CN115846403A - Cobalt-based alloy with long rod-shaped phase structure with large number of stacking faults and deformation nanometer twin crystals and preparation method thereof - Google Patents
Cobalt-based alloy with long rod-shaped phase structure with large number of stacking faults and deformation nanometer twin crystals and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a cobalt-based alloy with a long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and a preparation method thereof, belonging to the technical field of forming processing and heat treatment of MP159 cobalt-based high-temperature alloy. The cobalt-based alloy is an MP159 high-temperature alloy plate, and the preparation method comprises the following steps: heating and insulating the MP159 high-temperature alloy plate, and then cooling the plate to room temperature by water; soaking the heat-treated MP159 high-temperature alloy plate in liquid nitrogen, and carrying out cryogenic rolling; and carrying out aging heat treatment on the rolled MP159 high-temperature alloy plate, and then air-cooling to room temperature. The long rod-shaped gamma 'strengthening phase with a large amount of stacking faults and deformation nanometer twin crystals is prepared in the MP159 high-temperature alloy through the preparation process of liquid nitrogen deep cooling rolling and aging heat treatment, and the long rod-shaped gamma' strengthening phase with a large amount of stacking faults and deformation nanometer twin crystals can obviously improve the hot corrosion resistance of the MP159 high-temperature alloy.
Description
Technical Field
The invention relates to a cobalt-based alloy with a long rod-shaped phase structure and a large number of stacking faults and deformation nanometer twin crystals and a preparation method thereof, belonging to the technical field of forming processing and heat treatment of MP159 cobalt-based high-temperature alloy.
Background
MP159 superalloy is widely used to manufacture ultra-high strength bolt fasteners in aerospace and other fields due to its high strength, good ductility and excellent corrosion resistance. But still can receive the influence of the harsh and complicated environment such as high temperature and high pressure that aeroengine produced and sodium, sulphur and chloride that fuel burning produced in the space service process. Therefore, further improving the corrosion resistance of the MP159 cobalt-based high-temperature alloy is a key engineering problem to be solved in the field of aerospace.
The MP159 high-temperature alloy is a cold deformation strengthening cobalt-based high-temperature alloy, and the strengthening mode is mainly strengthened by precipitating a gamma' strengthening phase through cold deformation and aging heat treatment. At present, a great deal of research work is only dedicated to improving the mechanical properties of the MP159 high-temperature alloy, for example, cai Sheqing and the like research that the cold drawing process has obvious improvement on the mechanical properties of the alloy, the ultimate tensile strength of the alloy is improved by 75% compared with the initial solid solution state, gu Yuhao and the like strengthen the alloy plate by the cold rolling and aging process, wherein the room-temperature tensile strength and the elongation can respectively reach 1.8GPa and 12.5%. With the rapid development of the aerospace field, the requirement on the hot corrosion resistance of the MP159 high-temperature alloy is higher and higher. However, there are few reports on how to improve the high temperature corrosion resistance of the MP159 superalloy. IN recent years, some documents report that the γ' phase having crystal defects can improve not only the mechanical properties of the IN718 superalloy but also the hot corrosion resistance of the IN718 superalloy. However, no literature reports how to prepare a gamma' strengthening phase with crystal defects in the MP159 high-temperature alloy. Therefore, it is very critical to improve the hot corrosion resistance of the MP159 superalloy by preparing a strengthening phase with a large number of crystal defects through a simple preparation process.
Disclosure of Invention
Aiming at the problems and the defects of the prior art, the invention provides the cobalt-based alloy with a long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and the preparation method thereof, namely a long rod-shaped gamma 'strengthening phase with a large number of stacking faults and deformation nanometer twin crystals is prepared in the MP159 high-temperature alloy through a preparation process of liquid nitrogen deep cooling rolling and aging heat treatment, and the long rod-shaped gamma' strengthening phase with a large number of stacking faults and deformation nanometer twin crystals can obviously improve the hot corrosion resistance of the MP159 high-temperature alloy.
