CN115846403B - Cobalt-based alloy with long rod-shaped phase structure of a 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 of a large number of stacking faults and deformation nanometer twin crystals and preparation method thereof Download PDFInfo
- Publication number
- CN115846403B CN115846403B CN202211165897.4A CN202211165897A CN115846403B CN 115846403 B CN115846403 B CN 115846403B CN 202211165897 A CN202211165897 A CN 202211165897A CN 115846403 B CN115846403 B CN 115846403B
- Authority
- CN
- China
- Prior art keywords
- rolling
- temperature
- long rod
- cobalt
- deformation
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E30/00—Energy generation of nuclear origin
- Y02E30/30—Nuclear fission reactors
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a cobalt-based alloy with a large number of faults and long rod-shaped phase structures of deformed nanometer twin crystals and a preparation method thereof, belonging to the technical field of MP159 cobalt-based superalloy forming processing and heat treatment. The cobalt-based alloy is an MP159 superalloy plate, and the preparation method comprises the following steps: heating and preserving heat of the MP159 high-temperature alloy plate, and then cooling to room temperature by water; soaking the heat-treated MP159 high-temperature alloy plate in liquid nitrogen, and performing cryogenic rolling; and (5) carrying out aging heat treatment on the MP159 high-temperature alloy plate after rolling, and then air-cooling to room temperature. The long rod-shaped gamma 'strengthening phase with a large amount of faults and deformation nanometer twin crystals is prepared in the MP159 high-temperature alloy through a preparation process of liquid nitrogen cryogenic rolling and aging heat treatment, and the long rod-shaped gamma' strengthening phase with a large amount of faults and deformation nanometer twin crystals can remarkably improve the hot corrosion resistance of the MP159 high-temperature alloy.
Description
Technical Field
The invention relates to a cobalt-based alloy with a large number of faults and deformation nanometer twin crystal long rod-shaped phase structures and a preparation method thereof, belonging to the technical field of MP159 cobalt-based superalloy forming processing and heat treatment.
Background
MP159 superalloys are widely used to make ultra-high strength bolt fasteners in the aerospace field due to their high strength, good ductility and excellent corrosion resistance. However, in the space service process, the air engine is still influenced by the high temperature and high pressure generated by the aeroengine and the severe complex environments such as sodium, sulfur, chloride and the like generated by fuel combustion. Therefore, further improving the corrosion resistance of MP159 cobalt-based superalloy is a critical engineering problem to be solved in the aerospace field.
MP159 superalloy is a cold deformation strengthened cobalt-based superalloy, and the strengthening mode is mainly strengthening by cold deformation and aging heat treatment to precipitate gamma' strengthening phase. At present, a great deal of research work is only dedicated to improving the mechanical properties of MP159 high-temperature alloy, for example, cai Sheqing and the like research that the cold drawing process obviously improves the mechanical properties of the alloy, the ultimate tensile strength of the alloy is improved by 75 percent compared with that of the initial solid solution state, gu Yuhao and the like strengthen the alloy plate by a cold rolling and aging process, wherein the room-temperature tensile strength and the elongation rate can reach 1.8GPa and 12.5 percent respectively. With the rapid development of the aerospace field, the requirements on the hot corrosion resistance of MP159 superalloy are higher and higher. However, few documents report how to improve the high temperature corrosion resistance of MP159 superalloys. IN recent years, some documents report that the gamma' -phase having crystal defects can not only improve the mechanical properties of the IN718 superalloy, but also improve the hot corrosion resistance of the IN718 superalloy. However, no literature is reported on how to prepare a gamma prime strengthening phase with crystal defects in MP159 superalloys. Therefore, it is particularly critical how to prepare a strengthening phase with a large number of crystal defects by a simple preparation process to improve the hot corrosion resistance of MP159 superalloy.
Disclosure of Invention
Aiming at the problems and the defects existing in the prior art, the invention provides a cobalt-based alloy with a long rod-shaped phase structure of a large number of faults and deformation nanometer twin crystals and a preparation method thereof, namely, a long rod-shaped gamma 'strengthening phase with a large number of faults and deformation nanometer twin crystals is prepared in MP159 high-temperature alloy through a preparation process of liquid nitrogen cryogenic rolling and aging heat treatment, and the long rod-shaped gamma' strengthening phase with a large number of faults and deformation nanometer twin crystals can obviously improve the hot corrosion resistance of the MP159 high-temperature alloy.
