CN113308627A - Nickel-based alloy containing carbide and nano twin crystal composite structure and preparation method thereof - Google Patents
Nickel-based alloy containing carbide and nano twin crystal composite structure and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a nickel-based alloy containing a carbide and nano twin crystal composite structure and a preparation method thereof, and relates to the technical field of nano-structure metal materials. The organization structure of the surface layer of the nickel-based alloy is a composite structure of carbide and nanometer twin crystal, and the carbide is dispersed and distributed on the nanometer twin crystal to form the composite structure of the carbide and the nanometer twin crystal. The method is characterized in that the nickel-based alloy is treated by successively utilizing surface mechanical rolling treatment and aging treatment, so that a nano twin crystal and carbide composite structure is prepared on the surface layer of the nickel-based alloy. The nano twin crystal lamella spacing in the composite structure is 15-50 nm, the carbide size is 5-50 nm, the micro hardness of the structure is 4.9-5.2 GPa, which is 1.3-1.9 times of that of the nickel-based alloy before surface treatment, so that the hardness of the nickel-based alloy is integrally improved, and the nickel-based alloy has thermal stability.
Description
Technical Field
The invention relates to the technical field of nano-structure metal materials, in particular to a nickel-based alloy containing a carbide and nano-twin crystal composite structure with higher hardness and thermal stability and a preparation method thereof.
Background
The nickel-based alloy has excellent oxidation resistance and stronger corrosion resistance, and is mainly applied to the industrial fields of aerospace, mechanical manufacturing and the like. The nickel-based original structure is mainly composed of original grains with larger sizes, and the overall structure hardness is lower. In order to increase the hardness of the nickel-based alloy, many scientists have studied over centuries and have proposed a number of methods for strengthening materials, including solid solution strengthening, second phase strengthening, and plastic deformation strengthening. It can be found that although the methods of solid solution strengthening and second phase strengthening can significantly improve the hardness of the alloy, the addition of alloying elements will change the physical and chemical properties of the material. On the other hand, defects such as grain boundaries, dislocations, etc. must be introduced into the material by plastic deformation, and these defects can effectively increase the alloy hardness. This plastic deformation method does not change the chemical composition of the material, but cannot maintain plasticity and thermal stability, as compared with solution treatment and second phase strengthening. The documents Talin A, Marquis E A, Goods S H, et al, Thermal stability of Ni-Mn electrodispositides [ J ]. Acta Materialia, 2006, 54(7): 1935-. However, after the nanocrystalline Ni-Mn alloy is subjected to aging treatment of keeping the temperature at 600 ℃ for 1 h, the microhardness is 2.6 GPa, and after the nanocrystalline Ni-Mn alloy is aged at 700 ℃, the microhardness is only 1.9 GPa after the nanocrystalline Ni-Mn alloy is kept the temperature for 1 h. The coarsening temperature of the nanocrystalline nickel-based alloy is indicated in the literature to be 600 ℃, indicating that the sample has acceptable thermal stability, but lower hardness.
The document Hu J, Y.N.S, K.L. Thermal analysis of electrodeposited nano-grained Ni-Mo alloys [ J ]. Scripta Materialia, 2018, 154: 182: 185. Zhonghu et al prepare nanocrystalline Ni-Mo alloy by electrolytic deposition process, the grain size is 14.0 +/-3.8 nm, and the micro hardness of the material is 5.8 GPa. The nanocrystalline Ni-Mo alloy is subjected to aging treatment at 600 ℃ for 1 h, and then has microhardness of 3.2 GPa, and is aged at 700 ℃ for 1 h, and the microhardness is still 2.9 GPa. The grain size of the nanocrystalline Ni-Mo alloy is only increased to 17.9 +/-4.7 nm after the aging at 746 +/-3 ℃. The hardness of the nanocrystalline nickel-based alloy prepared by the method is improved to a certain extent, and the thermal stability is good.
Although the existing plastic deformation technology can refine grains on pure nickel and nickel-based alloy to improve the hardness of the material, the deformation degree of the material is not enough or difficult to regulate, so that the precise regulation becomes a difficult problem; furthermore, the increase in hardness is limited from place to place in practical applications because it is generally necessary to sacrifice plasticity at the expense of difficulty in maintaining thermal stability during temperature rise.
