CN115584454B - Method for improving high-temperature alloy performance and application of high-temperature alloy in commercial MP35N nickel-cobalt-based high-temperature alloy - Google Patents
Method for improving high-temperature alloy performance and application of high-temperature alloy in commercial MP35N nickel-cobalt-based high-temperature alloy Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 99
- 238000000034 method Methods 0.000 title claims abstract description 37
- QXZUUHYBWMWJHK-UHFFFAOYSA-N [Co].[Ni] Chemical compound [Co].[Ni] QXZUUHYBWMWJHK-UHFFFAOYSA-N 0.000 title claims abstract description 17
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 37
- 239000000463 material Substances 0.000 claims description 11
- 239000013078 crystal Substances 0.000 claims description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 8
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
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- 229910001247 waspaloy Inorganic materials 0.000 description 3
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- 229910001011 CMSX-4 Inorganic materials 0.000 description 1
- -1 IN718 Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
The invention relates to the field of high-temperature alloy, in particular to a method for improving the performance of the high-temperature alloy and application of the high-temperature alloy in commercial MP35N nickel-cobalt-based high-temperature alloy. On the premise of not depending on alloying, the high-density nano-scale stable grain boundary network structure is prepared through special plastic deformation. Further, the nickel-cobalt-based alloy with the simple component has good thermal stability at the temperature below 900 ℃; the Vickers hardness of the alloy is improved by more than 50 percent at the temperature below 800 ℃ compared with that of a superalloy without the structure with the same component; in particular at 700 ℃, ensures a steady state creep rate of 10 DEG C ‑7 s ‑1 On the premise that the creep stress is up to 1GPa, which is superior to the performance of all nickel-cobalt-based high-temperature alloys in the prior art. The invention firstly proposes to strengthen a novel structure of a high-density nano-scale stable grain boundary network in the superalloy, and the design concept is based on the regulation and control of the grain boundary self structure and the grain boundary strengthening, which are different from the common alloying means and the second-phase strengthening of the superalloy at the present stage.
Description
Technical Field
The invention relates to the field of high-temperature alloy, in particular to a method for improving the performance of the high-temperature alloy and application of the high-temperature alloy in commercial MP35N nickel-cobalt-based high-temperature alloy.
Background
The high-temperature alloy has the advantages of good high-temperature strength, excellent creep resistance and the like, is widely applied to the fields of aerospace and energy, and is an irreplaceable key material for modern national defense construction. Along with the continuous improvement of the performance requirements of weapon equipment, higher performance requirements are also provided for high-temperature alloy structural parts such as turbine discs, blades and the like. On one hand, the new generation of high-temperature alloy materials are required to have higher temperature bearing capacity, and on the other hand, the new generation of high-temperature alloy materials are required to have higher strength, so that the aims of weight reduction and synergy are fulfilled.
The high-temperature alloy at the present stage is mainly strengthened by introducing gamma-prime and gamma-prime ordered phases through alloying means, the element types are up to 10-20, and the volume fraction of the second phase is up to 10-60%. As a type of metal material with the highest alloying degree, alloying means have become increasingly weak in terms of improving the high-temperature alloy performance. For example, the room temperature yield strength of a typical GH4169 alloy in wrought superalloys is on the order of 1.1GPa, but decays rapidly to 0.7GPa at 760 ℃; furthermore, due to the problem of gamma-prime phase stability, the stable use temperature is only 650 ℃. The total amount of refractory elements (W, nb, re, mo and the like) is further improved, and on one hand, the material strength is not greatly improved; on the other hand, the precipitation of harmful phases in the alloy is aggravated; in addition, the alloy smelting, processing and other performances are poorer and worse.
In recent years, students at home and abroad try alloying means, and methods for improving the temperature bearing capacity and mechanical properties of the alloy are as follows: dislocation enhancement, fine grain enhancement, and the like. The structure prepared by the method has remarkable effect on improving the room temperature strength of the high-temperature alloy, but has no improvement on key service performances such as thermal stability, high-temperature strength, high-temperature creep and the like under the high-temperature environment (600 ℃), but has deterioration effect and cannot improve the high-temperature strength and the temperature bearing capacity of the high-temperature alloy. Therefore, at present, development of high-temperature alloy, especially high-strength (yield strength at room temperature is in the order of 2 GPa), high-temperature-bearing capacity (yield strength at 700 ℃ is in the order of 1.5 GPa), and development of high-temperature alloy with excellent creep resistance is urgently required for new design principles.