In order to achieve the above object, the present invention provides the following solutions:
the invention provides a preparation method of a cobalt-based alloy with a large amount of stacking faults and deformation nanometer twin crystal long rod-shaped phase structures, wherein the cobalt-based alloy is an MP159 high-temperature alloy plate, and the chemical composition is as follows: 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 Nb and the balance of Al; the preparation method comprises the following steps:
(1) Solution treatment: heating and preserving heat of the MP159 high-temperature alloy plate, and then cooling to room temperature by water;
(2) Cryogenic rolling: immersing the MP159 high-temperature alloy plate processed in the step (1) in liquid nitrogen, and performing 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 the temperature is kept for 4 hours.
Further, in the step (2), the mixture is soaked in liquid nitrogen for 15min.
Further, in the step (2), the deep cold rolling is performed by adopting a multi-pass rolling mode, after each pass of rolling is finished, the deep cold rolling is quickly placed into liquid nitrogen to be soaked for 10min, and then the next pass of rolling is performed.
Further, the reduction per pass is 10% of the original thickness of the MP159 superalloy sheet.
Further, in the step (2), the deformation of the MP159 superalloy sheet material after being subjected to cryogenic rolling is 48% of the original thickness.
The invention also provides the cobalt-base alloy with the long rod-shaped phase structure of a great amount of stacking faults and deformation nanometer twin crystals, which is prepared by the preparation method.
The invention discloses the following technical effects:
(1) According to the invention, the grains of the MP159 high-temperature alloy plate are thinned through cryogenic rolling, and the dislocation density in the alloy and the high-density stacking fault and deformation nanometer twin crystal can be greatly increased. Compared with the common room temperature rolling process, the preparation process of the invention adopting the deep cooling rolling and aging heat treatment can prepare a long rod-shaped gamma 'strengthening phase with a large amount of faults and deformation nanometer twin crystals in the MP159 high-temperature alloy, and the long rod-shaped gamma' strengthening phase with a large amount of faults and deformation nanometer twin crystals can be used as an effective channel for outwards diffusing elements from a matrix in the hot corrosion process, so that a flatter and denser oxide film is formed on the surface of the alloy, thereby obviously improving the hot corrosion resistance of the MP159 high-temperature alloy plate.
(2) The invention has 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 of the prior art, the drawings that are needed in the embodiments will be briefly described below, it being obvious that the drawings in the following description are only some embodiments of the present invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a Transmission Electron Microscope (TEM) microscopic image of MP159 superalloy sheet after treatment in example 1; wherein (a) is a bright field image of a rod-like gamma '-phase precipitated after aging for 2 hours, (b) is an enlarged view of the area of (a), (b) is a selected area electron diffraction spot of the area, and (c) is a high-resolution microscopic structure image of transmission of the rod-like gamma' -phase;
FIG. 2 is an EDS element distribution diagram of MP159 superalloy sheets after treatment in example 1;
FIG. 3 is a Transmission Electron Microscope (TEM) microscopic image of MP159 superalloy sheet after treatment in example 2;
FIG. 4 is an EDS elemental distribution diagram of MP159 superalloy sheet after treatment in example 2;
FIG. 5 is a transmission electron micrograph of an MP159 superalloy sheet after treatment of comparative example 1;
FIG. 6 is an EDS elemental distribution of MP159 superalloy sheet after treatment of comparative example 1;
FIG. 7 is a transmission electron microscopic microstructure of the MP159 superalloy sheet after treatment of comparative example 2, wherein (a) is an aged precipitated phase, (b) is an enlarged picture of the precipitated phase, (c) is a selected area electron diffraction pattern of the precipitated phase, and (c) the upper right hand panel is a selected area electron diffraction spot of the area;
FIG. 8 is a graph showing the mass loss of MP159 superalloy sheets in example 2 and comparative example 2 as a function of hot corrosion time, (a) is an overall graph, and (b) is a second-stage graph;
FIG. 9 is a cross-sectional transmission electron microscope microstructure of an alloy sample of example 2 of the present invention after the 5 th cycle at 800 ℃;
FIG. 10 is a cross-sectional EDS image of an alloy sample of example 2 of the present invention after the 5 th cycle at 800 ℃;
FIG. 11 is a cross-sectional transmission electron microscopic microstructure of a comparative example 2 alloy specimen of the present invention after the 5 th cycle at 800 ℃;
FIG. 12 is a cross-sectional EDS image of a comparative example 2 alloy sample of the present invention after the 5 th cycle at 800 ℃.
