CN114346141A - Multi-section hot working method for preparing weak alpha texture titanium alloy forging - Google Patents
Multi-section hot working method for preparing weak alpha texture titanium alloy forging Download PDFInfo
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- CN114346141A CN114346141A CN202210047355.0A CN202210047355A CN114346141A CN 114346141 A CN114346141 A CN 114346141A CN 202210047355 A CN202210047355 A CN 202210047355A CN 114346141 A CN114346141 A CN 114346141A
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- 238000005242 forging Methods 0.000 title claims abstract description 62
- 238000000034 method Methods 0.000 title claims abstract description 58
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 46
- 230000008569 process Effects 0.000 claims abstract description 26
- 238000001953 recrystallisation Methods 0.000 claims abstract description 17
- 230000015572 biosynthetic process Effects 0.000 claims abstract description 8
- 230000002195 synergetic effect Effects 0.000 claims abstract description 4
- 230000009466 transformation Effects 0.000 claims description 27
- 238000010438 heat treatment Methods 0.000 claims description 17
- 238000004321 preservation Methods 0.000 claims description 17
- 238000001816 cooling Methods 0.000 claims description 9
- 230000009467 reduction Effects 0.000 claims description 3
- 238000004088 simulation Methods 0.000 claims description 3
- 238000012360 testing method Methods 0.000 claims description 3
- 230000002401 inhibitory effect Effects 0.000 claims description 2
- 238000010791 quenching Methods 0.000 claims description 2
- 230000000171 quenching effect Effects 0.000 claims description 2
- 230000003313 weakening 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
- 239000013078 crystal Substances 0.000 description 9
- 238000012545 processing Methods 0.000 description 4
- 230000007704 transition Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 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
- 238000010274 multidirectional forging Methods 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
- 230000008859 change 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
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 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
- 230000001939 inductive effect Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
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- 230000035882 stress Effects 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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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
Abstract
The invention discloses a multistage hot working method for preparing a titanium alloy forging with a weak alpha texture, belongs to the field of titanium alloy hot working processes, and can solve the problem that a strong alpha texture is easy to form in a titanium alloy hot working process. The alpha texture of the titanium alloy is weakened by utilizing the synergistic effect of the beta texture and the beta recrystallization, the formation of an alpha macro area in the thermal deformation process is inhibited, and the uniformity of the structure is improved. The method can prepare the titanium alloy forging with the weak {11-20} alpha texture, the strength of the {11-20} alpha texture after 30% thermal deformation is 1.80mud, the maximum strength of the texture is about 5.82mud, and the texture strength is greatly reduced compared with that of the traditional process. The method can realize the precise regulation and control of the tissue texture, has simple process flow and is easy for actual production.
Description
Technical Field
The invention belongs to the field of titanium alloy hot working processes, and particularly relates to a multi-section hot working method for preparing a titanium alloy forging with weak alpha texture.
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 marine industry, the medical industry and the like. Among them, the aero-engine is one of the main applications of titanium alloy in the field of aerospace. The development of high-performance and light titanium alloy parts can improve the weight reduction effect and reliability of an aeroengine, and is one of important measurement standards for the advancement of a new generation of aircrafts.
The titanium alloy is mainly used for manufacturing parts of compressor blade discs, fan blades, sealing elements and the like in aeroengines, which serve as a medium-temperature region (about 400 ℃). The failure or the rupture of the parts of the aero-engine in use can cause serious consequences, so the load-bearing fatigue life of the titanium alloy is one of the important indexes influencing the service performance. However, titanium alloys are very prone to form strong α texture during hot forming, resulting in reduced texture uniformity, which in turn leads to anisotropic mechanical properties and a dramatic decrease in mechanical properties in certain loading directions. In addition, micro-scale and centimeter-scale microtexture, i.e., "macro-domains", in which the orientation of alpha-phase grains tends to be uniform may be formed during hot working. The macro-regions are not only present in the "bimodal structure" where the alpha phase ratio is large, but also in the "lamellar structure" where the alpha phase ratio is small. Because the macro area and the surrounding crystal grains generally have larger orientation difference, the stress is more easily concentrated in the macro area in the deformation process, and the probability of crack nucleation is increased. In addition, the orientation of all crystal grains in the macro-area is almost consistent, the obstruction effect of the crystal boundary is small, and the crack propagation speed is greatly improved. Therefore, the existence of the macro area greatly reduces the load-bearing fatigue life and the use reliability of titanium alloy parts, especially large-size forgings.