In order to achieve the purpose, the invention provides the following scheme:
the invention provides a preparation method of a cobalt-based alloy with a long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals, wherein the cobalt-based alloy is an MP159 high-temperature alloy plate and comprises the following chemical components: 35.7wt% of Co, 25.5wt% of Ni, 19.0wt% of Cr, 9.0wt% of Fe, 7.0wt% of Mo, 3.0wt% of Ti, 0.6 wt% of Nb0, and the balance of Al; the preparation method comprises the following steps:
(1) Solution treatment: heating and insulating the MP159 high-temperature alloy plate, and then cooling the plate to room temperature by water;
(2) Deep cooling rolling: soaking the MP159 high-temperature alloy plate treated in the step (1) in liquid nitrogen, and carrying out cryogenic rolling;
(3) Aging treatment: and (3) carrying out aging heat treatment on the MP159 high-temperature alloy plate rolled in the step (2), and then cooling to room temperature.
Further, in the step (3), the temperature of the aging heat treatment is 800 ℃, and the heat preservation time is 2-25h.
Further, in the step (1), the temperature is heated to 1050 ℃ and kept for 4 hours.
Further, in the step (2), soaking in liquid nitrogen for 15min.
Further, in the step (2), the deep cooling rolling is carried out in a multi-pass rolling mode, after each pass of rolling is finished, the rolling is quickly placed into liquid nitrogen to be soaked for 10min, and then the next pass of rolling is carried out.
Further, the reduction per pass was 10% of the original thickness of the MP159 superalloy sheet material.
Further, in the step (2), the MP159 high-temperature alloy plate undergoes deep cooling rolling, and the deformation amount of the MP159 high-temperature alloy plate is 48% of the original thickness.
The invention also provides the cobalt-based alloy with the long rod-shaped phase structure and a large number of stacking faults and deformation nanometer twin crystals, which is prepared by the preparation method.
The invention discloses the following technical effects:
(1) The invention not only refines the crystal grains of the MP159 high-temperature alloy plate through deep cooling rolling, but also can greatly increase the dislocation density in the alloy and the high-density stacking fault and deformation nanometer twin crystal. Compared with the common room temperature rolling process, the deep cooling rolling and aging heat treatment preparation process adopted by the invention can prepare the long rod-shaped gamma 'strengthening phase with a large amount of stacking faults and deformation nanometer twin crystals in the MP159 high-temperature alloy under the same condition, and in the hot corrosion process, the long rod-shaped gamma' phase with a large amount of stacking faults and deformation nanometer twin crystals can be used as an effective channel for the outward diffusion of elements from a matrix to form a smoother and denser oxidation film on the surface of the alloy, thereby obviously improving the hot corrosion resistance of the MP159 high-temperature alloy plate.
(2) The method has the advantages of simple process and convenient operation, and is suitable for large-scale popularization and production.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings needed to be used in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings without inventive exercise.
FIG. 1 is a TEM micrograph of the MP159 superalloy sheet after treatment in example 1; wherein (a) is a bright field image of a rod-shaped gamma 'phase precipitated after aging for 2h, (b) is an enlarged image of a region (a), (b) a small image at the upper left corner is a selected area electron diffraction spot of the region, and (c) is a high-resolution microstructure image of transmission of the rod-shaped gamma' phase;
FIG. 2 is the EDS elemental distribution plot of the MP159 superalloy sheet after treatment in example 1;
FIG. 3 is a TEM micrograph of the MP159 superalloy sheet after treatment in example 2;
FIG. 4 is the EDS elemental profile of the MP159 superalloy sheet after treatment in example 2;
FIG. 5 is a TEM micrograph of the MP159 superalloy sheet material treated in comparative example 1;
FIG. 6 is an EDS elemental profile of the MP159 superalloy sheet after treatment in comparative example 1;
FIG. 7 is a TEM micrograph of the MP159 superalloy sheet treated in comparative example 2, wherein (a) is an aged precipitated phase, (b) is an enlarged image of the precipitated phase, (c) is a selected area electron diffraction pattern of the precipitated phase, and (c) the small upper-right-corner image is selected area electron diffraction spots in the area;
FIG. 8 is a graph of mass loss of MP159 superalloy sheets as a function of hot corrosion time for example 2 and comparative example 2, wherein (a) is a graph of overall change and (b) is a graph of second stage change;
FIG. 9 is a transmission electron micrograph of a cross section of an alloy specimen of example 2 of the present invention taken at 800 ℃ after 5 th cycle;
FIG. 10 is a cross-sectional EDS image of an alloy specimen of example 2 of the present invention after the 5 th cycle at 800 ℃;
FIG. 11 is a transmission electron micrograph of a cross section of a comparative example 2 alloy specimen of the present invention at 800 ℃ after 5 th cycle;
FIG. 12 is a cross-sectional EDS image of a comparative example 2 alloy specimen of the present invention after the 5 th cycle at 800 ℃.