Detailed Description
Various exemplary embodiments of the invention will now be described in detail, which should not be considered as limiting the invention, but rather as more detailed descriptions 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. In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless otherwise defined, 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 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 invention described herein without departing from the scope or spirit of the invention. Other embodiments will be apparent to those skilled in the art from consideration of the specification of the present invention. The specification and examples of the present invention are exemplary only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are intended to be inclusive and mean an inclusion, but not limited to.
The embodiment of the invention provides a preparation method of a cobalt-based alloy with a large number of stacking faults and long rod-shaped phase structures of deformed nanometer twin crystals, wherein the cobalt-based alloy is an MP159 high-temperature alloy plate, and the chemical composition is as follows: 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 Nb and the balance of Al; the preparation method comprises the following steps:
(1) Solution treatment: heating and preserving heat of the MP159 high-temperature alloy plate, and then cooling to room temperature by water;
(2) Cryogenic rolling: immersing the MP159 high-temperature alloy plate processed in the step (1) in liquid nitrogen, and performing 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 the temperature is kept for 4 hours.
In the embodiment of the invention, in the step (2), the mixture is soaked in liquid nitrogen for 15min.
In the embodiment of the invention, in the step (2), the deep cold rolling is performed by adopting a multi-pass rolling mode, and after each pass of rolling is finished, the deep cold rolling is quickly placed into liquid nitrogen to be soaked for 10 minutes, and then the next pass of rolling is performed.
In the embodiment of the invention, the reduction per pass is 10% of the original thickness of the MP159 superalloy sheet.
In the embodiment of the invention, in the step (2), the deformation of the MP159 superalloy sheet material is 48% of the original thickness after the MP159 superalloy sheet material is subjected to cryogenic rolling.
The embodiment of the invention also provides the cobalt-based alloy with the long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals, which is prepared by the preparation method.
In the embodiment of the invention, the MP159 superalloy plate is purchased from Guizhou aerospace fine manufacturing Co.
The technical scheme of the invention is further described by the following examples.
Example 1
(1) Solution treatment: the MP159 superalloy plate is placed in a muffle furnace, heated to 1050 ℃ from room temperature along with the furnace at a heating rate of 10 ℃/min, kept for 4 hours, and then cooled to room temperature.
(2) Cryogenic rolling: pouring liquid nitrogen into an iron tank, and soaking MP159 high-temperature alloy plates with the length, width and thickness of 100mm, 50mm and 6mm treated in the step (1) in the liquid nitrogen for 15min after the vaporization of the liquid nitrogen is stable;
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 out the MP159 high-temperature alloy plate from liquid nitrogen after the roller rotates uniformly, rolling in a 5-pass rolling mode, wherein the deformation of each pass is 10% of the thickness of the original plate, rapidly soaking a rolling sample in the liquid nitrogen after each pass of rolling is finished, soaking for 10min, and carrying out rolling deformation of the next pass after soaking is finished; until the total deformation reaches 48% of the thickness of the original MP159 superalloy sheet.
(3) Aging treatment: and (3) placing 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 by air.
The transmission electron microscope microstructure of the MP159 superalloy sheet processed in the embodiment 1 of the invention is shown in fig. 1, wherein (a) is a bright field image of a rod-like gamma 'phase precipitated after aging for 2 hours, (b) is an enlarged view of a region (a), a small image at the upper left corner in (b) is a selected area electron diffraction spot of the region, and (c) is a high resolution microstructure image of transmission of the rod-like gamma' phase; the EDS element distribution diagram is shown in FIG. 2. As can be seen from fig. 1 and 2, long rod-like precipitated phases have started to form inside the MP159 superalloy plate. The long rod-like phase is a gamma' phase with an L12 superlattice as determined by selective electron diffraction techniques. 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 great amount of stacking faults and deformed nanometer twin crystals are generated in the precipitated phases.