The alpha strong texture and macro-zone formation of the titanium alloy are generally considered to be related to the orientation relation and the variant selection in the phase transformation process, and the beta phase texture before hot processing can cause the formation of the macro-zone during hot processing. Therefore, in order to eliminate the macro-area hazard as much as possible, methods such as beta single-phase area one-way forging, multi-way forging, heat treatment and the like are usually adopted before the titanium alloy is subjected to hot working to fully and uniformly recrystallize and weaken the beta texture. However, due to the influence of strong dynamic recovery of the beta phase, inducing complete dynamic recrystallization of the beta phase generally requires a large deformation amount, has requirements on temperature and deformation rate, and is difficult to realize in actual large forgings. In addition, the steady-state recrystallization needs to strictly control the heat preservation time and temperature, and crystal grains are easy to grow due to overlong time in actual production. Multidirectional forging requires repeated machining, and the process is complicated.
The invention application with the publication number of CN 112676503A provides a forging processing method of a TC32 titanium alloy large-specification bar. The method is characterized in that the method comprises the steps of performing recrystallization homogenization forging after cogging forging, then forging below beta transition temperature, and finally forging a finished product. The titanium alloy is subjected to static recrystallization in cogging forging to realize rapid refinement and homogenization of the structure. However, the static recrystallization requires strict control of the holding time and temperature, and the crystal grains are likely to grow due to too long time in actual production. And the method needs to be heated and cooled for many times, and forging is carried out for many times at different temperatures, so that the process is complex. At the same time, the problems of strong alpha texture and macro-zone cannot be solved. The invention application with the publication number of CN 105728617A provides a Ti60 titanium alloy isothermal forging and heat treatment method, which comprises the steps of preparing a cake blank or a ring blank from an ingot at a temperature of 30-50 ℃ below the beta transition temperature of 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 to finally prepare the forging. Although the method can prepare the forged piece meeting the strength and elongation indexes, the forging needs to be carried out for multiple times below the beta transition temperature, the process is complex, and alpha-phase strong texture and macro-area are easily formed, so that the fatigue performance is reduced. The invention application with the publication number of CN 103882358A provides a forging and heat treatment method of TC4 titanium alloy. Forging the blank at 30-50 ℃ below the TC4 titanium alloy beta transformation point to prepare a primary forging blank; then heating the primary forging stock to the beta transformation point and forging the primary forging stock to obtain a middle-grade forging stock at the temperature of between 10 and 20 ℃; and finally, carrying out solid solution treatment on the intermediate forging stock at 950-980 ℃ and aging at high temperature of 650-700 ℃ to obtain the final forging. The method can meet the requirements of strength and plasticity, but needs to be heated and cooled for many times and forged for many 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 in the prior art, the invention provides a multi-section continuous hot working method for preparing a titanium alloy forging with weak alpha texture, and solves the problem that the titanium alloy is easy to form the strong alpha texture in the hot working process. The method has simple and easily controlled hot processing process, can produce the titanium alloy forging with good tissue uniformity, and is suitable for industrial production.