Detailed Description
Reference will now be made in detail to various exemplary embodiments of the invention, the detailed description should not be construed as limiting the invention but as a more detailed description of certain aspects, features and embodiments of the invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. Further, for numerical ranges in this disclosure, it is understood that each intervening value, between the upper and lower limit of that range, is also specifically disclosed. Every smaller range between any stated value or intervening value in a stated range and any other stated or intervening value in that stated range is encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated by reference herein for the purpose of disclosing and describing the methods and/or materials associated with the documents. In case of conflict with any incorporated document, the present specification will control.
It will be apparent to those skilled in the art that various modifications and variations can be made in the specific embodiments of the present disclosure without departing from the scope or spirit of the disclosure. Other embodiments will be apparent to those skilled in the art from consideration of the specification. The description and examples are intended to be illustrative only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are open-ended terms that mean including but not limited to.
The embodiment of the invention provides a preparation method of a cobalt-based alloy with a long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals, wherein the cobalt-based alloy is an MP159 high-temperature alloy plate and comprises the following chemical components: 35.7wt% of Co, 25.5wt% of Ni, 19.0wt% of Cr, 9.0wt% of Fe9, 7.0wt% of Mo, 3.0wt% of Ti, 0.6 wt% of Nb0, and the balance of Al; the preparation method comprises the following steps:
(1) Solution treatment: heating and insulating the MP159 high-temperature alloy plate, and then cooling the plate to room temperature by water;
(2) Deep cooling rolling: soaking the MP159 high-temperature alloy plate treated in the step (1) in liquid nitrogen, and carrying out cryogenic rolling;
(3) Aging treatment: and (3) carrying out aging heat treatment on the MP159 high-temperature alloy plate rolled in the step (2), and then cooling to room temperature.
In the embodiment of the invention, in the step (3), the temperature of the aging heat treatment is 800 ℃, and the heat preservation time is 2-25h.
In the embodiment of the invention, in the step (1), the temperature is heated to 1050 ℃ and kept for 4 hours.
In the present example, in step (2), soaking in liquid nitrogen was carried out for 15min.
In the embodiment of the invention, in the step (2), the deep cooling rolling is carried out by adopting a multi-pass rolling mode, after each pass of rolling is finished, the deep cooling rolling is quickly placed into liquid nitrogen for soaking for 10min, and then the next pass of rolling is carried out.
In the embodiment of the invention, the reduction per pass is 10% of the original thickness of the MP159 high-temperature alloy plate.
In the embodiment of the invention, in the step (2), the MP159 high-temperature alloy plate undergoes deep cooling rolling, and the deformation amount is 48% of the original thickness.
The embodiment of the invention also provides the cobalt-based alloy which is prepared by the preparation method and has a long rod-shaped phase structure with a large number of stacking faults and deformation nanometer twin crystals.
In the embodiment of the invention, the MP159 high-temperature alloy plate is purchased from Guizhou aerospace Fine manufacturing company Limited.
The technical solution of the present invention is further illustrated by the following examples.
Example 1
(1) Solution treatment: the MP159 high-temperature alloy plate is put into a muffle furnace to be heated to 1050 ℃ from room temperature along with the furnace at the heating rate of 10 ℃/min, the temperature is kept for 4h, and then the temperature is cooled to room temperature by water.
(2) Deep cooling and rolling: pouring liquid nitrogen into an iron bath, and soaking the MP159 high-temperature alloy plate with the length, width and thickness of 100mm, 50mm and 6mm processed in the step (1) in the liquid nitrogen for 15min after the liquid nitrogen is vaporized and stabilized;
coating lubricating oil on the surface of a roller of a rolling mill, starting the rolling mill, setting the rotating speed of the roller to be 0.5m/min, taking the MP159 high-temperature alloy plate out of liquid nitrogen after the roller rotates uniformly, rolling by adopting a 5-pass rolling mode, wherein the deformation of each pass is 10% of the thickness of the original plate, quickly putting a rolled sample into the liquid nitrogen for soaking after the rolling of each pass is finished, wherein the soaking time is 10min, and performing the next-pass rolling deformation after the soaking is finished; until the total deformation reaches 48% of the original plate thickness of the MP159 high-temperature alloy.