Example 2
(1) Solution treatment: the MP159 superalloy plate is placed in a muffle furnace, heated to 1050 ℃ from room temperature along with the furnace at a heating rate of 10 ℃/min, kept for 4 hours, and then cooled to room temperature.
(2) Cryogenic rolling: pouring liquid nitrogen into an iron tank, and soaking MP159 high-temperature alloy plates with the length, width and thickness of 100mm, 50mm and 6mm treated in the step (1) in the liquid nitrogen for 15min after the vaporization of the liquid nitrogen is stable;
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 out the MP159 high-temperature alloy plate from liquid nitrogen after the roller rotates uniformly, rolling in a 5-pass rolling mode, wherein the deformation of each pass is 10% of the thickness of the original plate, rapidly soaking a rolling sample in the liquid nitrogen after each pass of rolling is finished, soaking for 10min, and carrying out rolling deformation of the next pass after soaking is finished; until the total deformation reaches 48% of the thickness of the original MP159 superalloy sheet.
(3) Aging treatment: and (3) placing the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 25 hours, and then cooling to room temperature by air.
The transmission electron microscope microstructure diagram of the MP159 superalloy sheet processed in example 2 of the present invention is shown in FIG. 3, and the EDS element distribution diagram is shown in FIG. 4. As can be seen from fig. 3 and 4, as the aging time increases, the number of long rod-shaped gamma ' -phases in the MP159 superalloy plate subjected to cryogenic rolling is increased, the shape of the long rod-shaped gamma ' -phases gradually grows into a rod shape, and the long rod-shaped gamma ' -reinforced phase obtained by aging for a long time has a large number of stacking faults and deformed nano twin crystals.
Comparative example 1
(1) Solution treatment: the MP159 superalloy plate is placed in a muffle furnace, heated to 1050 ℃ from room temperature along with the furnace at a heating rate of 10 ℃/min, kept for 4 hours, and then cooled to room temperature.
(2) Cryogenic rolling: pouring liquid nitrogen into an iron tank, and soaking MP159 high-temperature alloy plates with the length, width and thickness of 100mm, 50mm and 6mm treated in the step (1) in the liquid nitrogen for 15min after the vaporization of the liquid nitrogen is stable;
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 out the MP159 high-temperature alloy plate from liquid nitrogen after the roller rotates uniformly, rolling in a 5-pass rolling mode, wherein the deformation of each pass is 10% -15% of the thickness of the original plate, rapidly soaking a rolling sample in the liquid nitrogen after each pass of rolling is finished, soaking for 10-15min, and carrying out rolling deformation of the next pass after soaking is finished; until the total deformation reaches 48% of the thickness of the original MP159 superalloy sheet.
(3) Aging treatment: and (3) placing the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 0.5h, and then air-cooling to room temperature.
The transmission electron microscope microstructure diagram of the MP159 superalloy plate processed by the method of the invention in comparative example 1 is shown in figure 5, and the EDS element distribution diagram is shown in figure 6. As can be seen from fig. 5 and 6, the alloy does not exhibit a precipitated phase and the elements are uniformly distributed.
Comparative example 2
And (3) carrying out a common room-temperature rolling process on the MP159 high-temperature alloy plate:
(1) Solution treatment: the MP159 superalloy plate is placed in a muffle furnace, heated to 1050 ℃ from room temperature along with the furnace at a heating rate of 10 ℃/min, kept for 4 hours, and then cooled to room temperature.
(2) And (3) 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; after the roller rotates uniformly, the MP159 high-temperature alloy plate with the length, the width and the thickness of 100mm, 50mm and 6mm after the solution treatment is rolled and deformed. The total rolling deformation is 48% of the original plate thickness of the MP159 superalloy, rolling is carried out in 5 passes, the deformation of each pass is 10% of the original plate thickness, until the total deformation reaches 48% of the original plate thickness of the MP159 superalloy, and the MP159 superalloy plate with 48% of rolling deformation under the room temperature condition is obtained.
(3) Aging treatment: and (3) placing the MP159 high-temperature alloy plate rolled in the step (2) into a muffle furnace at 800 ℃, preserving heat for 25 hours, and then cooling to room temperature by air.
