phase ratio is small. Because the macro region and surrounding grains generally have larger orientation difference, stress is more easily concentrated in the macro region in the deformation process, and the probability of crack nucleation is increased. In addition, the orientation of all grains in the macro region is almost uniform, the blocking effect of grain boundaries is small, and the rate of crack propagation is greatly improved. Therefore, the existence of the macro region greatly reduces the load-holding fatigue life and the use reliability of titanium alloy parts, especially large-size forgings.
It is believed that the alpha-strong texture of the titanium alloy and the formation of macro-domains is related to the orientation relationship and the selection of variants during phase transformation, and that the beta-phase texture prior to hot working results in the formation of macro-domains during hot working. Therefore, in order to eliminate the harm of the macro area as much as possible, the method of unidirectional forging, multidirectional forging, heat treatment and the like of the beta single-phase area is often adopted before the titanium alloy is thermally processed to enable the beta single-phase area to be fully and uniformly recrystallized and weaken the beta texture. However, due to the effect of the strong dynamic recovery of the beta phase, the induction of the complete dynamic recrystallization of the beta phase generally requires a large deformation amount, and has requirements on temperature and deformation rate, which is difficult to realize in practical large forgings. In addition, the stable recrystallization requires strict control of the heat preservation time and temperature, and the grain growth is easily caused by overlong time in actual production. The multidirectional forging requires repeated processing for a plurality of times, and the working procedure is complex.
The invention application of publication No. CN 112676503A proposes a forging processing method of TC32 titanium alloy large-size bars. The forging method is characterized in that after cogging forging, recrystallization homogenization forging is carried out, then forging is carried out below beta transition temperature, and finally the forging is carried out on the finished product. In the cogging forging, the titanium alloy is subjected to static recrystallization to realize rapid refinement and homogenization of the structure. However, static recrystallization requires strict control of the holding time and temperature, and grain growth is easily caused by too long time in practical production. In addition, the method needs multiple times of temperature rise and reduction, multiple times of forging at different temperatures, and the process is complex. And the problems of strong alpha texture and macro region cannot be solved. The publication No. CN 105728617A discloses an isothermal forging and heat treatment method of Ti60 titanium alloy, which comprises the steps of preparing an ingot into a cake blank or a ring blank at the temperature of 30-50 ℃ below the beta transition temperature of the Ti60 titanium alloy; and carrying out isothermal forging on the cake blank or the ring blank on an oil press, and finally carrying out solid solution aging treatment on the forging piece to finally prepare the forging piece. Although the method can prepare the forge piece meeting the indexes of strength and elongation, the forging needs to be forged for many times below the beta transformation temperature, the process is complex, and the alpha phase strong texture and macro region are extremely easy to form, so that the fatigue performance is reduced. The publication No. CN 103882358A discloses a forging and heat treatment method of TC4 titanium alloy. Firstly forging the blank at the temperature of 30-50 ℃ below the TC4 titanium alloy beta transformation point to prepare a primary forging stock; then heating the primary forging stock to the beta transformation point of 10-20 ℃ for forging to prepare a medium-grade forging stock; finally, carrying out solid solution at 950-980 ℃ and high-temperature aging at 650-700 ℃ on the intermediate forging stock to obtain the final forging. The method can meet the requirements of strength and plasticity, but also needs to increase and decrease temperature for multiple times and forge for multiple times at different temperatures, and can not solve the problems of strong texture and macro area caused by thermal deformation.
Disclosure of Invention
Aiming at the defects existing in the prior art, the invention provides a multistage continuous hot processing method for preparing a titanium alloy forging with weak alpha texture, which solves the problem that the titanium alloy hot processing process is easy to implement into strong alpha texture. The method has the advantages of simple and easily controlled hot working process, capability of producing titanium alloy forgings with good tissue uniformity, and suitability for industrial production.