(3) Aging treatment: and (3) putting the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 2 hours, and then cooling to room temperature in air.
A transmission electron microscope microstructure picture of the MP159 high-temperature alloy plate treated by the method of the embodiment 1 is shown in a figure 1, wherein (a) is a bright field image of a rod-shaped gamma 'phase precipitated after 2h aging, (b) is an enlarged view of a region (a), (b) a small picture at the upper left corner is selected region electron diffraction spots of the region, and (c) is a high-resolution microstructure picture of rod-shaped gamma' phase transmission; the EDS elemental profile is shown in FIG. 2. As can be seen from fig. 1 and 2, the long rod-like precipitated phases started to form in the MP159 high-temperature alloy sheet. Such long rod-like phases are the gamma' phase with the L12 superlattice as determined by selective electron diffraction techniques. And the distribution of alloy elements in the long rod-shaped gamma' phase is analyzed by a TEM-EDS technology, and the alloy elements mainly comprise Ti, ni, co and Cr elements. Through high-resolution transmission tissue analysis, a large amount of stacking faults and deformation nanometer twin crystals are generated inside the precipitated phase.
Example 2
(1) Solution treatment: the MP159 high-temperature alloy plate is put into a muffle furnace to be heated to 1050 ℃ from room temperature along with the furnace at the heating rate of 10 ℃/min, the temperature is kept for 4h, and then the temperature is cooled to room temperature by water.
(2) Deep cooling and rolling: pouring liquid nitrogen into an iron bath, and soaking the MP159 high-temperature alloy plate with the length, width and thickness of 100mm, 50mm and 6mm processed in the step (1) in the liquid nitrogen for 15min after the liquid nitrogen is vaporized and stabilized;
coating lubricating oil on the surface of a roller of a rolling mill, starting the rolling mill, setting the rotating speed of the roller to be 0.5m/min, taking the MP159 high-temperature alloy plate out of liquid nitrogen after the roller rotates uniformly, rolling by adopting a 5-pass rolling mode, wherein the deformation of each pass is 10% of the thickness of the original plate, quickly putting a rolled sample into the liquid nitrogen for soaking after the rolling of each pass is finished, wherein the soaking time is 10min, and performing the next-pass rolling deformation after the soaking is finished; until the total deformation reaches 48 percent of the thickness of the original MP159 high-temperature alloy plate.
(3) Aging treatment: and (3) putting the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 25h, and then air-cooling to room temperature.
The transmission electron microscopic structure picture of the MP159 high-temperature alloy plate treated by the method of the invention in the embodiment 2 is shown in figure 3, and the EDS element distribution picture is shown in figure 4. As can be seen from fig. 3 and fig. 4, the number of long rod-shaped γ 'phases in the cryogenically rolled 48% MP159 superalloy sheet is increased with the increase of aging time, and the shape gradually grows into a rod shape, and TEM-EDS structure analysis shows that a large amount of stacking faults and deformed nano twins exist in the long rod-shaped γ' strengthening phase obtained by long-time aging.
Comparative example 1
(1) Solution treatment: the MP159 high-temperature alloy plate is put into a muffle furnace to be heated to 1050 ℃ from room temperature along with the furnace at the heating rate of 10 ℃/min, the temperature is kept for 4h, and then the temperature is cooled to room temperature by water.
(2) Deep cooling rolling: pouring liquid nitrogen into an iron bath, and soaking the MP159 high-temperature alloy plate with the length, width and thickness of 100mm, 50mm and 6mm processed in the step (1) in the liquid nitrogen for 15min after the liquid nitrogen is vaporized and stabilized;
coating lubricating oil on the surface of a roller of a rolling mill, starting the rolling mill, setting the rotating speed of the roller to be 0.5m/min, taking an MP159 high-temperature alloy plate out of liquid nitrogen after the roller rotates uniformly, rolling by adopting a 5-pass rolling mode, wherein the deformation of each pass is 10-15% of the thickness of the original plate, quickly putting a rolling sample into the liquid nitrogen for soaking after the rolling of each pass is finished, wherein the soaking time is 10-15min, and carrying out the rolling deformation of the next pass after the soaking is finished; until the total deformation reaches 48% of the original plate thickness of the MP159 high-temperature alloy.