The invention adopts the following technical scheme: pre-deforming a preset beta texture above a beta phase transformation point, pre-deforming a preset beta sub-dynamic recrystallization grain through heat treatment, finally forging below the beta phase transformation point, weakening the alpha texture of the titanium alloy through the synergistic effect of the beta texture and the beta recrystallization, inhibiting the formation of an alpha macro area in the thermal deformation process and improving the uniformity of the texture; the method specifically comprises the following steps:
firstly, carrying out thermal deformation by adopting a thermal simulation testing machine to preset a beta deformation texture, wherein the thermal deformation is carried out under a vacuum condition, firstly, heating a titanium alloy sample to be 30 ℃ above a beta transformation point, heating at a speed of 10 ℃/s, heating to a specified temperature, and then, carrying out heat preservation for 10min to obtain a uniform structure;
performing thermal deformation after heat preservation, and performing pre-deformation on the titanium alloy at the temperature of 20-50 ℃ above a beta transformation point to introduce beta grains with specific (001) orientation, wherein the deformation amount is 10-30%, and the deformation rate is controlled at 0.01/s-0.1/s;
secondly, after predeformation, continuously preserving heat for 2-20s at the temperature of 30-50 ℃ above the beta transformation point to induce sub-dynamic recrystallization and refine grains;
thirdly, cooling the forging to 50-150 ℃ below the beta transformation point for heat preservation, wherein the cooling rate needs to be controlled to be 5-10 ℃/s, and the heat preservation time needs to be controlled to be 5-10 s so as to ensure that the alpha phase cannot be separated out in the cooling and heat preservation processes;
fourthly, forging at the temperature of 50-180 ℃ below the beta transformation point, wherein the forging deformation is 10-30%, the deformation rate is controlled at 0.01/s-0.1/s, and finally, air cooling or quenching the forged piece to the room temperature.
The invention has the following beneficial effects:
1. most conventional wisdom holds that beta phase texture prior to hot working can lead to the formation of "macro-domains". The method adopts a reverse idea, skillfully utilizes the beta-phase texture before hot working, introduces the (001) beta texture through single forging, and does not need repeated temperature rise and temperature reduction. The invention avoids the complicated 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 hot processing flow of the titanium alloy.
2. The invention presets beta sub-dynamic recrystallization grains through the heat treatment after the forging on the beta phase transformation point, can obviously play a role in grain refinement, and further homogenizes the forging structure. Compared with the traditional process which needs multiple times of heating and large deformation amount forging in a single-phase region to introduce dynamic recrystallization grains, the process flow of the invention is simplified, and the effect of improving the uniformity of the structure can be achieved.
3. The method can obviously weaken alpha texture, inhibit macro areas and improve the uniformity of the forging structure. Under the condition of the same total deformation and deformation rate, compared with the forged piece prepared by the traditional two-phase region forging process, the forged piece prepared by the process has the advantages that the {11-20} alpha texture strength is obviously reduced, the area of a macro region 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 double-phase titanium alloys, and has universality.
Drawings
FIG. 1 is a process flow diagram of the present invention.
FIG. 2 is an alpha-phase antipole diagram (deformation temperature 150 ℃ below the beta-transformation point, deformation amount 30% and deformation rate 0.01/s) of the central region of a titanium alloy forging prepared by the traditional two-phase region hot working method along the forging direction.
FIG. 3 is an alpha phase reversal in the forging direction for the center region of a forging produced in accordance with example 1 of the present invention.
Detailed Description
The invention will be further illustrated by the following examples
Example 1
Step one, preparing original titanium alloy
In the embodiment, the alpha + beta titanium alloy TC19 is selected for hot working, and the phase transition temperature is about 950 ℃. The microstructure of the original titanium alloy is a two-state structure and does not have obvious alpha texture. Cutting an original titanium alloy ingot or bar into cylindrical samples, polishing the surfaces of the cylindrical samples to be bright, and cleaning the cylindrical samples by using organic solvents such as absolute ethyl alcohol and acetone.
Step two, presetting beta deformation texture
And (3) performing thermal deformation by using a thermal simulation testing machine to preset a beta deformation texture, wherein the thermal deformation is performed under a vacuum condition. Firstly, heating a titanium alloy sample to 30 ℃ above a beta transformation point, wherein the heating rate is 10 ℃/s, and after heating to a specified temperature, keeping the temperature for 10 minutes to obtain a uniform structure. And (3) carrying out thermal deformation after heat preservation, wherein the deformation temperature is 30 ℃ above the beta transformation point, the deformation rate is 0.01/s, and the deformation amount is 15%. And (5) directly performing the third step without reducing the temperature after thermal deformation.