The invention adopts the following technical scheme: presetting beta texture by pre-deforming above a beta phase transition point, presetting beta sub-dynamic recrystallization grains by heat treatment, forging below the beta phase transition point, weakening alpha texture of the titanium alloy by synergistic effect of the beta texture and beta recrystallization, inhibiting formation of an alpha macro region in the thermal deformation process and improving tissue uniformity; the method specifically comprises the following steps:
Firstly, carrying out thermal deformation by adopting a thermal simulation tester to preset beta deformation texture, wherein the thermal deformation is carried out under a vacuum condition, firstly, heating a titanium alloy sample to 30 ℃ above a beta phase transition point, wherein the heating speed is 10 ℃/s, and after heating to a specified temperature, preserving heat for 10min to obtain a uniform tissue;
Carrying out thermal deformation after heat preservation, and pre-deforming the titanium alloy at 20-50 ℃ above the beta transformation point to introduce (001) -oriented beta grains, wherein the deformation amount is 10-30%, and the deformation rate is controlled to be 0.01-0.1/s;
Secondly, keeping the temperature at 30-50 ℃ for 2-20 s above the beta phase transition point after pre-deformation to induce sub-dynamic recrystallization and refine grains;
Thirdly, cooling the forging to 50-150 ℃ below the beta phase transition point for heat preservation, wherein the cooling rate is controlled to be 5-10 ℃/s, and the heat preservation time is controlled to be 5-10 s so as to ensure that alpha phase is not separated out in the cooling and heat preservation process;
And fourthly, forging at 50-180 ℃ below the beta phase transition point, wherein the forging deformation amount is 10-30%, the deformation rate is controlled to be 0.01/s-0.1/s, and finally air cooling or quenching the forging to room temperature.
The beneficial effects of the invention are as follows:
1. Most conventional wisdom holds that β -phase texture prior to thermal processing results in the formation of "macros". The invention adopts a reverse thought to skillfully utilize the beta-phase texture before hot working, introduces the (001) beta-phase texture through single forging, and does not need repeated temperature rise and drop. The invention avoids complex procedures of repeated unidirectional forging, multidirectional forging, heat treatment and the like adopted in the traditional process for eliminating the beta texture, and greatly simplifies the titanium alloy heat processing flow.
2. According to the invention, the beta sub-dynamic recrystallization grains are preset through heat treatment after forging of beta phase transformation points, so that the effect of grain refinement can be obviously achieved, and the forging structure is further homogenized. Compared with the traditional process, the invention has the advantages that the process flow is simplified, and the effect of improving the structural uniformity can be also achieved.
3. The invention can play the obvious roles of weakening alpha texture, inhibiting macro area and improving the uniformity of forging tissue. Under the condition that the total deformation and the deformation rate are the same, compared with the forge piece prepared by the traditional two-phase region forging process, the forge piece prepared by the process has the advantages that the {11-20} alpha texture strength is obviously reduced, the macro region area is obviously reduced, and the structure is more uniform.
4. The process provided by the invention can be applied to the hot working process of various dual-phase titanium alloys, and has universality.
Drawings
FIG. 1 is a process flow diagram of the present invention.
FIG. 2 is an alpha opposite pole plot (deformation temperature 150 ℃ below beta transus, deformation amount 30% and deformation rate 0.01/s) of a titanium alloy forging center area along the forging direction prepared by a conventional two-phase zone hot working method.
FIG. 3 is an opposite pole view of the center region of the forging prepared in example 1 of the present invention along the forging direction.
Detailed Description
The invention will be further illustrated by the following examples
Example 1
Step one, original titanium alloy preparation work
In this example, the α+β titanium alloy TC19 was selected for hot working, with a transformation temperature of about 950 ℃. The microstructure of the original titanium alloy is a bimodal structure and does not have obvious alpha texture. Cutting an original titanium alloy cast ingot or bar into a cylindrical sample, polishing the surface to be bright, and cleaning by using an organic solvent such as absolute ethyl alcohol, acetone and the like.
Step two, presetting beta deformation texture
Thermal deformation was performed using a thermal simulation tester to preset the beta-deformation texture, wherein the thermal deformation was performed under vacuum conditions. First, the titanium alloy sample was heated to 30 ℃ above the beta transus point at a heating rate of 10 ℃/s, and then incubated for 10 minutes after the temperature was raised to the specified temperature to obtain a uniform structure. Thermal deformation is carried out after heat preservation, the deformation temperature is 30 ℃ above the beta phase transition point, the deformation rate is 0.01/s, and the deformation quantity is 15%. And (3) directly performing the third step without reducing the temperature after thermal deformation.
Step three, presetting beta sub-dynamic recrystallization
Forging above the beta transus followed by heat treatment at 30 ℃ above the beta transus to introduce beta sub-dynamic recrystallized grains. In order to avoid the growth of beta-phase grains and the generation of stable recrystallized grains caused by overlong heat preservation time, and further destroy the pre-set beta-phase weak (001) texture, the heat preservation temperature is 30 ℃ above the beta phase transition point, and the heat preservation time is 2s.