(3) Aging treatment: and (3) putting the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving the heat for 0.5h, and then cooling the plate to room temperature in an air cooling mode.
The transmission electron microscope microscopic structure picture of the MP159 high-temperature alloy plate treated by the invention in the comparative example 1 is shown in figure 5, and the EDS element distribution picture is shown in figure 6. As can be seen from fig. 5 and 6, no precipitated phase was present in the alloy, and the elements were uniformly distributed.
Comparative example 2
Carrying out a common room temperature rolling process on the MP159 high-temperature alloy plate:
(1) Solution treatment: the MP159 high-temperature alloy plate is put into a muffle furnace to be heated to 1050 ℃ from room temperature along with the furnace at the heating rate of 10 ℃/min, the temperature is kept for 4h, and then the temperature is cooled to room temperature by water.
(2) Rolling at room temperature: coating lubricating oil on the surface of a roller of a rolling mill, starting the rolling mill, and setting the rotating speed of the roller to be 0.5m/min; and after the roller rotates uniformly, rolling and deforming the MP159 high-temperature alloy plate with the length, the width and the thickness of 100mm, 50mm and 6mm after the solution treatment. And the total rolling deformation is 48 percent of the thickness of the original MP159 high-temperature alloy plate, the rolling is carried out by 5 times, the deformation of each time is 10 percent of the thickness of the original plate until the total deformation reaches 48 percent of the thickness of the original MP159 high-temperature alloy plate, and the MP159 high-temperature alloy plate with the rolling deformation of 48 percent under the room temperature condition is obtained.
(3) And (3) aging treatment: and (3) putting the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 25h, and then cooling to room temperature in air.
The transmission electron microscope microscopic structure picture of the MP159 high-temperature alloy plate treated by the comparative example 2 of the invention is shown in figure 7, wherein (a) is precipitated phase after aging, (b) is an enlarged picture of the precipitated phase, (c) is a selected area electron diffraction picture of the precipitated phase, and (c) the small picture at the upper left corner is the selected area electron diffraction picture of the area, in order to prove the composition condition of the area phase. As can be seen from FIG. 7, the precipitated phases in the alloy are in a short rod shape, and selective electron diffraction spots prove that the structure of the alloy is still L12 superlattice gamma' phase, but diffraction spots of nanometer twin crystals and stacking faults do not exist.
Performance testing
In order to test the corrosion resistance, the MP159 high temperature alloy sheet material treated with example 2 in which a large amount of long rod-like gamma '-strengthening phase having a large number of stacking faults and deformed nano twins was precipitated after aging for 25 hours and the relative proportion of short rod-like gamma' -free nano twins precipitated after aging for 25 hours was subjected to a hot corrosion resistance test in which a salt solution (75wt% Na) was sprayed with a salt solution 2 SO 4 +25wt% NaCl) was uniformly sprayed on the surface of the alloy specimen (MP 159 high-temperature alloy sheet material after treatment of example 2 and comparative example 2), after which the alloy specimen with the salt adhered thereto was weighed until the deposition rate reached 6-6.5mg/cm 2 . The sample with the attached salt is placed in a muffle furnace at 800 ℃ for heat preservation. The sample was removed from the furnace after each cycle of 5h and air cooled to room temperature. The cooling rate was 2.5 ℃/min. In order to obtain the net weight change of the MP159 high-temperature alloy plate, the sample is ultrasonically cleaned in acetone for 15min, and the alloy sample after ultrasonic cleaning is weighed by a precision balance. In the next hot corrosion cycle, the salt layer is deposited on the surface of the alloy sample again until 50h, namely 10 cycles, and then the alloy sample is cooled to room temperature in an air cooling mode.
