CN116463569B - Method for regulating orientation of titanium-aluminum alloy sheet layer through strong magnetic field heat treatment - Google Patents
Method for regulating orientation of titanium-aluminum alloy sheet layer through strong magnetic field heat treatment Download PDFInfo
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 72
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 title claims abstract description 55
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 54
- 238000000034 method Methods 0.000 title claims abstract description 32
- 230000001105 regulatory effect Effects 0.000 title claims abstract description 14
- 230000001276 controlling effect Effects 0.000 claims abstract description 17
- 238000001816 cooling Methods 0.000 claims abstract description 11
- 229910045601 alloy Inorganic materials 0.000 claims description 29
- 239000000956 alloy Substances 0.000 claims description 29
- 239000013078 crystal Substances 0.000 claims description 13
- 238000004321 preservation Methods 0.000 claims description 9
- 230000008569 process Effects 0.000 abstract description 11
- 230000005415 magnetization Effects 0.000 abstract description 4
- 239000012071 phase Substances 0.000 description 23
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 15
- 239000003792 electrolyte Substances 0.000 description 15
- 238000005498 polishing Methods 0.000 description 15
- LRHPLDYGYMQRHN-UHFFFAOYSA-N N-Butanol Chemical compound CCCCO LRHPLDYGYMQRHN-UHFFFAOYSA-N 0.000 description 10
- VLTRZXGMWDSKGL-UHFFFAOYSA-N perchloric acid Chemical compound OCl(=O)(=O)=O VLTRZXGMWDSKGL-UHFFFAOYSA-N 0.000 description 10
- 238000005520 cutting process Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 229910010038 TiAl Inorganic materials 0.000 description 6
- 238000007711 solidification Methods 0.000 description 6
- 230000008023 solidification Effects 0.000 description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 5
- 244000137852 Petrea volubilis Species 0.000 description 5
- 238000009826 distribution Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000005406 washing Methods 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 230000000930 thermomechanical effect Effects 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000001808 coupling effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000005426 magnetic field effect Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000007781 pre-processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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- 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
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- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
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- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Hard Magnetic Materials (AREA)
Abstract
The invention provides a method for regulating and controlling the orientation of a titanium-aluminum alloy sheet layer by heat treatment of a strong magnetic field, which comprises the following steps: after the set magnetic field strength is reached, placing the titanium-aluminum alloy sample in the central position in the strong magnetic field heat treatment furnace, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum; wherein the set value of the magnetic field intensity is 10T; heating from room temperature to a set temperature at a constant rate, keeping the temperature for 20 min-15 h, performing strong magnetic field heat treatment, and heating and cooling the sample along with the furnace; wherein the heat treatment interval is above the T α temperature of the titanium-aluminum alloy; after the strong magnetic field heat treatment, the sheet group with a certain orientation of the titanium-aluminum alloy preferentially grows, so that the purpose of adjusting and controlling the orientation of the titanium-aluminum alloy sheet is achieved. In the invention, a strong magnetic field is introduced into the heat treatment process (the temperature is higher than T α) of the titanium-aluminum alloy, and additional magnetization energy and driving force are applied by using the strong magnetic field, so that the lamellar clusters with a certain orientation preferentially grow.
Description
Technical Field
The invention relates to the technical field of titanium-aluminum-based intermetallic compounds, in particular to a method for regulating and controlling orientation of a titanium-aluminum alloy sheet layer through heat treatment of a strong magnetic field.
Background
The titanium-aluminum alloy has the characteristics of low density, high specific strength, excellent high-temperature oxidation resistance, creep resistance and the like, and is considered as an ideal candidate material for replacing nickel-based superalloy for service at the temperature range of 650-900 ℃ for hot-end components such as aerospace vehicles and the like. Particularly, when the (alpha 2 and gamma) lamellar orientations are consistent, the comprehensive high-temperature mechanical properties of the titanium-aluminum alloy are more excellent, and particularly, the crack initiation/expansion and creep deformation capabilities of the alloy are improved, so that the service temperature of the alloy is improved, and the titanium-aluminum alloy has advantages in the aspects of engine blades and the like. However, the difficulty in controlling the sheet orientation of the titanium-aluminum alloy is that two consecutive solid state phase transitions β→α and α→α 2 +γ are involved after solidification, since the titanium-aluminum alloy sheet orientation is ultimately formed by the α→α 2 +γ phase transition. Therefore, it is difficult to achieve the purpose of controlling the orientation of the flakes using conventional solidification and heat treatment methods.