Step four, conventional two-phase zone forging
The temperature is reduced below the beta phase transition point after heat treatment, the temperature reduction rate is controlled to be 10 ℃/s so as to avoid introducing a martensite phase at an excessive speed, and the heat preservation time is controlled to be 5s so as to avoid precipitating an alpha phase due to the excessive time. And then carrying out thermal deformation, wherein the deformation temperature is 150 ℃ below the beta phase transition point, the deformation amount is 30%, and the deformation rate is 0.01/s. Finally, quenching the sample with helium to room temperature.
As a comparison, the titanium alloy forging is prepared by adopting a traditional two-phase zone hot working method, the deformation temperature is 150 ℃ below the beta phase transition point, the deformation amount is 30%, and the deformation rate is 0.01/s. FIG. 2 is an opposite pole view of the forging center along the forging direction, showing that the titanium alloy forging prepared by the conventional hot working method has a stronger {11-20} α texture with a texture strength of about 8.30mud. FIG. 3 is an opposite pole view of the center region of a forging prepared in example 1 of the present invention along the forging direction with a {11-20} α texture strength of about 1.80mud and a maximum texture strength of about 5.82mud. In conclusion, the method can effectively inhibit the formation of strong alpha texture and improve the uniformity of the tissue. The mechanism is that the preset beta texture can optimize the grain orientation of alpha precipitated phases in the thermal deformation process, so that the starting condition of an alpha sliding system is changed, the starting of a non-basal plane sliding system is promoted, a new alpha deformation texture is formed, meanwhile, the beta recrystallization can play a role in refining grains, and the formation of the strong alpha texture is finally weakened under the synergistic effect of the beta recrystallization and the alpha precipitation.
Example 2
The present embodiment differs from example 1 in that:
in the second step, the temperature rising speed is 10 ℃/s, the deformation temperature is 30 ℃ above the beta phase transition point, the deformation speed is 0.01/s, and the deformation quantity is 30%. The remainder was the same as in example 1.
Example 3
The present embodiment differs from example 1 in that:
in the third step, the heat preservation temperature is 30 ℃ above the beta phase transition point, and the heat preservation time is 20s.
The remainder was the same as in example 1.
Example 4
The present embodiment differs from example 1 in that:
In the fourth step, the deformation temperature is 80 ℃ below the beta phase transition point, the deformation amount is 30%, and the deformation rate is controlled to be 0.01/s. And finally, air cooling the sample to room temperature.
The remainder was the same as in example 1.
Claims (2)
1. A multistage hot working method for preparing a titanium alloy forging with weak alpha texture is characterized by comprising the following steps of: presetting beta texture by pre-deforming above a beta phase transition point, presetting beta sub-dynamic recrystallization grains by heat treatment, forging below the beta phase transition point, weakening alpha texture of the titanium alloy by synergistic effect of the beta texture and beta recrystallization, inhibiting formation of an alpha macro region in the thermal deformation process and improving tissue uniformity; the method specifically comprises the following steps:
Firstly, adopting a thermal simulation tester to perform thermal deformation to preset beta deformation texture, firstly, heating a titanium alloy sample to 30 ℃ above a beta transformation point, heating to a specified temperature, and then preserving heat for 10 minutes to obtain a uniform structure;
Carrying out thermal deformation after heat preservation, and pre-deforming the titanium alloy at 20-50 ℃ above the beta transformation point to introduce (001) -oriented beta grains, wherein the deformation amount is 10-30%, and the deformation rate is controlled to be 0.01-0.1/s;
Secondly, keeping the temperature at 30-50 ℃ for 2-20 s above the beta phase transition point after pre-deformation to induce sub-dynamic recrystallization and refine grains;
Thirdly, cooling the forging to 50-150 ℃ below the beta phase transition point for heat preservation, wherein the heat preservation time is controlled to be 5-10 s to ensure that alpha phase is not separated out in the cooling and heat preservation process;
Fourthly, forging at the temperature of 50-180 ℃ below the beta phase transition point, wherein the forging deformation amount is 10-30%, the deformation rate is controlled to be 0.01/s-0.1/s, and finally cooling the forging to room temperature;
the first step of thermal deformation is carried out under vacuum condition, and the temperature rising speed is 10 ℃/s;
and in the third step, the cooling rate is controlled to be 5 ℃/s-10 ℃/s.
2. The multi-stage hot working method for preparing a titanium alloy forging with weak alpha texture according to claim 1, wherein the method comprises the following steps: and in the fourth step, the cooling mode is air cooling or quenching.
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