Based on this, the present invention has been made.
Disclosure of Invention
The invention aims to provide a method for improving the performance of a high-temperature alloy and application of the method in commercial MP35N nickel-cobalt-based high-temperature alloy, which is independent of alloying, and introduces a high-density nano-scale stable grain boundary network through special plastic deformation, so that the key service performances of the high-temperature alloy, such as structural heat stability, high-temperature strength, high-temperature creep and the like, are obviously improved, and the method becomes a new way for improving the performance of the high-temperature alloy.
In order to achieve the above purpose, the present invention adopts the following technical scheme:
a method for improving the performance of high-temperature alloy, prepare the stable grain boundary network of high-density nanometer scale through plastic deformation, raise the structural thermal stability of the high-temperature alloy, high-temperature intensity, key service performance of high-temperature creep obviously; plastic deformation refines the grains of the superalloy below the critical dimension and induces grain boundary relaxation, and the superalloy grain size is on the nanometer scale with a grain boundary volume fraction of >30% with relaxation characteristics and is connected to each other as a network.
According to the method for improving the performance of the high-temperature alloy, the grain size of the high-temperature alloy is smaller than 30nm.
According to the method for improving the performance of the high-temperature alloy, the high-density nano-scale stable grain boundary network prepared by plastic deformation has ultrahigh structural heat stability, the obvious grain growth temperature is more than 0.7Tm, and Tm is the melting point of the material.
The method for improving the performance of the superalloy relies on relaxation grain boundary strengthening rather than the conventional second phase of gamma 'or gamma'.
According to the method for improving the high-temperature alloy performance, the improvement of the high-temperature alloy performance depends on the structural regulation and control of the grain boundary and does not depend on alloying means.
The method for improving the performance of the high-temperature alloy obviously reduces the element types in the prior brand high-temperature alloy.
The method for improving the performance of the high-temperature alloy obviously reduces the content of aluminum, titanium and niobium elements in the prior brand high-temperature alloy.
The method for improving the performance of the superalloy is suitable for deforming the superalloy and the related fields.
The application of the method for improving the performance of the superalloy in commercial MP35N nickel cobalt-based superalloy comprises, by weight, 33-35% of Co, 19-21% of Cr, 9-11% of Mo, 1% of Ti and the balance of Ni; the high-density nano-scale stable grain boundary network is prepared by a plastic deformation process, the grain size is 8-15 nm, and the obvious growth temperature of the grains is 950-1100 ℃.
The method for improving the performance of the high-temperature alloy is applied to commercial MP35N nickel-cobalt-based high-temperature alloy, and the high-density nano-scale stable grain boundary network prepared by a plastic deformation process has the Vickers hardness of the material at 760 ℃ of up to 5.1GPa; at 700 ℃/1036MPa, the indentation steady state creep rate is as low as 10 -7 s -1 。
The design idea of the invention is as follows:
the invention enables the high-temperature alloy to obtain a high-density nano-scale stable grain boundary network through special plastic deformation on the premise of not changing or actively reducing the material components, so as to realize the key service performance of not (or less) depending on alloying and obviously improving the thermal stability, high-temperature strength, high-temperature creep and the like of the high-temperature alloy structure.
The strengthening mode of the high-performance superalloy mainly depends on precipitation phase strengthening. The means for continuously improving the alloy performance is generally to improve the alloying degree of the material, but the adoption of the means can deteriorate the process performance, and the performance improvement is not obvious.
The traditional nanocrystalline reinforcement can greatly improve the room temperature strength of the high-temperature alloy. However, this structure becomes unstable at 600 ℃ or higher, and its high-temperature strengthening and high-temperature creep properties are drastically deteriorated, so that the high-temperature alloy properties at high temperatures cannot be effectively improved.