In recent years, scientific researchers at home and abroad have proposed many methods for this problem and have conducted a great deal of research including seed crystal method, control of solidification path, thermo-mechanical processing, and the like. The seed crystal method is to select titanium aluminum alloy with specific components as seed crystal, the high temperature alpha phase of the parent metal grows along the non-preferential direction <11-20> under the seeding action of the seed crystal, and the orientation of the sheet layer in the final solidification structure is consistent with the growth direction according to the following bit relation when the gamma phase is precipitated in the alpha phase. The key of the seed crystal method is the preparation of the seed crystal, but the titanium-aluminum alloy which satisfies the seed crystal preparation at present is less, and the Ti-Al-Si system is mainly used, so that the application of the seed crystal method is greatly limited. The key of the method for controlling the solidification path to regulate and control the orientation of the lamellar is to control the first precipitated phase to be the full beta phase in the solidification process. However, once alpha grains are directly nucleated and grow up from the liquid phase due to enrichment of solute elements in the process, the alpha phase is no longer controlled by beta phase orientation, and the purpose of controlling lamellar orientation cannot be achieved. On the basis, chen et al found that the degree of mismatching of a 0-degree lamellar orientation interface is lower than 45-degree lamellar orientation, and therefore proposed that directional heat treatment controls nucleation driving force of alpha phase to obtain PST TiAl single crystals parallel to the growth direction, room temperature plasticity and yield strength of the PST TiAl single crystals reach 6.9% and 708 MPa respectively, and tensile strength and creep resistance at 900 ℃ are also greatly improved. In addition to the above method for controlling lamellar orientation ,"EffecT of aged-heaT TreaTmenT on microsTrucTure of α exTruded TiAl alloy","Lamellar orienTaTion conTrol in TiAl base alloys by a Two-sTep compression process aT high TemperaTure" proposes a thermo-mechanical processing in the alpha single-phase region or the (alpha + beta) two-phase region, promoting the selection of variants of the alpha phase and the formation of deformed textures, combined with subsequent processes, obtaining stable, fine and uniformly oriented lamellar structures. However, the titanium-aluminum alloy has low room temperature plasticity, so that defects such as holes and cracks are easy to form in the hot working process. Therefore, it is desirable to find a simple and efficient method for regulating the orientation of the lamellae.
Disclosure of Invention
In the invention, a strong magnetic field is introduced into the titanium-aluminum alloy heat treatment process (the temperature is higher than T α), and additional magnetization energy and driving force are applied by using the strong magnetic field, so that the lamellar clusters in a certain orientation preferentially grow, which shows that the strong magnetic field heat treatment can effectively regulate and control the orientation of the titanium-aluminum alloy lamellar, and has important significance for regulating and controlling the orientation of the titanium-aluminum alloy lamellar.
Specifically, the invention is realized by adopting the following technical scheme:
the invention provides a method for regulating and controlling the orientation of a titanium-aluminum alloy sheet layer by heat treatment of a strong magnetic field, which comprises the following steps:
After the set magnetic field strength is reached, placing the titanium-aluminum alloy sample in the central position in the strong magnetic field heat treatment furnace, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum; wherein the set value of the magnetic field intensity is 10T;
Heating from room temperature to a set temperature at a constant rate, keeping the temperature for 20 min-15 h, performing strong magnetic field heat treatment, and heating and cooling the sample along with the furnace; wherein the heat treatment interval is above the T α temperature of the titanium-aluminum alloy;
After the strong magnetic field heat treatment, the sheet group with a certain orientation of the titanium-aluminum alloy preferentially grows, so that the purpose of adjusting and controlling the orientation of the titanium-aluminum alloy sheet is achieved.