Disclosure of Invention
The invention aims to provide a nickel-based alloy containing a carbide and nano twin crystal composite structure and a preparation method thereof, wherein the nickel-based alloy has higher hardness and thermal stability simultaneously under the combined action of the carbide and the nano twin crystal structure.
The technical solution for realizing the purpose of the invention is as follows:
the nickel-based alloy with the composite structure of the carbide and the nanometer twin crystal has the structure that the surface layer of the nickel-based alloy is of the composite structure consisting of the nanometer twin crystal and the carbide, and the carbide is dispersed and distributed on the nanometer twin crystal structure, so that the nickel-based alloy has high hardness and thermal stability.
Preferably, the higher hardness means that the hardness of the nickel-based alloy is not less than 4 GPa.
Preferably, the thermal stability refers to that the nickel-based alloy is kept for 1 hour at the temperature of more than 500 ℃, the structural size of the nickel-based alloy does not exceed 100nm, and the structure is maintained in a nanometer scale.
Specifically, the nano twin crystal lamella spacing is distributed between 15 nm and 50 nm, the carbide size is distributed between 5 nm and 50 nm, and the thickness of the tissue structure of the surface layer of the nickel-based alloy is 100-300 mu m.
Preferably, the nickel-based alloy comprises, in atomic percentage (at.%), 59.50-64.0% of Ni, 20.0-24.0% of Cr, 13.0-15.0% of W, 1.0-2.0% of Mo, 0.94-1.33% of Co, 0.3-1.0% of Mn, 0.25-0.75% of Si, 0.2-0.5% of Al, 0.2-0.5% of Fe, 0.05-0.15% of C, 0.001-0.03% of P, and 0.001-0.015% of S.
The method for preparing the nickel-based alloy comprises the following specific steps:
(1) carrying out solution treatment on the nickel-based alloy to be treated to obtain a single-phase nickel-based alloy with a uniform structure;
(2) performing multi-pass treatment on the single-phase nickel-based alloy by utilizing surface mechanical rolling treatment to obtain the nickel-based alloy with the nanometer twin crystal structure;
(3) carrying out aging treatment on the nickel-based alloy with the nanometer twin crystal structure obtained in the step (2), and precipitating carbide as a second phase to finally obtain the nickel-based alloy with the composite structure of the carbide and the nanometer twin crystal structure,
the surface mechanical rolling treatment adopts a surface mechanical rolling treatment system, the surface mechanical rolling processing treatment system comprises a treatment cutter and a cooling system, the high-hardness cutter is used for carrying out mechanical rolling treatment on the single-phase nickel-based alloy with the uniform structure, and the cooling system is used for reducing the temperature rise in the surface mechanical rolling process.
Preferably, the solution treatment process is as follows: carrying out solution treatment for 2h at 1220 ℃, and cooling to room temperature by water cooling.
Preferably, the total pass of the surface mechanical rolling treatment is 4 passes.
Preferably, the cutter head part of the processing cutter is a hard alloy ball, the hard alloy ball is made of WC-Co alloy, and the diameter of the hard alloy ball is 4-10 nm; the cooling system is liquid nitrogen gas cooling.
Preferably, the shape of the nickel-based alloy is a rod, and the surface mechanical rolling treatment specifically comprises the following steps: the nickel-based alloy is axially rotated around the nickel-based alloy, the hard alloy ball of the processing cutter is contacted with the surface of the single-phase nickel-based alloy with a uniform structure, the pressing is kept to a certain depth, the processing cutter is fed, and meanwhile, the processing cutter moves from one end of the rod-shaped sample to the other end, so that the process finishes one-pass processing; after the above processes are repeated for a plurality of times, the nanometer twin crystal structure is formed on the surface of the nickel-based alloy; the depth of the hard alloy ball pressed into the surface of the nickel-based alloy in each pass of treatment is determined according to the thickness of the required nano twin crystal structure layer.
Specifically, the nickel-based alloy is rod-shaped, the diameter of the nickel-based alloy is 8-20 mm, and the length of the nickel-based alloy is 50-80 mm.
Specifically, the rotating speed of the nickel-based alloy rotating around the axial direction of the nickel-based alloy is 100-1000 r/min, and the feeding speed of the machining cutter along the axial direction of the nickel-based alloy is 40-80 mm/min.
Specifically, the reduction depth of the hard alloy ball-shaped cutter on the surface of the nickel-based alloy in each processing pass is 20-80 μm.
Preferably, the aging treatment temperature is 600 or 700 ℃, and the aging treatment time is 2 h.
Compared with the prior art, the invention has the following remarkable advantages:
(1) the invention utilizes the method of surface mechanical rolling treatment to obtain a nano twin crystal structure composite structure containing carbide on the surface of the nickel-based alloy, the strengthening mechanism of the nano twin crystal structure obtained on the surface of the nickel-based alloy by the surface mechanical rolling treatment can be explained by Hall-Petch relationship, and the hardness of the nickel-based alloy is obviously improved because the spacing of the twin crystal layers is only a few nanometers. And the precipitation of the carbide after the aging treatment can further improve the resistance of the movement of the nano twin crystal interface, so that the structure is stably kept in place. Therefore, the composite structure of the carbide and the nanometer twin crystal structure effectively improves the hardness and the thermal stability of the nickel-based alloy.
(2) The carbide and nanometer twin crystal composite structure is prepared in the nickel-based alloy through surface mechanical rolling treatment and aging treatment, and deformation process parameters are easy to control based on the surface mechanical rolling treatment technology. The technology can optimize surface mechanical treatment processing parameters, cutter parameters and the like according to the characteristics of a material to be processed, finally control the thickness of the nanometer twin crystal structure layer and obtain a required structure.
(3) The surface mechanical rolling treatment method used in the invention prepares a nanometer twin crystal structure with a certain thickness on the surface layer of the nickel-based alloy, which is different from a uniform structure material prepared by the traditional method. The invention avoids pollution on the premise of not changing the chemical components of the material, can improve the hardness and the thermal stability of the nickel-based alloy by changing the microstructure, and is more convenient and environment-friendly.
The present invention is described in further detail below with reference to the attached drawing figures.
Drawings
FIG. 1 is a high resolution TEM image of a nano-twin structure in the Ni-based alloy of example 1.
FIG. 2 is a transmission electron microscope photograph of a nano-twin structure in the nickel-based alloy in example 2.
FIG. 3 is a comparison of the micro-hardness of the nickel-base alloys of examples 1 and 2 and the prior art nickel-base alloys.
Detailed Description
The invention is explained in further detail below with reference to the figures and examples.
A nickel-based alloy containing a carbide and nano twin crystal composite structure and a preparation method thereof are provided, and the nickel-based alloy containing the structure has higher hardness and thermal stability. Firstly, the nickel base alloy to be treated is subjected to solution treatment to obtain a single-phase uniform structure. Then, the uniform single-phase nickel-based alloy is subjected to surface mechanical rolling treatment, a nano twin crystal structure is obtained on the surface layer of the single-phase nickel-based alloy, then the nickel-based alloy is subjected to aging treatment, so that carbide is precipitated in the nano twin crystal structure, and finally a carbide and nano twin crystal composite structure is obtained, and the hardness and the thermal stability of the nickel-based alloy are remarkably improved by the structure.
When the surface mechanical rolling treatment is adopted to carry out surface treatment on the nickel-based alloy, the surface mechanical rolling treatment system comprises a treatment cutter and a cooling system. The tool bit part of the tool is a hard alloy ball which is made of WC-Co alloy, and the diameter of the hard alloy ball is 4-10 mm. Liquid nitrogen gas is adopted for cooling in the cooling treatment process so as to reduce the temperature rise in the treatment process. For the low-layer fault energy nickel-based alloy, the surface mechanical rolling treatment process does not need cooling, and the room temperature is kept.
In the carbide and nano-twin composite structure, the interlayer spacing of the nano-twin and the mixed sheet of the matrix is distributed between 15 and 50 nm, and the size of the carbide second phase is distributed between 5 and 50 nm.
The surface mechanical rolling treatment process comprises the following steps: the rod-shaped nickel-based alloy is axially rotated along the self direction, the hard alloy ball of the processing cutter is contacted with the surface of the rod-shaped nickel-based alloy and pressed into the surface of the rod-shaped nickel-based alloy to a certain depth, and then the hard alloy ball moves from one end of the workpiece to the other end of the workpiece along the surface of the rod-shaped nickel-based alloy rotating piece to complete one pass processing; repeating the above process to form a plastic deformation layer on the surface of the nickel-based alloy; the rod-shaped nickel base alloy has the diameter of 8-20 mm and the length of 50-80 mm. The rotating speed of the rod-shaped nickel-based alloy rotating member is 100-800 r/min, the feeding speed of the treatment cutter along the axial direction of the rod-shaped nickel-based alloy rotating member is 40-80 mm/min, the pressing depth of the hard alloy ball cutter head on the surface of the rod-shaped nickel-based alloy in each treatment pass is 20-80 mu m, and the treatment pass is 4.
The aging treatment process comprises the following steps: and (3) heating the box type electric furnace to a preset aging temperature, then putting the nickel-based alloy with the nano twin crystal structure after the surface mechanical rolling treatment into the furnace, preserving the heat for a certain time, taking out the nickel-based alloy, and naturally cooling the nickel-based alloy in the air.
The aging time is as follows: 2h, aging temperature: 600. 700 ℃.
Example 1
(1) The chemical elements in the nickel-base alloy to be treated are measured in atomic percent (at.%): 63.02% of Ni, 27.38% of Cr, 4.55% of W, 1.35% of Mo, 1.22% of Co, 0.52% of Mn, 0.60% of Si, 0.60% of Al, 0.26% of Fe, 0.47% of C, 0.02% of P and 0.01% of S. And (3) carrying out solid solution treatment on the nickel-based alloy at the treatment temperature of 1220 ℃ for 2h, and then cooling the nickel-based alloy to room temperature by water to obtain the single-phase nickel-based alloy with a uniform structure.
(2) And (3) repeatedly performing surface mechanical rolling treatment on the single-phase nickel-based alloy with a uniform structure by utilizing the surface mechanical rolling treatment, and finally obtaining the nickel-based alloy with the nanometer twin crystal structure by utilizing the surface mechanical rolling treatment with the total pass of 4.
(3) And (3) carrying out aging treatment on the nickel-based alloy containing the nano twin crystal structure in the step (2), wherein the aging temperature is 600 ℃, the aging time is 2 hours, and finally obtaining the nickel-based alloy containing the carbide and the nano twin crystal composite structure by utilizing the aging treatment.
The surface mechanical rolling treatment process comprises the following steps: the diameter of the uniform single-phase rod-shaped nickel-based alloy is 16 mm, and the autorotation speed of the alloy rod is 600 r/min. The processing cutter head is a WC-Co hard alloy ball with the thickness of 8 mm, the feeding speed is 40 mm/min, the pressing depth of the hard alloy ball cutter head on the surface of the nickel-based alloy in each processing pass is 20 mu m, and the total processing pass is 4.
The organization structure of the surface layer of the nickel-based alloy obtained in the embodiment 1 is a carbide and nano-twin composite structure, wherein the thickness of the carbide and nano-twin composite structure is 100 micrometers, the distance between nano-twin lamellar layers is 23.6 nm, the size of the carbide is 6 nm, the number of the nickel-based alloy in the embodiment is #1, as shown in a high-resolution transmission electron microscope image of the carbide and nano-twin composite structure in the nickel-based alloy, the micro-hardness of the structure is 5.2 GPa. The structure obviously improves the hardness of the nickel-based alloy and keeps thermal stability.
Example 2
The difference from the embodiment 1 is that:
the nickel-based alloy containing the carbide and the nanometer twin crystal composite structure is obtained by utilizing surface mechanical rolling treatment and aging treatment, and the carbide and nanometer twin crystal composite structure has higher hardness and thermal stability. The chemical elements in the nickel-based alloy are the same as those in example 1. The surface mechanical rolling treatment parameters are as follows: the diameter of the rod-shaped nickel-based alloy is 16 mm, the rotating speed is 600 r/min, the processing cutter head is a WC-Co hard alloy ball with the diameter of 8 mm, the feeding speed is 40 mm/min, the pressing depth of the hard alloy ball cutter head on the surface of the nickel-based alloy in each processing pass is 20 mu m, and the total processing pass is 4. The aging treatment parameters are as follows: the aging temperature is 700 ℃, and the aging time is 2 h.
The thickness of the composite structure containing carbide and nano twin crystals on the surface layer of the nickel-based alloy obtained in the embodiment is 100 micrometers, wherein the interlayer spacing of the nano twin crystals is 37.5 nm, the size of the carbide is 36.4 nm, the number of the nickel-based alloy in the embodiment is #2, as shown in a transmission electron microscope image of the composite structure containing carbide and nano twin crystals in the nickel-based alloy, the micro hardness of the structure is 4.9 GPa. The structure significantly improves the hardness of the nickel-base alloy and maintains thermal stability.
Comparative example 1
The documents Talin A, Marquis E A, Goods S H, et al, Thermal stability of Ni-Mn electrodepots [ J ]. Acta Materialia, 2006, 54(7): 1935-. The nanocrystalline Ni-Mn alloy is subjected to aging treatment at 600 ℃ for 1 h, and then has microhardness of 2.6 GPa, and is aged at 700 ℃ for 1 h, and the microhardness is only 1.9 GPa. The nanocrystalline nickel-based alloy prepared by the method has lower hardness.
Comparative example 2
The document Hu J, Y.N.S, K.L. Thermal analysis of electrodeposited nano-grained Ni-Mo alloys [ J ]. Scripta Materialia, 2018, 154: 182: 185. Zhonghu et al prepare nanocrystalline Ni-Mo alloy by electrolytic deposition process, the grain size is 14.0 +/-3.8 nm, and the micro hardness of the material is 5.8 GPa. The nanocrystalline Ni-Mo alloy is subjected to aging treatment at 600 ℃ for 1 h, and then has microhardness of 3.2 GPa, and is aged at 700 ℃ for 1 h, and the microhardness is only 2.9 GPa. The grain size of the nanocrystalline Ni-Mo alloy is only increased to 17.9 +/-4.7 nm after the nanocrystalline Ni-Mo alloy is aged at 746 +/-3 ℃, which shows that the method maintains higher thermal stability in temperature rise. The nanocrystalline nickel-based alloy prepared by the method has good thermal stability and low hardness.
The hardness test of example 1-2 shows that the nickel-base alloy containing the composite structure of carbide and nano twin crystal has a hardness of 4.9-5.2 GPa and a micro-hardness 1.3-1.9 times that of the nickel-base alloy before treatment. Comparing the micro-hardness of the nickel-based alloys of examples 1 and 2 with the micro-hardness of the nickel-based alloys of comparative examples 1 and 2, it can be seen from fig. 3 that the nickel-based alloys treated by the process of the present invention can maintain higher hardness at 600 c and 700 c than the nickel-based alloys treated by the electrodeposition process. Meanwhile, in the examples 1 and 2, the sizes of the nanometer twin crystal structure and the carbide structure are both smaller than 100nm, and the nickel-based alloy treated by the process can keep thermal stability at 600 ℃ and 700 ℃. The conclusion also shows that the nickel-based alloy prepared by the technology has higher hardness and thermal stability.
Claims (10)
1. The nickel-based alloy with the composite structure of the carbide and the nanometer twin crystal is characterized in that the texture structure of the surface layer of the nickel-based alloy is a composite structure consisting of the nanometer twin crystal and the carbide, and the carbide is distributed on the nanometer twin crystal structure, so that the nickel-based alloy has high hardness and thermal stability.
2. The nickel-base alloy of claim 1 wherein the relatively high hardness is a hardness of not less than 4 GPa.
3. The nickel-base alloy according to claim 1, wherein the thermal stability is a heat retention of more than 500 ℃ for 1 hour, and the structural size of the nickel-base alloy does not exceed 100 nm.
4. The nickel-base alloy according to claim 1, wherein the nano twin lamella spacing in the composite structure is 15-50 nm, the carbide size is 5-50 nm, and the thickness of the texture structure of the surface layer of the nickel-base alloy is 100-300 μm.
5. Nickel-base alloy according to any of claims 1 to 3, characterized in that the composition of the nickel-base alloy is, in atomic percent (at.%): 59.50-64.0% of Ni, 20.0-24.0% of Cr, 13.0-15.0% of W, 1.0-2.0% of Mo, 0.94-1.33% of Co, 0.3-1.0% of Mn, 0.25-0.75% of Si, 0.2-0.5% of Al, 0.2-0.5% of Fe, 0.05-0.15% of C, 0.001-0.03% of P and 0.001-0.015% of S.
6. A method for preparing the nickel-base alloy according to any of claims 1 to 5, characterized by the following specific steps:
(1) carrying out solution treatment on the nickel-based alloy to be treated to obtain a single-phase nickel-based alloy with a uniform structure;
(2) performing multi-pass treatment on the single-phase nickel-based alloy by utilizing surface mechanical rolling treatment to obtain the nickel-based alloy with the nanometer twin crystal structure;
(3) carrying out aging treatment on the nickel-based alloy with the nanometer twin crystal structure obtained in the step (2), and precipitating carbide as a second phase to finally obtain the nickel-based alloy containing the carbide and the nanometer twin crystal composite structure,
the surface mechanical rolling treatment adopts a surface mechanical rolling treatment system, the surface mechanical rolling processing treatment system comprises a treatment cutter and a cooling system, the high-hardness cutter is used for carrying out mechanical rolling treatment on the single-phase nickel-based alloy with the uniform structure, and the cooling system is used for reducing the temperature rise in the surface mechanical rolling process.
7. The method of claim 6, wherein the solution treatment process is as follows: carrying out solution treatment for 2h at 1220 ℃, and cooling to room temperature by water cooling.
8. The method of claim 6, wherein the total number of passes of the surface mechanical rolling process is 4 passes.
9. The method of claim 6, wherein the nickel-based alloy is rod-shaped, and the mechanical rolling process of the surface comprises the following specific steps: the nickel-based alloy rotates around the self axial direction, the hard alloy ball of the processing cutter is contacted with the surface of the nickel-based alloy, the hard alloy ball is pressed into the nickel-based alloy to a certain depth, the processing cutter is fed, and meanwhile, the hard alloy ball moves from one end of the nickel-based alloy to the other end, and the process finishes one pass processing; after the above processes are repeated for a plurality of times, the nanometer twin crystal structure is formed on the surface of the nickel-based alloy; the depth of the hard alloy ball pressed into the surface of the nickel-based alloy in each pass of treatment is determined according to the required thickness of the nano twin crystal structure layer, wherein the diameter of the nickel-based alloy is 8-20 mm, and the length of the nickel-based alloy is 50-80 mm; the rotation speed of the nickel-based alloy rotating around the self axial direction is 100-1000 r/min, and the feeding speed is 40-80 mm/min; the reduction depth of each pass is 20-80 μm.
10. The method according to claim 6, wherein the ageing temperature is 600 or 700 ℃ and the ageing time is 2 h.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113308626A (en) * | 2020-02-27 | 2021-08-27 | 南京理工大学 | Nickel-based alloy containing gradient nano-structure and preparation method thereof |
| CN114058989A (en) * | 2021-11-17 | 2022-02-18 | 贵州大学 | Method for improving high-temperature strength of precipitation-strengthened high-temperature alloy |
| CN115216675A (en) * | 2022-07-28 | 2022-10-21 | 吉林大学 | Method for preparing superfine layered twin crystal structure on surface of aluminum alloy |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104894498A (en) * | 2015-06-09 | 2015-09-09 | 大连理工大学 | Nanometer crystal twinning ultrahigh-hardness surface forming method of nickel base alloy |
| CN109943696A (en) * | 2017-12-21 | 2019-06-28 | 中国科学院金属研究所 | A method of precipitation strengthening alloy intensity is improved using matrix nano structure |
-
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104894498A (en) * | 2015-06-09 | 2015-09-09 | 大连理工大学 | Nanometer crystal twinning ultrahigh-hardness surface forming method of nickel base alloy |
| CN109943696A (en) * | 2017-12-21 | 2019-06-28 | 中国科学院金属研究所 | A method of precipitation strengthening alloy intensity is improved using matrix nano structure |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113308626A (en) * | 2020-02-27 | 2021-08-27 | 南京理工大学 | Nickel-based alloy containing gradient nano-structure and preparation method thereof |
| CN113308626B (en) * | 2020-02-27 | 2022-03-18 | 南京理工大学 | Nickel-based alloy containing gradient nano-structure and preparation method thereof |
| CN114058989A (en) * | 2021-11-17 | 2022-02-18 | 贵州大学 | Method for improving high-temperature strength of precipitation-strengthened high-temperature alloy |
| CN115216675A (en) * | 2022-07-28 | 2022-10-21 | 吉林大学 | Method for preparing superfine layered twin crystal structure on surface of aluminum alloy |
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