Step three, presetting beta sub-dynamic recrystallization
After forging above the beta transus point, heat treatment is carried out at 30 ℃ above the beta transus point to introduce beta sub-dynamic recrystallization grains. In order to avoid the growth of beta-phase crystal grains and the generation of stable recrystallized crystal grains caused by overlong heat preservation time and further destroy a beta-phase weak (001) texture preset at the early stage, the heat preservation temperature is 30 ℃ above the beta-phase transformation point, and the heat preservation time is 2 s.
Step four, forging the conventional two-phase region
After heat treatment, the temperature is reduced to be below a beta transformation point, the temperature reduction rate needs to be controlled at 10 ℃/s so as to avoid introducing a martensite phase at an excessively high rate, and the heat preservation time needs to be controlled at 5s so as to avoid precipitation of an alpha phase caused by excessively long time. Then, thermal deformation is carried out, the deformation temperature is 150 ℃ below the beta transformation point, the deformation amount is 30%, and the deformation rate is 0.01/s. Finally, the sample is quenched to room temperature with helium.
As a contrast, the titanium alloy forging is prepared by adopting the traditional two-phase region hot working method, the deformation temperature is 150 ℃ below the beta transformation point, the deformation amount is 30%, and the deformation rate is 0.01/s. FIG. 2 is an alpha phase reversal diagram of the central region of the forging along the forging direction, and it can be seen that the titanium alloy forging prepared by the traditional hot working method has a strong {11-20} alpha texture, and the texture strength is about 8.30 mud. FIG. 3 is a plot of the α phase reversal in the forging direction for the central region of a forging produced using inventive example 1, with {11-20} α texture strength of about 1.80mud and maximum texture strength of about 5.82 mud. In conclusion, the method can effectively inhibit the formation of the strong alpha texture and improve the uniformity of the texture. The mechanism is that the preset beta texture can optimize the crystal grain orientation of an alpha precipitated phase in the thermal deformation process, further change the starting condition of an alpha sliding system, promote the starting of a non-basal plane sliding system, form a new alpha deformation texture, simultaneously, beta recrystallization can play a role in refining the crystal grains, and the synergistic effect of the alpha texture and the alpha texture finally weakens the formation of a strong alpha texture.
Example 2
The present embodiment differs from embodiment 1 in that:
in the second step, the temperature rise speed is 10 ℃/s, the deformation temperature is 30 ℃ above the beta transformation point, the deformation rate is 0.01/s, and the deformation amount is 30%. The rest is the same as in example 1.
Example 3
The present embodiment differs from embodiment 1 in that:
in the third step, the heat preservation temperature is 30 ℃ above the beta transformation point, and the heat preservation time is 20 s.
The rest is the same as in example 1.
Example 4
The present embodiment differs from embodiment 1 in that:
in the fourth step, the deformation temperature is 80 ℃ below the beta transformation point, the deformation amount is 30 percent, and the deformation rate is controlled to be 0.01/s. Finally, the sample is cooled to room temperature by air.
The rest is the same as in example 1.
Claims (4)
1. A multi-section hot working method for preparing a titanium alloy forging with weak alpha texture is characterized by comprising the following steps: pre-deforming a preset beta texture above a beta phase transformation point, pre-deforming a preset beta sub-dynamic recrystallization grain through heat treatment, finally forging below the beta phase transformation point, weakening the alpha texture of the titanium alloy through the synergistic effect of the beta texture and the beta recrystallization, inhibiting the formation of an alpha macro area in the thermal deformation process and improving the uniformity of the texture; the method specifically comprises the following steps:
firstly, a thermal simulation testing machine is adopted for thermal deformation to preset a beta deformation texture, firstly, a titanium alloy sample is heated to 30 ℃ above a beta transformation point, and is heated to a specified temperature and then is kept warm for 10min to obtain a uniform structure;
performing thermal deformation after heat preservation, and performing pre-deformation on the titanium alloy at the temperature of 20-50 ℃ above a beta transformation point to introduce beta grains with specific (001) orientation, wherein the deformation amount is 10-30%, and the deformation rate is controlled at 0.01/s-0.1/s;
secondly, after predeformation, continuously preserving heat for 2-20s at the temperature of 30-50 ℃ above the beta transformation point to induce sub-dynamic recrystallization and refine grains;
thirdly, cooling the forging to 50-150 ℃ below the beta transformation point for heat preservation, wherein the heat preservation time needs to be controlled within 5-10 s to ensure that the alpha phase cannot be separated out in the processes of cooling and heat preservation;
fourthly, forging at the temperature of 50-180 ℃ below the beta transformation point, wherein the forging deformation amount is 10-30%, the deformation rate is controlled at 0.01/s-0.1/s, and finally cooling the forging to room temperature.
2. The multi-stage hot working method for preparing the titanium alloy forging with the weak alpha texture as claimed in claim 1, wherein the method comprises the following steps: the first step of thermal deformation is carried out under vacuum condition, and the temperature rise speed is 10 ℃/s.
3. The multi-stage hot working method for preparing the titanium alloy forging with the weak alpha texture as claimed in claim 1, wherein the method comprises the following steps: in the third step, the temperature reduction rate needs to be controlled at 5-10 ℃/s.
4. The multi-stage hot working method for preparing the titanium alloy forging with the weak alpha texture as claimed in 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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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112642976A (en) * | 2020-12-01 | 2021-04-13 | 太原理工大学 | Two-stage non-isothermal forging method for controlling titanium alloy beta forging texture |
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| JPH06212378A (en) * | 1993-01-11 | 1994-08-02 | Daido Steel Co Ltd | Treatment of beta type titanium alloy hot formed product |
| CA2738007A1 (en) * | 2008-09-22 | 2010-03-25 | Snecma | Method for manufacturing a titanium part through initial .beta. forging |
| CN110396656A (en) * | 2019-08-21 | 2019-11-01 | 太原理工大学 | A kind of composite reinforcement process of superhigh intensity TB8 titanium alloy |
| CN112642976A (en) * | 2020-12-01 | 2021-04-13 | 太原理工大学 | Two-stage non-isothermal forging method for controlling titanium alloy beta forging texture |
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- 2022-01-17 CN CN202210047355.0A patent/CN114346141A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06212378A (en) * | 1993-01-11 | 1994-08-02 | Daido Steel Co Ltd | Treatment of beta type titanium alloy hot formed product |
| CA2738007A1 (en) * | 2008-09-22 | 2010-03-25 | Snecma | Method for manufacturing a titanium part through initial .beta. forging |
| CN110396656A (en) * | 2019-08-21 | 2019-11-01 | 太原理工大学 | A kind of composite reinforcement process of superhigh intensity TB8 titanium alloy |
| CN112642976A (en) * | 2020-12-01 | 2021-04-13 | 太原理工大学 | Two-stage non-isothermal forging method for controlling titanium alloy beta forging texture |
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| Title |
|---|
| LIN PENG;TANG TINGTING; CHI CHENGZHONG;ZHANG SHUZHI; ZHANG CHANGJIANG: "Dynamic Globularization Behavior of O-phase Lamellae in Ti-22AI-25Nb (at%) Alloy during Deformation at Elevated Temperatures", RARE METAL MATERIALS AND ENGINEERING, vol. 47, no. 2, pages 416 - 422, XP085409683, DOI: 10.1016/S1875-5372(18)30081-X * |
| 张长江，林鹏等: "热处理对锻态2.5%(TiB+TiC)/Ti复合材料组织与性能的影响", 稀有金属材料与工程, vol. 45, no. 12, pages 3172 - 3176 * |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN112642976A (en) * | 2020-12-01 | 2021-04-13 | 太原理工大学 | Two-stage non-isothermal forging method for controlling titanium alloy beta forging texture |
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