Preferably, the titanium-aluminum alloy comprises Ti-48Al-2Cr-2Nb alloy, ti-43Al-0.7Fe alloy and Ti-44.8Al-4Nb-1Mo-0.2B alloy.
Preferably, the titanium aluminum alloy is a titanium aluminum alloy containing trace Fe elements.
Preferably, the titanium-aluminum alloy containing trace Fe elements is Ti-43Al-0.7Fe alloy.
Preferably, the method further comprises:
and (3) preprocessing the titanium-aluminum alloy containing trace Fe elements before the strong magnetic field heat treatment to prepare the titanium-aluminum alloy containing trace Fe elements with large-size grains.
Preferably, the pretreatment comprises: and (3) placing the titanium-aluminum alloy containing the trace Fe element into a tube furnace for heat treatment.
Preferably, the heat treatment regime is: firstly, placing the titanium-aluminum alloy containing the trace Fe element in a tube furnace, when the temperature in the furnace reaches 1420 ℃, placing a sample in a heat preservation device for 20min, then reducing the temperature to 1350 ℃ at a speed of 10 ℃/min for heat preservation for 1h, and then cooling the furnace.
Preferably, when the titanium-aluminum alloy is subjected to short-time heat preservation of < 5 h at a temperature above T α ℃, the content of the lamellar orientation and the magnetic field direction is increased by 0-30 degrees; when the titanium-aluminum alloy is subjected to long-time heat preservation of more than 5 h at a temperature above T α ℃, the content of the sheet orientation and the magnetic field direction is increased by 60-90 degrees.
Compared with the prior art, the invention has the following beneficial technical effects:
the invention applies additional magnetization energy and driving force by using a strong magnetic field (10T) to ensure that the lamellar clusters with certain orientation preferentially grow, thereby realizing the regulation and control of lamellar orientation.
The method is different from the existing method for regulating and controlling the orientation of the titanium-aluminum alloy sheet, and a strong magnetic field (10T) is introduced in the heat treatment process above the temperature T α. Compared with heat treatment under the condition of no magnetic field, under the condition of strong magnetic field, the titanium-aluminum alloy with different components is subjected to short-time heat preservation (less than 5 h) at the temperature of T α, and the content of the lamellar orientation and the magnetic field direction at 0-30 DEG is increased; preserving heat for a long time (more than 5 h) above the temperature T α, and increasing the content of the lamellar orientation and the magnetic field direction at 60-90 degrees; in addition, the invention further discovers that the strong magnetic field has a remarkable influence on the orientation of the TiAl alloy sheets with larger sheet group size obtained by pretreatment, and particularly, after the Ti-43Al-0.7Fe alloy containing trace iron elements is pretreated to obtain larger sheet group size and then subjected to strong magnetic field heat treatment, the strong magnetic field effect capability can be improved, so that the preferential growth of the sheets with certain orientation is more obvious, and the strong magnetic field heat treatment is also indicated to effectively realize the regulation and control of the orientation of the titanium-aluminum alloy sheets and is suitable for regulating and controlling the orientations of the sheets of titanium-aluminum alloys with various components.
The method directly introduces a strong magnetic field of 10T in the heat treatment process of the titanium-aluminum alloy T α, and has the advantages of convenient operation, simple equipment and process, shorter period and high material utilization rate.
Drawings
FIG. 1 is a schematic diagram of a magnetic field apparatus of the present invention and sample placement;
FIG. 2 is a microstructure of Ti-43Al-0.7Fe of example 1 after heat treatment of 1350 ℃/30 min according to the invention;
FIG. 3 shows the alignment distribution of the sheet layer of Ti-43Al-0.7Fe after heat treatment at 1350 ℃/30 min in example 1 of the present invention;
FIG. 4 shows the alpha phase crystal orientation of Ti-43Al-0.7Fe after heat treatment at 10T-1350 deg.C/30 min in example 1 of the present invention;
FIG. 5 is a microstructure of example 2 of the present invention after heat treatment of 2Ti-43Al-0.7Fe at 1350 ℃/10 h;
FIG. 6 shows the alignment distribution of the sheet layer after heat treatment of Ti-43Al-0.7Fe at 1350 ℃/10 h in example 2 of the invention;
FIG. 7 shows the microstructure of Ti-48Al-2Cr-2Nb after heat treatment of 1420 ℃/60 min in example 3 of the present invention;
FIG. 8 is a distribution of sheet orientation after heat treatment of 1420 ℃/60 min of Ti-48Al-2Cr-2Nb in example 3 of the present invention;
FIG. 9 shows the microstructure of Ti-44.8Al-4Nb-1Mo-0.1B heat treated at 1425 ℃/20 min in example 4 of the invention;
FIG. 10 is a distribution of sheet orientation after heat treatment of 1425 ℃ C./20 min ℃ C. Of Ti-44.8Al-4Nb-1Mo-0.1B in example 4 of the present invention.