The transmission electron microscopic structure diagram of the MP159 superalloy plate processed by the comparative example 2 is shown in fig. 7, wherein (a) is an aged precipitated phase, (b) is an enlarged picture of the precipitated phase, (c) is a selected area electron diffraction pattern of the precipitated phase, and (c) the upper left small image is a selected area electron diffraction pattern of the area, so as to prove the composition condition of the area phase. As can be seen from fig. 7, the precipitated phase in the alloy is in a short rod shape, and the selected-area electron diffraction spots prove that the structure is still the L12 superlattice gamma' phase, but no diffraction spots of nano twin crystals and stacking faults exist.
Performance testing
In order to test the corrosion resistance, the MP159 high-temperature alloy plate treated by the method of example 2 in which a long rod-shaped gamma 'strengthening phase with a large amount of faults and deformation nano twin crystals is precipitated after aging for 25 hours and the short rod-shaped gamma' relative proportion 2 in which no nano twin crystals are precipitated after aging for 25 hours is subjected to hot corrosion resistance test, and a salt solution (75 wt% Na) is sprayed by adopting a salt solution spraying method 2 SO 4 +25wt% NaCl) was uniformly sprayed on the surface of the alloy sample (MP 159 superalloy plate treated in example 2 and comparative example 2), and then the alloy sample with attached salt was weighed until the deposition rate reached 6-6.5mg/cm 2 . The sample with attached salt was placed in a muffle furnace at 800 ℃ for incubation. Taking 5h as one cycle, taking out the sample from the furnace after each cycle, and air-cooling to room temperature. The cooling rate was 2.5℃per minute. 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, a salt layer was again deposited on the surface of the alloy coupon for up to 50 hours, i.e., 10 cycles, followed by air cooling to room temperature.
In fig. 8, (a) is an overall change chart of the mass loss of the MP159 superalloy sheet material with hot corrosion time in example 2 and comparative example 2, and (b) is a change chart of the mass loss of the MP159 superalloy sheet material with hot corrosion time in example 2 and comparative example 2 in the second stage (in the drawing, RTR48 means that 48% of MP159 is comparative example 2 rolled at room temperature, and cr48 means 48% of MP159 is example 2 deep-cold rolled). As can be seen from fig. 8, the hot corrosion profile can be divided into three stages according to the weight loss of the hot corrosion coupon. In the first stage (cycles 1 to 2), since 48% of MP159 superalloy sheet material was not precipitated with a rod-like gamma '-strengthening phase in the deep cold rolling at 0.5h, and the long rod-like gamma' -strengthening phase was not precipitated in the alloy sample at 2h, the same trend in weight loss was observed with the alloy sample of comparative example 2, and the difference was very small. Along with the extension of the aging time, the size of the rod-shaped gamma' -strengthening phase becomes thicker for 25 hours, and the quantity is also gradually increasedThe more stacking faults and deformed nanometer twin crystals are arranged in the nano-crystal structure. It can be seen that the weight loss of the alloy sample of example 2 in the second stage (cycles 2 to 6) is always smaller than that of comparative example 2, indicating that the alloy sample of example 2 of the present invention has higher hot corrosion resistance than that of the alloy sample of comparative example 2. In particular, the difference in weight loss between the alloy samples of comparative example 2 and example 2 was the greatest in the 4 th hot corrosion cycle, reaching 19.65mg cm -2 。
To further confirm that the hot corrosion resistance of the alloy is related to the long rod-like gamma prime strengthening phase deposited after aging, fig. 9 and 10 are respectively a cross-sectional transmission electron micrograph and EDS image of the example 2 alloy sample at 800 ℃ for the 5 th cycle, i.e., after aging for 25 hours, and fig. 11 and 12 are respectively a cross-sectional transmission electron micrograph and EDS image of the comparative example 2 alloy sample at 800 ℃ for the 5 th cycle, i.e., after aging for 25 hours. It can be seen that the alloy sample of example 2 of the present invention forms a more uniform, planar, more dense oxide layer after hot corrosion than the 48% rolled sample at room temperature (comparative example 2). The method is characterized in that a 48% alloy sample prepared by deep cold rolling after 25 hours is precipitated with a long rod-shaped gamma 'strengthening phase with a large amount of faults and deformation nano twin crystals, the large amount of faults and deformation nano twin crystals in the long rod-shaped gamma' strengthening phase can be used as effective channels for outwards diffusing 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 embodiments are only illustrative of the preferred embodiments of the present invention and are not intended to limit the scope of the present invention, and various modifications and improvements made by those skilled in the art to the technical solutions of the present invention should fall within the protection scope defined by the claims of the present invention without departing from the design spirit of the present invention.