The invention discovers that the high-temperature alloy performance can be greatly improved by regulating and controlling the self structure of the grain boundary besides the alloying means in the research process. Specifically, when the size of the nanocrystalline crystal grain prepared by the plastic deformation method is smaller than a certain critical value, the crystal boundary of the nanocrystalline crystal grain spontaneously relaxes to a stable state to form a high-density nanoscale stable crystal boundary network, so that the thermal stability is greatly improved. The high-density nano-scale stable grain boundary network has excellent strengthening capability and creep resistance at high temperature, can greatly improve the strength and temperature bearing capability of the high-temperature alloy, and obviously improves the application temperature of grain boundary strengthening in the high-temperature alloy.
The high-density nano-scale stable grain boundary network in the invention has distinct structural characteristics: the grain size is generally smaller than 30nm, the grain interior has high-density twin crystal or stacking fault and other grain boundary relaxation characteristics, the grain boundary presents low-index surface characteristics, and the volume fraction of the sigma CSL low-energy grain boundary is more than 30 percent so as to ensure that the grain boundaries are connected with each other to form a network.
The high-density nano-scale stable grain boundary network in the invention has distinct structural heat stability characteristics: the significant grain growth temperature is more than 0.7Tm, which is significantly higher than the thermal stability (0.4-0.6 Tm) of the nanostructure above the critical grain size of the alloy with the same composition. The improvement of the structural thermal stability is due to the contribution of the relaxation of the grain boundary induced below the critical grain size, and is distinguished from the improvement of the thermal stability caused by the factors such as second phase pinning in the ODS alloy.
Further, the nickel-cobalt-based alloy (MP 35N) with the simple component has good structural heat stability at the temperature below 900 ℃; the Vickers hardness of the alloy is improved by more than 50 percent at the temperature below 800 ℃ compared with that of a superalloy without the structure with the same component; especially at 700 ℃, ensures that the steady state creep rate is as low as 10 -7 s -1 On the premise that the creep stress is up to 1GPa, which is superior to the performance of all nickel-cobalt-based high-temperature alloys in the prior art. The invention firstly proposes to strengthen a novel structure of a high-density nano-scale stable grain boundary network in the superalloy, and the design concept is based on the regulation and control of the grain boundary self structure and the grain boundary strengthening, which are different from the common alloying means and the second-phase strengthening of the superalloy at the present stage.
Compared with the prior art, the invention has the advantages that:
1. the degree of dependence on alloying is small. The invention adopts a high-density nano-scale stable grain boundary network to improve the performance of the high-temperature alloy, the strengthening concept is based on the structural adjustment of the grain boundary, and is quite different from the alloying means commonly used in the prior high-temperature alloy, thereby greatly reducing the dependency of the alloy on alloy components. On one hand, the problems of high alloy cost, high smelting recovery difficulty, poor processing performance and the like associated with high alloying are solved to a certain extent in the invention. On the other hand, the invention can greatly improve the high-temperature performance of the material by prefabricating the high-density nano-scale stable grain boundary network on the premise of not changing or even actively reducing the alloy components, and the performance of the material even exceeds the performance of the material with higher alloying level. For example, the MP35N alloy used in the examples of the present invention contains only 5 constituent elements, but by prefabricating the novel nanostructured network therein, the performance of the alloy has significantly exceeded that of GH4169, waspaloy constituent element >7, and the like.
2. The performance is improved obviously. The high-density nano-scale stable grain boundary network provided by the invention has the structure that the grain size is thinned to be below the critical size, and is generally smaller than 30nm. Such a small grain size ensures both a high stability of the grain boundaries themselves and an ultra-high density of the grain boundaries in the sample. The high density grain boundaries and the strengthening effect they bring are extremely pronounced in the samples of the present invention. Taking the MP35N alloy used in the examples of the present invention as an example, the Vickers hardness at 760 ℃ is as high as 5.1GPa, which is the nickel-based superalloy with the highest strength level observed by the inventors at the same temperature so far. More significantly, at 700 ℃, steady state creep rates are as low as 10 -7 s -1 Under the condition of magnitude, the creep stress is as high as 1GPa. The related creep stress level is far higher than the complex component deformation superalloy performance under the same conditions, such as: GH4169 (0.6 GPa); in addition, the creep stress is superior to that of single-crystal high-temperature alloys with highest alloying degree, such as: SRR99 (0.8 GPa).