Reference numerals:
The device comprises a magnet 1, a water cooling system 2, a refractory material 3, a temperature measuring instrument 4, a quartz tube 5, a SiC heating body 6, a sample 7 and a thermocouple 8.
Description of the embodiments
The following description of the embodiments of the present invention will be made clearly and completely with reference to the accompanying drawings, in which it is apparent that the embodiments described are only some embodiments of the present invention, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
Examples
Cutting the cast Ti-43Al-0.7Fe alloy into a sample with the size of phi 10 multiplied by 10 mm by wire cutting;
pretreating a tube furnace to prepare large-size grains, obtaining an average lamellar group size of lamellar tissues of which the average lamellar group size is 1.2-mm, and then performing magnetic field heat treatment, wherein a heat treatment system is 1420 ℃/20 min-1350 ℃/1 h;
After the magnetic field strength reaches a set value of 10T, placing the sample in the center position of a magnetic field heat treatment furnace according to the graph shown in fig. 1, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum;
Setting the heat treatment temperature as 1350 ℃ (alpha single-phase zone), raising the temperature from room temperature to the set temperature at 40 ℃/min, preserving the heat for 30 min, and then cooling to the room temperature in a furnace;
Polishing a section parallel to the magnetic field direction: firstly polishing to 2000# by using SiC sand paper, then electropolishing, wherein the electrolyte is 60% methanol, 35% n-butanol and 5% perchloric acid, the voltage is 35V, the time is 25: 25 s, the temperature of the electrolyte is less than or equal to 10 ℃, and after polishing, placing the electrolyte into ultrasonic waves, washing with alcohol and airing;
representing microstructure by using BSE mode in scanning electron microscope, and counting proportion of different oriented sheets by using IPP software, wherein the result is shown in figure 2 and figure 3;
after heat treatment is carried out on Ti-43Al-0.7Fe alloy sheet layers under the condition of 10T strong magnetic field at 1350 ℃/30 min, the included angle between the Ti-43Al-0.7Fe alloy sheet layers and the magnetic field direction is more than 72%, and the EBSD result shows that the alpha crystal grains with <11-20> and <10-10> orientation are preferentially grown, which indicates that the Ti-43Al-0.7Fe alloy sheet layers can be effectively regulated and controlled to be oriented by the strong magnetic field when the Ti-43Al-0.7Fe alloy sheet layers are subjected to the magnetic field heat treatment in an alpha single-phase region.
Comparative example 1
Cutting the cast Ti-43Al-0.7Fe alloy into a sample with the size of phi 10 multiplied by 10 mm by wire cutting, wherein the initial lamellar block size distribution is 200-700 mu m;
After the magnetic field strength reaches a set value of 10T, placing the sample in the center position of a magnetic field heat treatment furnace according to the graph shown in fig. 1, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum;
Setting the heat treatment temperature as 1350 ℃ (alpha single-phase zone), raising the temperature from room temperature to the set temperature at 40 ℃/min, preserving the heat for 30 min, and then cooling to the room temperature in a furnace;
Polishing a section parallel to the magnetic field direction: firstly polishing to 2000# by using SiC sand paper, then electropolishing, wherein the electrolyte is 60% methanol, 35% n-butanol and 5% perchloric acid, the voltage is 35V, the time is 25: 25 s, the temperature of the electrolyte is less than or equal to 10 ℃, and after polishing, placing the electrolyte into ultrasonic waves, washing with alcohol and airing;
The BSE mode in a scanning electron microscope is used for representing the microstructure, IPP software is used for counting the proportion of the different orientation sheets, and the result shows that after heat treatment under the condition of a strong magnetic field of 10T and under 1350 ℃/30 min, the proportion of the included angle between the Ti-43Al-0.7Fe alloy sheet and the magnetic field direction can reach 40 percent, and compared with the embodiment 1, the effect of the strong magnetic field on the orientation of the TiAl alloy sheet with the larger sheet group size obtained by pretreatment is obvious.
Examples
Cutting the cast Ti-43Al-0.7Fe alloy into a sample with the size of phi 10 multiplied by 10 mm by wire cutting;
pretreating a tube furnace to prepare large-size grains, obtaining an average lamellar group size of lamellar tissues of which the average lamellar group size is 1.2-mm, and then performing magnetic field heat treatment, wherein a heat treatment system is 1420 ℃/20 min-1350 ℃/1 h;
After the magnetic field strength reaches a set value of 10T, placing the sample in the center position of a magnetic field heat treatment furnace according to the graph shown in fig. 1, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum;
setting the heat treatment temperature as 1350 ℃ (alpha single-phase zone), raising the temperature from room temperature to the set temperature at 40 ℃/min, preserving the heat for 10 h, and then cooling to the room temperature in a furnace;
Polishing a section parallel to the magnetic field direction: firstly polishing to 2000# by using SiC sand paper, then electropolishing, wherein the electrolyte is 60% methanol, 35% n-butanol and 5% perchloric acid, the voltage is 35V, the time is 25: 25 s, the temperature of the electrolyte is less than or equal to 10 ℃, and after polishing, placing the electrolyte into ultrasonic waves, washing with alcohol and airing;
the microstructure is characterized by a BSE mode in a scanning electron microscope, the proportion of the different orientation sheets is counted by IPP software, and the result is shown in figure 5 and figure 6;
After heat treatment is carried out on the Ti-43Al-0.7Fe alloy sheet under the condition of a strong magnetic field of 10T by 1350 ℃/10 h, under the coupling action of a magnetic field and a thermal field, the proportion of the included angle between the Ti-43Al-0.7Fe alloy sheet and the magnetic field direction is increased by 60-90 degrees due to the comprehensive effect of the easy magnetization direction, thus the Ti-43Al-0.7Fe alloy sheet is 48 percent, which shows that under the condition of the strong magnetic field, the Ti-43Al-0.7Fe alloy is insulated in an alpha single-phase region for different time, different regulating and controlling effects can be achieved, and further the heat treatment at the temperature above T α can realize the regulation and control of the orientation of the titanium-aluminum alloy sheet.
Examples
Cutting the cast Ti-48Al-2Cr-2Nb alloy subjected to hot isostatic pressing of the powder into a sample with the size phi of 10 multiplied by 8 mm by wire cutting;
After the magnetic field strength reaches a set value of 10T, placing the sample in the center position of a magnetic field heat treatment furnace according to the graph shown in fig. 1, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum;
Setting the heat treatment temperature as 1420 ℃ (alpha single-phase zone), raising the temperature from room temperature to the set temperature at 40 ℃/min, preserving the heat for 1h, and then cooling to the room temperature in a furnace;
Polishing a section parallel to the magnetic field direction: firstly polishing to 2000# by using SiC sand paper, then electropolishing, wherein the electrolyte is 60% methanol, 35% n-butanol and 5% perchloric acid, the voltage is 30V, the time is 15 s, the temperature of the electrolyte is less than or equal to 10 ℃, and after polishing, the electrolyte is placed into ultrasonic waves to be washed by alcohol and dried;
Characterizing microstructure by BSE mode in scanning electron microscope, and counting proportion of different slice orientations by IPP software, wherein the result is shown in FIG. 7 and FIG. 8;
After being subjected to 1420 ℃/1 h heat treatment under the condition of 10T strong magnetic field, the average content of the included angle between the Ti-48Al-2Cr-2Nb alloy sheet and the magnetic field direction is increased by 17 percent at 0-30 degrees, which shows that the strong magnetic field can effectively regulate and control the orientation of the titanium-aluminum alloy sheet when the magnetic field heat treatment is performed in an alpha single-phase region.
Examples
A hot isostatic pressed Ti-44.8Al-4Nb-1Mo-0.2B alloy was wire cut into test pieces having a size of Φ10X18 8 mm
After the magnetic field strength reaches a set value of 10T, placing the sample in the center position of a magnetic field heat treatment furnace according to the graph shown in fig. 1, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum;
Setting the heat treatment temperature to 1425 ℃ (beta single-phase zone), increasing the temperature to the set temperature from room temperature at 40 ℃/min, preserving heat to 20 min, reducing the temperature to 900 ℃ at the rate of 10 ℃/min, and then cooling in a furnace;
Polishing a section parallel to the magnetic field direction: firstly polishing to 2000# by using SiC sand paper, then electropolishing, wherein the electrolyte is 60% methanol, 35% n-butanol and 5% perchloric acid, the voltage is 35V, the time is 15 s, the temperature of the electrolyte is less than or equal to 10 ℃, and after polishing, the electrolyte is placed into ultrasonic waves to be washed by alcohol and dried;
characterizing microstructure by BSE mode in scanning electron microscope, and counting proportion of different slice orientations by IPP software, wherein the result is shown in figure 9 and figure 10;
After 1425 ℃/20 min heat treatment under a strong magnetic field of 10T ℃, the average content of the included angle between the Ti-44.8Al-4Nb-1Mo-0.2B alloy sheet and the magnetic field direction is increased by 5 percent at 0-30 degrees, and the average content of the alloy sheet is increased by 6 percent at 30-60 degrees, which indicates that the aim of regulating and controlling the orientation of the titanium-aluminum alloy sheet can be achieved by performing the magnetic field heat treatment in a beta single-phase region in the strong magnetic field.
It should be noted that in this document, terms such as "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
Although embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made therein without departing from the principles and spirit of the invention, the scope of which is defined in the appended claims and their equivalents.
Claims (1)
1. A method for regulating and controlling orientation of a titanium-aluminum alloy sheet layer through strong magnetic field heat treatment comprises the following steps:
Placing the titanium-aluminum alloy containing the trace Fe element into a tube furnace for heat treatment to prepare a titanium-aluminum alloy containing the trace Fe element with large-size crystal grains, wherein the titanium-aluminum alloy containing the trace Fe element is Ti-43Al-0.7Fe alloy;
The heat treatment system is as follows: firstly, placing the titanium-aluminum alloy containing the trace Fe element in a tube furnace, when the temperature in the furnace reaches 1420 ℃, placing a sample in a heat preservation device for 20 min, then reducing the temperature to 1350 ℃ at a speed of 10 ℃/min for heat preservation for 1h, and then cooling the furnace;
after the set magnetic field strength is reached, placing a titanium-aluminum alloy sample containing trace Fe elements in the central position of a strong magnetic field heat treatment furnace, and ensuring that the sample is heated uniformly and the surrounding gradient magnetic field is minimum; wherein the set value of the magnetic field intensity is 10T;
Heating from room temperature to a set temperature at a constant rate, keeping the temperature for 20min-15 h, performing strong magnetic field heat treatment, and heating and cooling the sample along with the furnace; wherein the heat treatment interval is above the T α temperature of the titanium-aluminum alloy;
After the strong magnetic field heat treatment, the sheet group with a certain orientation of the titanium-aluminum alloy preferentially grows, so that the aim of regulating and controlling the orientation of the titanium-aluminum alloy sheet is fulfilled;
When the titanium-aluminum alloy is subjected to short-time heat preservation at a temperature of more than T α and less than 5h, the content of the orientation of the sheet layer and the magnetic field direction is increased by 0-30 degrees; when the titanium-aluminum alloy is subjected to long-time heat preservation of more than 5h at a temperature above T α ℃, the content of the sheet orientation and the magnetic field direction is increased by 60-90 degrees.
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| CN116463569B true CN116463569B (en) | 2024-07-02 |
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