Claims (6)
1. The preparation method of the cobalt-based alloy with a large number of stacking faults and deformation nanometer twin crystal long rod-shaped phase structures is characterized by comprising the following steps of:
(1) Heating and preserving heat of the MP159 high-temperature alloy plate, and then cooling to room temperature by water;
(2) Immersing the MP159 high-temperature alloy plate processed in the step (1) in liquid nitrogen, and performing cryogenic rolling;
(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 step (3), the temperature of the aging heat treatment is 800 ℃, and the heat preservation time is 2-25h;
in the step (2), the deformation of the MP159 superalloy sheet material after cryogenic rolling is 48% of the original thickness.
2. The method according to claim 1, wherein in the step (1), the temperature is raised to 1050℃and the temperature is kept for 4 hours.
3. The method according to claim 1, wherein in the step (2), the mixture is immersed in liquid nitrogen for 15 minutes.
4. The method according to claim 1, wherein in the step (2), the deep cold rolling is performed by multi-pass rolling, and after each pass of rolling is completed, the deep cold rolling is rapidly immersed in liquid nitrogen for 10 minutes, and then the next pass of rolling is performed.
5. The method of claim 4, wherein the reduction per pass is 10% of the original thickness of the MP159 superalloy sheet.
6. A cobalt-based alloy having a long rod-like phase structure of a plurality of layer errors and deformed nano twin crystals prepared by the preparation method of any one of claims 1 to 5.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211165897.4A CN115846403B (en) | 2022-09-23 | 2022-09-23 | Cobalt-based alloy with long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211165897.4A CN115846403B (en) | 2022-09-23 | 2022-09-23 | Cobalt-based alloy with long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115846403A CN115846403A (en) | 2023-03-28 |
| CN115846403B true CN115846403B (en) | 2023-08-15 |
Family
ID=85661117
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211165897.4A Active CN115846403B (en) | 2022-09-23 | 2022-09-23 | Cobalt-based alloy with long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115846403B (en) |
Citations (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5665180A (en) * | 1995-06-07 | 1997-09-09 | The United States Of America As Represented By The Secretary Of The Air Force | Method for hot rolling single crystal nickel base superalloys |
| WO2003018856A2 (en) * | 2001-02-09 | 2003-03-06 | Questek Innovations Llc | Nanocarbide precipitation strengthened ultrahigh-strength, corrosion resistant, structural steels |
| CN108018509A (en) * | 2017-12-19 | 2018-05-11 | 重庆大学 | A kind of deformation heat treatment method for improving aluminum alloy rolled plate mechanical property |
| CN110055479A (en) * | 2019-05-30 | 2019-07-26 | 常州大学 | A kind of 800MPa grades of highly conductive novel Cu-Cr-Zr alloy and preparation method thereof |
| CN110964957A (en) * | 2019-12-26 | 2020-04-07 | 北京工业大学 | Cryogenic rolling and aging treatment process for high-strength Al-Zn-Mg alloy |
| CN111363949A (en) * | 2020-03-18 | 2020-07-03 | 北京科技大学 | Short-process preparation method of high-strength high-elasticity Cu-Ni-Mn alloy |
| CN111549266A (en) * | 2020-05-27 | 2020-08-18 | 北京科技大学 | Tissue regulation and control method for improving forming performance of aluminum alloy plate of vehicle body structure |
| CN111607719A (en) * | 2019-02-26 | 2020-09-01 | 南京理工大学 | Nickel-based alloy containing stacking fault and gamma' phase composite structure and preparation method thereof |
| WO2020249107A1 (en) * | 2019-06-14 | 2020-12-17 | 西安热工研究院有限公司 | Precipitation-strengthened nickel-based high-chromium superalloy and preparation method therefor |
| WO2020249113A1 (en) * | 2019-06-14 | 2020-12-17 | 西安热工研究院有限公司 | Low-chromium corrosion-resistant high-strength polycrystalline high-temperature alloy and preparation method therefor |