FIG. 8 (a) is a graph showing the mass loss of the MP159 superalloy sheet material in example 2 and comparative example 2 as a whole as a function of hot corrosion time, and (b) is a graph showing the mass loss of the MP159 superalloy sheet material in second stage example 2 and comparative example 2 as a function of hot corrosion time (in the graph, RTR48 means that 48% of MP159 is room temperature rolled, i.e., comparative example 2, and CR48 is cryogenically rolled, i.e., 48% of MP159, i.e., example 2). As can be seen in FIG. 8, the hot corrosion curve can be based on the hot corrosion coupon lossThe difference in weight is divided into three stages. In the first stage (1 st to 2 nd cycles), since 48% of the MP159 superalloy sheet cold-rolled at 0.5h did not precipitate the gamma '-strengthening phase in the form of a rod, but only the alloy sample at 2h just started to precipitate the gamma' -strengthening phase in the form of a long rod, it was observed that the weight loss between the alloy samples of comparative example 2 and example 2 varied in the same and very little manner. With the prolonging of the aging time, the rod-shaped gamma 'strengthening phase becomes thicker in size and gradually increases in number within 25h, and the more stacking faults and deformed nanometer twin crystals exist in the rod-shaped gamma' strengthening phase. It can be seen that the weight loss of the alloy coupon of example 2 in the second stage (cycles 2 through 6) is consistently less than that of comparative example 2, indicating that the alloy coupon of example 2 of the present invention has a higher hot corrosion resistance than the alloy coupon of comparative example 2. Particularly, in the 4 th hot corrosion cycle, the weight loss difference of the alloy samples of the comparative example 2 and the example 2 is the largest, and reaches 19.65mg cm -2 。
To further confirm that the hot corrosion resistance of the alloy is related to the gamma prime strengthening phase precipitated after aging, FIGS. 9 and 10 are the transmission electron microscopy microstructure and EDS image of the alloy sample of example 2 at 800 ℃ for 5 th cycle, i.e., after aging for 25h, respectively, and FIGS. 11 and 12 are the transmission electron microscopy microstructure and EDS image of the alloy sample of comparative example 2 at 800 ℃ for 5 th cycle, i.e., after aging for 25h, respectively. It can be seen that the alloy sample of example 2 of the present invention forms a more uniform, flat, denser oxide layer after hot etching as compared to the 48% room temperature rolled sample (comparative example 2). The reason is that after 25h, 48 percent of alloy samples are subjected to deep cooling rolling to precipitate a long rod-shaped gamma 'strengthening phase with a large amount of stacking faults and deformation nanometer twin crystals, the large amount of stacking faults and deformation nanometer twin crystals in the long rod-shaped gamma' strengthening phase can be used as effective channels for the outward diffusion of alloy elements from a matrix, and a compact oxide film is formed on the surface of the alloy, so that the hot corrosion resistance of the alloy is improved.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.
Claims (8)
1. A preparation method of a cobalt-based alloy with a long rod-shaped phase structure of a large number of stacking faults and deformed nanometer twin crystals is characterized in that the cobalt-based alloy is an MP159 high-temperature alloy plate, and the preparation method comprises the following steps:
(1) Heating and insulating the MP159 high-temperature alloy plate, and then cooling the plate to room temperature by water;
(2) Soaking the MP159 high-temperature alloy plate treated in the step (1) in liquid nitrogen, and carrying out cryogenic rolling;
(3) And (3) performing aging heat treatment on the MP159 high-temperature alloy plate rolled in the step (2), and then cooling to room temperature.
2. The method according to claim 1, wherein in the step (3), the aging heat treatment is carried out at a temperature of 800 ℃ for 2 to 25 hours.
3. The method according to claim 1, wherein in the step (1), the temperature is increased to 1050 ℃ and the temperature is maintained for 4 hours.
4. The method according to claim 1, wherein in the step (2), the mixture is immersed in liquid nitrogen for 15min.
5. The method according to claim 1, wherein in the step (2), the cryogenic rolling is performed by a multi-pass rolling method, and after each pass of rolling is finished, the rolling is rapidly immersed in liquid nitrogen for 10min and then performed for the next pass of rolling.
6. The method of claim 4, wherein the reduction per pass is 10% of the original thickness of the MP159 superalloy sheet material.
7. The method according to claim 1, wherein in the step (2), the MP159 superalloy sheet is subjected to deep cold rolling to have a deformation of 48% of an original thickness.
8. A cobalt-based alloy having a long rod-like phase structure with a large number of stacking faults and deformed nano twins, which is produced by the production method described in any one of claims 1 to 7.
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