3. Can be overlapped with other strengthening modes. The invention mainly induces the relaxation of the grain boundary through plastic deformation, and improves the grain boundary structure to improve the performance of the high-temperature alloy. Which does not conflict with the second phase strengthening means used in conventional superalloys. Therefore, the two strengthening methods can be overlapped, so that the material performance is further improved, and a wider space is opened up for performance regulation.
4. The metal suitable for the method is a face-centered cubic structural superalloy, including iron-based, nickel-based and nickel-cobalt-based superalloys, which are required to have excellent processing performance, and deformation superalloys are preferred.
Drawings
FIG. 1 is a typical morphology of a high density nanoscale stabilized grain boundary network structure prepared by special plastic deformation in an MP35N alloy according to an embodiment of the present invention. Wherein, the graph A is a TEM morphology graph, the graph B is a high-power spectrum surface distribution graph, the graph C is a high-resolution morphology graph, and the graph D, E is a grain orientation and grain boundary characteristic graph respectively.
FIG. 2 shows the creep property of MP35N alloy with high density nano-scale stable grain boundary network structure and the comparison with different kinds of traditional high temperature alloy at 700 ℃. Wherein, the abscissa Stress is creep Stress (MPa), and the ordinate Creep strain rate is steady-state creep rate (s -1 ). IN the figure, NG-42 represents MP35N alloy with the grain size of 42nm and the common grain boundary characteristic, CG represents deformed coarse-grain MP35N alloy, multi-phase multiphase superalloy, single-phase multiphase superalloy, A286, IN800, C276, MP35N, nimonic90, waspaloy, IN718, CMSX-4/SC and SRR99/SC respectively represent different types of traditional superalloy, and SNG-9 represents MP35N alloy with the grain size of 9nm and the high-density nano-scale stable grain boundary network.
Detailed Description
In the specific implementation process, the invention prepares the high-density nano-scale stable grain boundary network structure through special plastic deformation on the premise of not depending on alloying. Wherein, the technological process and technological parameter range of special plastic deformation are as follows: and (3) under the low-temperature environment from room temperature to liquid nitrogen temperature, applying high-pressure, large-strain shearing and other extreme plastic deformation treatment to the sample, and refining the grain size of the high-temperature alloy to be below the critical size so as to induce the relaxation of grain boundaries. Wherein the applied pressure is more than 1GPa, the plastic deformation amount is more than 20, and the strain rate is more than 10 under the lower deformation amount (20-50) 3 s -1 Under the condition of higher deformation>100 The requirement for high strain rates may be reduced.
In the following, the technical solution of the present invention will be described in detail with reference to the accompanying drawings and examples, but it will be understood by those skilled in the art that the examples described below are some, but not all, examples only for illustrating the effect of the high-density nano-scale stable grain boundary network in enhancing the performance of superalloy in the present invention, and should not be construed as limiting the scope of the present invention. Based on the novel structure and embodiments of the high-density nanoscale stabilized grain boundary network, which are emphasized in the present invention, all other embodiments obtained by those of ordinary skill in the art without making any inventive effort are within the scope of the present invention.
Example 1
In this embodiment, the superalloy is a commercial MP35N alloy, comprising the following components in weight percent: 33.9% of Co, 20.9% of Cr, 10.2% of Mo, 0.9% of Ti and the balance of Ni.
The alloy of the embodiment is subjected to high-speed shearing deformation treatment, so that grains are greatly and effectively refined below a critical dimension, and grain boundary relaxation is further induced, and a novel structure of a high-density nano-scale stable grain boundary network is prepared.
The high-temperature alloy bar with the diameter of 6mm is used as a machined part, and a surface mechanical grinding treatment technology is utilized at the temperature of liquid nitrogen to carry out plastic deformation treatment on a sample by adopting high strain rate and strain quantity. The surface mechanical grinding treatment parameters are as follows: the ball head of the processing cutter is made of hard alloy, the radius of the ball head is 4mm, the horizontally arranged high-temperature alloy bar rotates at the rotating speed of 600r/min, the feeding speed of the processing cutter along the horizontal direction is 10mm/min, the rolling reduction of the processing cutter is 20 mu m each time, and the processing passes are 10 times.
As shown in FIG. 1, after the treatment, the gradient sample has a deep structure with 0-20 μm layer on the outermost layer, the grain size is extremely fine, the volume fraction of sigma CSL (coincident lattice grain boundary) reaches 9nm, and the sigma CSL is up to 44% and is mutually linked into a network (FIG. 1E). The sample has obvious grain growth temperature up to 1000 ℃, and accords with the structure and stability characteristics of the high-density nano-scale stable grain boundary network. The grain size in the depth of the subsurface layer which is larger than 20 mu m (20-50 mu m) is 42nm, the obvious grain growth temperature is up to 750 ℃, and the nano-crystal structure is a traditional nano-crystal structure.
The Vickers hardness test of the sample at different temperatures shows that the Vickers hardness of the novel nano-structure sample is as high as 5.1GPa at 760 ℃.
As shown in FIG. 2, the indentation creep test at 700℃was performed on the sample, and it was found that the steady-state creep rate was as low as 5.2X10 under a creep stress of 1GPa -8 ～9.5×10 -7 s -1 Far better than other structural properties of alloy with the same components, and creep stress (1 GPa) far higher than the properties of complex component high-temperature alloy under the same conditions, such as: GH4169 (0.6 GPa), waspaloy (0.5 GPa), nimonic90 (0.5 GPa), and the like.
Comparative example 1
The ordinary deformed coarse-grained MP35N alloy (with the grain size of about 70 microns and high-density dislocation and twin crystal inside) has the Vickers hardness of 1.8GPa at 760 ℃. The indentation creep test at 700 ℃ shows that under the condition of 0.3GPa creep stress, the steady-state creep rate is as high as 5 multiplied by 10 -4 s -1 . Compared with the deformation coarse-grain structure with the same component, the Vickers hardness of the novel structural high-temperature alloy prepared by the method is improved by 1.8 times, and the creep resistance is improved by orders of magnitude.
Comparative example 2
The ordinary nanostructured MP35N alloy (grain size about 42nm, no grain boundary relaxation induced) had a significant grain growth temperature of 750deg.C and a Vickers hardness of 1.8GPa at 760 ℃. The indentation creep test at 700 ℃ shows that under the condition of 0.1GPa creep stress, the steady-state creep rate is as high as 4 multiplied by 10 -4 s -1 . Compared with the deformation coarse-grain structure with the same component, the Vickers hardness of the novel structural high-temperature alloy prepared by the method is improved by 1.8 times, and the creep resistance is improved by orders of magnitude.
As can be seen from example 1, comparative example 1 and comparative example 2, the high-temperature alloys are all commercial MP35N alloys, and the high-temperature alloys are single-phase alloys, and the alloying degree is obviously lower than that of the conventional high-temperature alloys at the present stage. After the high-density nano-scale stable grain boundary network structure is introduced, the Vickers hardness at 760 ℃ is 5.1GPa, which is obviously higher than that of the deformed coarse crystal. In particular, at 700 ℃/1036MPa, the indentation steady state creep rate is as low as 10 -7 s -1 。
Example 2
In this embodiment, the superalloy is a commercial Inconel718 alloy, comprising the following components in weight percent: fe 19.1%, cr 17.9%, mo 3%, nb 5.32%, ti 0.96%, al 0.45%, C0.026% and the balance Ni.
The alloy of the embodiment is subjected to high-speed shearing deformation treatment, so that grains are greatly and effectively refined below a critical dimension, and grain boundary relaxation is further induced, and a novel structure of a high-density nano-scale stable grain boundary network is prepared.
The high-temperature alloy bar with the diameter of 15mm is used as a machined part, and the sample is subjected to plastic deformation treatment at room temperature by adopting a surface mechanical grinding treatment technology and adopting high strain rate and strain quantity. The surface mechanical grinding treatment parameters are as follows: the ball head of the processing cutter is made of hard alloy, the radius of the ball head is 4mm, the horizontally arranged high-temperature alloy bar rotates at the rotating speed of 500r/min, the feeding speed of the processing cutter along the horizontal direction is 10mm/min, the rolling reduction of the processing cutter is 20 mu m each time, and the processing passes are 10 times.
After the treatment, the gradient sample has a deep structure with 0-45 mu m of the outermost layer, the grain size is extremely fine and reaches 9nm, the volume fraction of sigma CSL (coincident lattice grain boundary) is up to 37%, the volume fraction and the lattice grain boundary are mutually linked to form a network, the obvious grain growth temperature of the sample is up to 980 ℃, and the gradient sample accords with the structure and the stability characteristics of the high-density nano-scale stable grain boundary network.
The Vickers hardness test of the sample at different temperatures shows that the Vickers hardness of the novel nano-structure sample is as high as 4GPa at 700 ℃.
Comparative example 3
Standard heat treated crude crystalline Inconel718 alloy (1050 ℃/2h solution annealed, 720 ℃/8h, 620 ℃/8h aging annealed) has a vickers hardness of 1.86GPa at 700 ℃. Compared with the precipitation strengthening coarse-grain sample subjected to the same component standard heat treatment, the novel structure Inconel718 superalloy prepared by the method disclosed by the invention has the advantage that the Vickers hardness of 700 ℃ is improved by 1.2 times.
Comparative example 4
Ordinary nanostructured Inconel718 alloy (grain size about 40 nm, no grain boundary relaxation induced) has a significant grain growth temperature of 757 ℃ and a vickers hardness of 2.4GPa at 700 ℃. The Vickers hardness of the novel structural superalloy prepared by the method is improved by 0.6 times at 700 ℃.
Claims (4)
1. A method for improving the performance of MP35N nickel cobalt-based superalloy is characterized in that a high-density nano-scale stable grain boundary network is prepared through plastic deformation, and the key service performance of the structural heat stability, high-temperature strength and high-temperature creep of the superalloy is improved; in a low-temperature environment from room temperature to liquid nitrogen temperature, the applied pressure needs to be more than 1GPa, the plastic deformation amount needs to be more than 20, and the strain rate needs to be more than 10 under the deformation amount of 20-50 3 s -1 The method comprises the steps of carrying out a first treatment on the surface of the Plastic deformation refines grains of the superalloy below a critical dimension and induces grain boundary relaxation, and the superalloy grain size is on the nanometer scale, with a sigma CSL grain boundary volume fraction of relaxation characteristics>30% and are connected with each other to form a network; the grain size of the high-temperature alloy is below 9 nm; the temperature for obviously growing the crystal grains is 950-1100 ℃.
2. The method for improving the performance of an MP35N nickel cobalt based superalloy according to claim 1 wherein the high density nano-scale stable grain boundary network has a material vickers hardness of up to 5.1GPa at 760 ℃.
3. The method for improving the performance of an MP35N nickel cobalt based superalloy according to claim 1 wherein the high density nanosize stable grain boundary network has an indentation steady state creep rate as low as 10 at 700 ℃/1036MPa -7 s -1 。
4. The method for improving the performance of the MP35N nickel cobalt-based superalloy according to claim 1, wherein the MP35N nickel cobalt-based superalloy comprises, by weight, 33-35% of Co, 19-21% of Cr, 9-11% of Mo, 1% of Ti and the balance of Ni.
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| CN105866167A (en) * | 2016-03-24 | 2016-08-17 | 中国华能集团公司 | Method for characterizing and analyzing grain boundary characteristics of nickel-based/ferronickel-based high-temperature alloy on basis of internal friction |
| CN112522784A (en) * | 2020-11-10 | 2021-03-19 | 中国科学院金属研究所 | Metal material with crystal space structure stable under high-temperature condition |
| CN112646964A (en) * | 2020-12-17 | 2021-04-13 | 中国科学院金属研究所 | High-temperature alloy with gradient nano-structure surface layer and preparation method thereof |
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| CN105866167A (en) * | 2016-03-24 | 2016-08-17 | 中国华能集团公司 | Method for characterizing and analyzing grain boundary characteristics of nickel-based/ferronickel-based high-temperature alloy on basis of internal friction |
| CN112522784A (en) * | 2020-11-10 | 2021-03-19 | 中国科学院金属研究所 | Metal material with crystal space structure stable under high-temperature condition |
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