| CN113234963A (en) * | 2021-05-19 | 2021-08-10 | 沈阳航空航天大学 | Nickel-chromium-based superalloy for room temperature and low temperature environment and preparation method thereof |
| CN113444958A (en) * | 2021-06-28 | 2021-09-28 | 威海蓝谷材料分析研究院有限公司 | High-strength high-toughness lamellar isomeric medium-entropy alloy and preparation method thereof |
| CN113502427A (en) * | 2021-06-23 | 2021-10-15 | 沈阳航空航天大学 | Co-Ni-Cr-based alloy with strength grade of 2.3GPa and preparation method thereof |
| WO2021223759A1 (en) * | 2020-05-08 | 2021-11-11 | 华能国际电力股份有限公司 | High-strength and corrosion-resistant nickel-based polycrystalline high-temperature alloy and preparation method therefor |
| CN114214583A (en) * | 2021-12-16 | 2022-03-22 | 西北工业大学 | Aging heat treatment process for high-efficiency reinforced nickel-based high-temperature alloy |
| WO2022160457A1 (en) * | 2021-01-29 | 2022-08-04 | 山东省科学院新材料研究所 | Heat treatment strengthening process for aluminum and magnesium as-cast alloy and application thereof |
| CN114990380A (en) * | 2022-06-24 | 2022-09-02 | 上海交通大学 | Beryllium-free super high-strength high-toughness copper alloy and preparation method thereof |
-
2022
- 2022-09-23 CN CN202211165897.4A patent/CN115846403B/en active Active
Patent Citations (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5665180A (en) * | 1995-06-07 | 1997-09-09 | The United States Of America As Represented By The Secretary Of The Air Force | Method for hot rolling single crystal nickel base superalloys |
| WO2003018856A2 (en) * | 2001-02-09 | 2003-03-06 | Questek Innovations Llc | Nanocarbide precipitation strengthened ultrahigh-strength, corrosion resistant, structural steels |
| CN108018509A (en) * | 2017-12-19 | 2018-05-11 | 重庆大学 | A kind of deformation heat treatment method for improving aluminum alloy rolled plate mechanical property |
| CN111607719A (en) * | 2019-02-26 | 2020-09-01 | 南京理工大学 | Nickel-based alloy containing stacking fault and gamma' phase composite structure and preparation method thereof |
| CN110055479A (en) * | 2019-05-30 | 2019-07-26 | 常州大学 | A kind of 800MPa grades of highly conductive novel Cu-Cr-Zr alloy and preparation method thereof |
| WO2020249113A1 (en) * | 2019-06-14 | 2020-12-17 | 西安热工研究院有限公司 | Low-chromium corrosion-resistant high-strength polycrystalline high-temperature alloy and preparation method therefor |
| WO2020249107A1 (en) * | 2019-06-14 | 2020-12-17 | 西安热工研究院有限公司 | Precipitation-strengthened nickel-based high-chromium superalloy and preparation method therefor |
| CN110964957A (en) * | 2019-12-26 | 2020-04-07 | 北京工业大学 | Cryogenic rolling and aging treatment process for high-strength Al-Zn-Mg alloy |
| CN111363949A (en) * | 2020-03-18 | 2020-07-03 | 北京科技大学 | Short-process preparation method of high-strength high-elasticity Cu-Ni-Mn alloy |
| WO2021223759A1 (en) * | 2020-05-08 | 2021-11-11 | 华能国际电力股份有限公司 | High-strength and corrosion-resistant nickel-based polycrystalline high-temperature alloy and preparation method therefor |
| CN111549266A (en) * | 2020-05-27 | 2020-08-18 | 北京科技大学 | Tissue regulation and control method for improving forming performance of aluminum alloy plate of vehicle body structure |
| WO2022160457A1 (en) * | 2021-01-29 | 2022-08-04 | 山东省科学院新材料研究所 | Heat treatment strengthening process for aluminum and magnesium as-cast alloy and application thereof |
| CN113234963A (en) * | 2021-05-19 | 2021-08-10 | 沈阳航空航天大学 | Nickel-chromium-based superalloy for room temperature and low temperature environment and preparation method thereof |
| CN113502427A (en) * | 2021-06-23 | 2021-10-15 | 沈阳航空航天大学 | Co-Ni-Cr-based alloy with strength grade of 2.3GPa and preparation method thereof |
| CN113444958A (en) * | 2021-06-28 | 2021-09-28 | 威海蓝谷材料分析研究院有限公司 | High-strength high-toughness lamellar isomeric medium-entropy alloy and preparation method thereof |
| CN114214583A (en) * | 2021-12-16 | 2022-03-22 | 西北工业大学 | Aging heat treatment process for high-efficiency reinforced nickel-based high-temperature alloy |
| CN114990380A (en) * | 2022-06-24 | 2022-09-02 | 上海交通大学 | Beryllium-free super high-strength high-toughness copper alloy and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| Microstructure evolution and strengthening mechanisms of MP159 superalloy during room temperature rolling and cryorolling;W.W.Zhang;Journal of Alloys and Compounds(第908期);164667 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115846403A (en) | 2023-03-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR102236938B1 (en) | Twinning/transformation induced plasticity high entropy steels and method for manufacturing the same | |
| Yuan et al. | Influence of process parameters and heat treatments on the microstructures and dynamic mechanical behaviors of Inconel 718 superalloy manufactured by laser metal deposition | |
| Luo et al. | Selective laser melting of an equiatomic AlCrCuFeNi high-entropy alloy: Processability, non-equilibrium microstructure and mechanical behavior | |
| Shahwaz et al. | A critical review on the microstructure and mechanical properties correlation of additively manufactured nickel-based superalloys | |
| Unocic et al. | High-temperature performance of UNS N07718 processed by additive manufacturing | |
| Chen et al. | Microstructures and mechanical behaviors of additive manufactured Inconel 625 alloys via selective laser melting and laser engineered net shaping | |
| Cheng et al. | The effect of subsequent heating treatment on the microstructure and mechanical properties of additive manufactured Hastelloy X alloy | |
| Ghaderi et al. | Microstructural evolution and mechanical properties of Al0. 5CoCrFeNi high-entropy alloy after cold rolling and annealing treatments | |
| Zhang et al. | The dynamic recrystallization evolution and kinetics of Ni–18.3 Cr–6.4 Co–5.9 W–4Mo–2.19 Al–1.16 Ti superalloy during hot deformation | |
| Sitek et al. | Influence of an aluminizing process on the microstructure and tensile strength of the nickel superalloy IN 718 produced by the Selective Laser Melting | |
| Zhang et al. | Enhancement of fatigue resistance of additively manufactured 304L SS by unique heterogeneous microstructure | |
| Zhao et al. | Impact of homogenization on microstructure-property relationships of Inconel 718 alloy prepared by laser powder bed fusion | |
| CN113025932A (en) | Preparation method of fine-grain and uniform-precipitation-phase nickel-based high-temperature alloy | |
| CN114182139B (en) | Precipitation strengthening nickel-based high-temperature alloy and preparation method thereof | |
| Liu et al. | Recrystallization and associated twinning evolution in nickel-based GH4141 Superalloy during annealing | |
| Wang et al. | Laser-clad Al-Ti-Zr and Cr-Ti-Zr coatings on Zr alloy: composition-induced microstructural and hardness differences | |
| Lan et al. | Significant transitions of microstructure and mechanical properties in laser additive manufacturing AlCoCrFeNi2. 1 eutectic high-entropy alloy under heat treatment | |
| Chen et al. | Microstructure and mechanical properties of a Monel K-500 alloy fabricated by directed energy deposition | |
| CN115846403B (en) | Cobalt-based alloy with long rod-shaped phase structure of a large number of stacking faults and deformation nanometer twin crystals and preparation method thereof | |
| Gan et al. | Tuning the mechanical properties of powder bed fusion printed CoCrFeNiMn high-entropy alloys by annealing and hot isostatic pressing | |
| Baskov et al. | Structure and properties of ep741np heat-resistant nickel alloy produced by selective laser melting | |
| Kumar et al. | High entropy alloys: laboratory to industrial attempt | |
| CN111441020A (en) | Method for preparing TC4 titanium alloy sputtering target material at low cost | |
| Zheng et al. | The Anisotropy of Mechanical Properties Response on Crystallographic Features of Gh5188 Superalloy Fabricated by Laser Powder Bed Fusion | |
| CN114318194B (en) | Nickel-based casting high-temperature alloy, heat treatment method thereof and alloy casting |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |