CN117026109A - High-strength creep-resistant low-specific gravity high/medium-entropy heat-resistant steel and preparation method thereof - Google Patents
High-strength creep-resistant low-specific gravity high/medium-entropy heat-resistant steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 105
- 239000010959 steel Substances 0.000 title claims abstract description 105
- 230000005484 gravity Effects 0.000 title claims abstract description 22
- 238000002360 preparation method Methods 0.000 title abstract description 19
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 78
- 238000005096 rolling process Methods 0.000 claims description 51
- 238000010438 heat treatment Methods 0.000 claims description 46
- 238000003723 Smelting Methods 0.000 claims description 42
- 229910052786 argon Inorganic materials 0.000 claims description 39
- 238000000034 method Methods 0.000 claims description 38
- 230000009467 reduction Effects 0.000 claims description 36
- 229910052760 oxygen Inorganic materials 0.000 claims description 29
- 239000002994 raw material Substances 0.000 claims description 25
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 24
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 21
- 239000001301 oxygen Substances 0.000 claims description 21
- 238000005097 cold rolling Methods 0.000 claims description 19
- 238000010791 quenching Methods 0.000 claims description 19
- 230000000171 quenching effect Effects 0.000 claims description 19
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 16
- 230000032683 aging Effects 0.000 claims description 14
- 238000004519 manufacturing process Methods 0.000 claims description 13
- 238000001953 recrystallisation Methods 0.000 claims description 13
- 238000002844 melting Methods 0.000 claims description 11
- 230000008018 melting Effects 0.000 claims description 11
- 238000002156 mixing Methods 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 5
- 239000007789 gas Substances 0.000 claims description 5
- 238000005339 levitation Methods 0.000 claims description 5
- 238000004090 dissolution Methods 0.000 claims description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 25
- 229910000601 superalloy Inorganic materials 0.000 abstract description 17
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 abstract description 7
- 229910052759 nickel Inorganic materials 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 description 36
- 239000000956 alloy Substances 0.000 description 36
- 230000008569 process Effects 0.000 description 34
- 239000000463 material Substances 0.000 description 25
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 19
- 239000000243 solution Substances 0.000 description 19
- 238000005728 strengthening Methods 0.000 description 10
- 238000005266 casting Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 9
- 239000012535 impurity Substances 0.000 description 8
- 239000000126 substance Substances 0.000 description 8
- 229910052717 sulfur Inorganic materials 0.000 description 8
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- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
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- 229910052751 metal Inorganic materials 0.000 description 4
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- 229910052715 tantalum Inorganic materials 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 238000010248 power generation Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 239000003245 coal Substances 0.000 description 2
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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Abstract
The invention relates to the technical field of heat-resistant steel, in particular to high-strength creep-resistant low-specific gravity high/medium entropy heat-resistant steel and a preparation method thereof, wherein the high/medium entropy heat-resistant steel comprises the following element components in percentage by atom: cr5-25at%; ni5-30at%; 1-7at% of Ti; 5-15at% of Al; mo is less than or equal to 4at%; nb is less than or equal to 2at%; ta is less than or equal to 2at%; mn is less than or equal to 2at%; c is less than or equal to 1at%; b is less than or equal to 0.15at%; zr is less than or equal to 0.01at% and Si is less than or equal to 0.3at%; the balance being Fe. The high/medium entropy heat-resistant steel with high strength, creep resistance and low specific gravity and the preparation method thereof are adopted to fill the technical bottleneck of low high temperature strength in the existing commercial austenitic steel, and the high/medium entropy heat-resistant steel has the high temperature strength far exceeding that of the existing austenitic heat-resistant steel, iron-nickel-based superalloy and part of nickel-based superalloy, and the steady creep rate is greatly reduced.
Description
Technical Field
The invention relates to the technical field of heat-resistant steel, in particular to high-strength creep-resistant low-specific gravity high/medium-entropy heat-resistant steel and a preparation method thereof.
Background
Thermal power generation is used as the most main power generation technology in China for a long time, and the steam parameters of a coal-fired power plant are improved, so that the higher the efficiency of the power plant is, the lower the coal consumption of the power plant can be reduced, and the lower the emission is. Along with the great improvement of main steam parameters of a coal-fired power plant generator set, the development of heat-resistant alloy which can be served at the performance requirement of a 700 ℃ -grade unit large-caliber thick-wall pipe and has excellent processability has become a major concern in the thermal power generation industry.
A great deal of engineering practice in the past shows that the main technical difficulty of 700 ℃ ultra supercritical (A-USC) coal-fired power plants is the development of heat-resistant materials for manufacturing high-temperature parts of boilers and turbines, including superheaters, reheaters, main steam pipes, other high Wen Chongxing parts of boilers, thick parts and high-temperature rotors, shells, blades and valves of turbines. Although superalloys have been used for many years to make air engines and gas turbines, the heat resistant alloys used in 700 ℃ a-USC coal-fired power plants are quite different than the superalloys used for air engines and gas turbines. The superalloy for air engines and gas turbines is a relatively small part for extremely high temperatures but short service times, while the heat resistant alloy for 700 ℃ a-USC coal fired power plants is a superalloy for medium and high temperature but relatively large parts and longer service times. Therefore, we refer to the alloy used in 700 ℃ a-USC coal-fired power plants as the reason for the heat resistant alloy.
At present, the types of mature heat-resistant alloys which can be used for the construction of 700 ℃ A-USC coal-fired power plants are fewer in the global range. For the requirements of 700 ℃ grade ultra supercritical unit boiler large-caliber thick-wall pipe on the material using performance, a series of nickel-based superalloy materials have been developed abroad, such as Inconel740H developed by special metal company in the united states, haynes282 developed by hals corporation in the united states, CCA617 (which is an improved component of 617 alloy) developed by german stecke, nimonic263 developed by roller-Royce corporation in the united kingdom, USC41 developed by japanese hitachi corporation, and the like. The materials have excellent high-temperature durable strength and oxidation resistance, but have high price, poor welding performance, high technical requirements on smelting, hot working and the like, and limit the rapid popularization and application of the materials.
In addition, japanese Sumitomo corporation has developed iron-nickel-based superalloys such as HR6W, HR35 (both of which are improved components of the HR3C alloy); sanmicro 25 iron-nickel based alloys were developed by mountain Tevick, sweden; iron-nickel-based superalloys such as GH2984, G110 and the like are also developed by Shenyang metal institute and iron and steel research institute of Chinese academy of sciences respectively. Compared with the nickel-based superalloy, the iron-nickel-based superalloy has the advantages of low heat strength and poor structural stability and corrosion resistance, although the iron-nickel-based superalloy has the advantages of raw material cost. Meanwhile, as deformation processing is still needed to obtain the organization and performance required by service, the preparation and processing technology is complex, the overall manufacturing cost is higher, and the difficulty of further improving the performance is greater.
The methods for improving the high-temperature mechanical properties of the alloy generally include solid solution strengthening, precipitation strengthening, grain boundary strengthening and the like, and the precipitation strengthening is the most important method for improving the high-temperature mechanical properties of the alloy and is the most widely used strengthening method. Stable Ll at high temperatures if precipitated in iron-based superalloys 2 Ni of structure 3 The (Al, ti) phase will significantly improve the high temperature mechanical properties of the iron-based superalloy. However, the precipitation strengthening iron-based superalloy at present often contains refractory and high-density metal elements such as W, re, for example: sanmicro 25 and HR6W, the addition of these refractory elements increases the cost and density of the alloy. Thus, in reducing or not containing expensiveOn the basis of the content of metal elements, the excellent high-temperature mechanical property of the alloy is maintained, and the alloy is a difficulty in designing the iron-based high-temperature alloy.
Disclosure of Invention
The invention aims to provide high/medium entropy heat-resistant steel with high strength, creep resistance and low specific gravity and a preparation method thereof, and the prepared high/medium entropy heat-resistant steel fills the technical bottleneck of low high temperature strength in the existing commercial austenitic steel, has the high temperature strength far exceeding that of the existing austenitic heat-resistant steel, iron-nickel-based superalloy and part of nickel-based superalloy, and greatly reduces the steady creep rate.
In order to achieve the above object, the present invention provides a high/medium entropy heat resistant steel with high strength, creep resistance and low specific gravity, comprising the following elemental components in atomic percent (at%): cr:5-25%; ni:5-30%; ti:1-7%; al:5-15%; mo: less than or equal to 4 percent; nb: less than or equal to 2 percent; ta: less than or equal to 2 percent; mn: less than or equal to 2 percent; c: less than or equal to 1 percent; b: less than or equal to 0.15 percent; zr: less than or equal to 0.01 percent, si: less than or equal to 0.3 percent; the balance being Fe.
A preparation method of high-strength creep-resistant low-specific gravity high/medium entropy heat-resistant steel comprises the following steps:
(1) Mixing the raw materials, smelting and pouring to obtain an ingot;
(2) And carrying out solution treatment on the obtained cast ingot, rolling and recrystallizing, and finally carrying out aging treatment to obtain the high/medium entropy heat-resistant steel.
Preferably, the smelting and casting in the step (1) are performed in a vacuum argon arc furnace or a vacuum magnetic levitation furnace.
Preferably, when using a vacuum argon arc furnace, the argon arc furnace is vacuumized to 1.0X10 -2 Pa or lower, and then argon is filled to make the gas pressure in the furnace lower than 6.0X10 3 Pa, above 3.0X10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
Preferably, when a vacuum magnetic levitation furnace is used, the furnace is evacuated to 3.0X10 -3 Pa or below, then argon is filled to make the air pressure in the furnace lower than 6.0X10 3 Pa, above 3.0X10 3 After Pa, the oxygen content and the nitrogen content in the furnace are both lower than 0 within 150 min.002% of the melting was started.
Preferably, the solution treatment in step (2) is: heating the cast ingot to 1000-1200 ℃ at the speed of 5-30 ℃/min, preserving heat for 1-10h, and then quenching with water or cooling in air.
Preferably, the rolling in step (2) is cold rolling or hot rolling and cold rolling or hot rolling;
wherein the cold rolling is as follows: the rolling reduction of each pass is not more than 0.2-0.5mm, and the total rolling reduction is 50% -90%;
the hot rolling and cold rolling are as follows: heating at a speed of 30-60 ℃/min to a rolling temperature, wherein the rolling reduction of each pass is not more than 0.5-1.5mm, the temperature is ensured to be within a rolling temperature range in the hot rolling process, the rolling temperature is 20-150 ℃ above the dissolution temperature of a precipitated phase, if the temperature is reduced, the temperature is kept for 5-15min in the rolling temperature range after the furnace is returned, the total rolling reduction is replaced by cold rolling after the total rolling reduction is 50-70%, the rolling reduction of each pass is not more than 0.2-0.5mm, and the total rolling reduction is 70-90%;
the hot rolling is as follows: heating at a speed of 30-60 ℃/min to a rolling temperature, wherein the rolling process does not return to the furnace, the rolling reduction of each pass is not more than 0.5-1.5mm, the rolling temperature is ensured to be 20-150 ℃ above the dissolution temperature of a precipitated phase in the rolling temperature range in the hot rolling process, if the temperature is reduced, the furnace returns to keep the temperature in the rolling temperature range for 5-15min, the total rolling reduction is 50-90%, and the rolling reduction of each pass is not more than 0.5-1.5mm.
Preferably, the recrystallization treatment in step (2) is: and heating the rolled ingot to 1150-1200 ℃ at a speed of 30-60 ℃/min, and preserving the temperature for 1-30min to finish recrystallization.
Preferably, the aging treatment in step (2) is: heating the recrystallized cast ingot to 500-650 ℃ at a speed of 30-60 ℃/min, preserving heat for 0.5-10h, and then performing water quenching or air cooling to finish aging treatment.
Preferably, L1 in the high/medium entropy heat resistant steel obtained in the step (2) 2 The volume fraction of the phase is more than or equal to 10 percent, and the yield strength at room temperature is more than or equal to 800MPa; at 800 ℃, the tensile strength is more than or equal to 500Mpa.
The mechanism of the invention:
(1) The addition of Cr element can improve the high-temperature strength of heat-resistant steel through solid solution strengthening on one hand, and can ensure that the heat-resistant steel has good corrosion resistance at high temperature and in complex environment on the other hand, but the high content of Cr can form alpha' or sigma phase to seriously influence the plasticity of the alloy, so that the atomic percentage of Cr in the invention is controlled to be 5-25at%.
(2) The addition of Ni element can widen the phase region formed by nano precipitated phase, inhibit the formation of other harmful intermetallic compounds and avoid brittleness caused by the formation of other harmful intermetallic compounds, but the high content of Ni can increase the cost of the alloy, so that the atomic percent of Ni is controlled to be 5-29at percent in the invention.
(3) Al element is L1 2 Phase-forming element promoting L1 2 Nano precipitated phase is precipitated, and the nano precipitated phase and the matrix keep a coherent relation, L1 in the alloy 2 The phase volume fraction is determined by the addition amount of Al element, so that the atomic percentage of Al in the invention is controlled to be 5-15at percent.
(4) The element Ti also forms L1 2 Important elements of the phase, substituting part of Al into L1 2 The phase does not destroy the microstructure of nano precipitated phase and increases L1 2 The phase inversion domain boundary energy (APB) improves the strength of the heat-resistant steel; meanwhile, the proper addition of Ti element can refine crystal grains and uniform structure, improve the hot corrosion resistance of the alloy, has lower specific gravity and cost, and can replace expensive Co, V and W to reduce the production cost and density of the alloy, so that the atomic percentage of Ti in the invention is controlled to be 1-7a percent.
(5) Because Mn has the volatilization problem in the smelting process, the preparation of the alloy is inconvenient, the waste is large, and the high content of Mn can reduce L1 2 Volume fraction of nano precipitated phase; however, segregation may occur due to the presence of Cu, and non-uniformity may be caused to the material structure. Thus, the alloy of the present invention removes Cu element and reduces Mn element content.
(6) Mo and Nb are solid solution strengthening elements commonly used in high-temperature alloys, and meanwhile Mo promotes Cr to be segregated in a matrix phase and Ti to be segregated in L1 2 Phase, the degree of mismatch can be adjusted. However, excessive amounts of Mo and Nb reduce the corrosion resistance of the alloy, making the alloy more susceptible to the formation of TCP phases at high temperatures, due toIn the invention, the atomic percentage of Mo is controlled below 4%, and the atomic percentage of Nb is controlled below 2%.
(7) Ta is a solid solution strengthening element commonly used in high-temperature alloys, and can replace part of Ti and Al to form L1 2 Phase, can increase L1 2 Thermal stability of the phases. However, excessive Ta increases the cost of the alloy and increases its density, so that the atomic percent of Ta in the present invention is controlled to 2% or less.
(8) The strengthening principle of the invention is as follows: in the heat-resistant steel taking Fe-Cr-Ni as a matrix, the contents of three elements of Ti, al and Ta are adjusted and added by controlling the contents of Cr and Ni, thereby realizing a large amount of L1 2 Nano precipitated phase to strengthen the matrix. Meanwhile, a small amount of Mo, nb and Ta elements are added, carbide or other intermetallic compound particles are separated out, and the high-temperature strength of the alloy is further improved. When the content of Cr element is increased, the content of Ni element is increased, on one hand, the base body is ensured to be in an austenite structure, on the other hand, enough Ni atoms are ensured to form nano precipitated phases, and meanwhile, the content of Ti, al and Ta is reduced properly, so that brittle intermetallic compounds are prevented from being formed, and vice versa.
The invention has the beneficial effects that:
1) The high/medium entropy heat-resistant steel provided by the invention is austenitic heat-resistant steel, has a simple component system, reduces noble metals and refractory heavy elements, reduces addition of alloy elements to the greatest extent, and realizes maximization of volume fraction of precipitated phases by adjusting atomic ratio of each component, so that the prepared high/medium entropy heat-resistant steel has the advantages of high strength, creep resistance, low specific gravity and low cost.
2) In the invention, cr is added to improve the strength and corrosion resistance of the heat-resistant steel; the addition of Ni can be used to widen the phase region formed by the nano precipitated phase and inhibit the generation of harmful intermetallic compounds; the addition of Al is added to endow the material with oxidation resistance and corrosion resistance, and is helpful for the formation of nano precipitated phases; adding Ti element to refine crystal grains and uniform structures, forming nano precipitated phases with Ni and Al to improve the strength of the heat-resistant steel, and simultaneously replacing expensive Co, V and W with Ti and trace Ta to reduce the production cost without damaging the microstructure of the nano precipitated phases; adding Mo and Nb elementsThe element increases the strength of the heat-resistant steel and promotes the segregation of Ti to L1 2 And (3) phase (C).
3) The invention also provides a preparation process of the high/medium-entropy austenitic heat-resistant steel with high heat strength and low cost, perfects a heat treatment process, reduces extra production cost caused by a complex treatment process, and has wide application prospect. In the scheme of the invention, a rolling process of cold rolling after hot rolling or hot rolling only is adopted, so that the problem of difficult deformation of a large cast ingot is solved, microcracks in the cast ingot can be eliminated in the initial stage of hot rolling, preparation is made for subsequent cold rolling or complete recrystallization, and the danger is reduced. The heat-resistant steel prepared by the preparation method has the advantages of good strength, easy processing and low processing cost, and the mechanical property of the heat-resistant steel is superior to that of most commercial heat-resistant steels, so that the heat-resistant steel is suitable for the service field of most heat-resistant steels.
The technical scheme of the invention is further described in detail through the drawings and the embodiments.
Drawings
FIG. 1 is a graph of the yield strength (ReL) of the high/medium entropy austenitic heat resistant steel of the present invention versus the prior art materials at different temperature temperatures;
FIG. 2 is a graph of the tensile strength (Rm) of the high/medium entropy austenitic heat resistant steel of the present invention versus the materials of the prior art, at different temperatures;
FIG. 3 is a graph comparing the cost of materials in the high/medium entropy austenitic heat resistant steel of the present invention with those in the prior art;
FIG. 4 is a graph comparing steady state creep rates of the high/medium entropy austenitic heat resistant steel of the present invention with materials of the prior art;
FIG. 5 is a graph comparing the specific strength of the high/medium entropy austenitic heat resistant steel of the present invention to materials in the prior art;
FIG. 6 is a grain microstructure of the high/medium entropy heat resistant steel of example 2 subjected to standard heat treatment;
FIG. 7 is a grain microstructure of the high/medium entropy heat resistant steel of example 3 subjected to standard heat treatment;
FIG. 8 is a morphology and element distribution diagram of a transmission electron microscope of a nano precipitated phase of the high/medium entropy heat resistant steel of example 5 subjected to standard heat treatment.
Detailed Description
The invention will be further described with reference to examples. Unless defined otherwise, technical or scientific terms used herein should be given the ordinary meaning as understood by one of ordinary skill in the art to which this invention belongs. The above-mentioned features of the invention or the features mentioned in the specific examples can be combined in any desired manner, and these specific examples are only intended to illustrate the invention and are not intended to limit the scope of the invention.
Example 1
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 46.245 Cr 16 Ni 26 Ti 6 Al 5 C 0.1 (at%) and a small amount of Mn:0.5; b:0.05; si:0.1; zr:0.005 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 10mm 3 Is a sheet ingot. Wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 4.0 multiplied by 10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 3.5 multiplied by 10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1200 ℃ at a speed of 30 ℃/min, preserving heat for 120min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 88%. And heating the rolled ingot to 1150 ℃ at a speed of 30 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 30 ℃/min, preserving heat for 1h, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 2
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 46.24 Cr 16 Ni 26 Ti 6 Al 5 Mo 0.5 C 0.1 (at%) and a small amount of B:0.1; si:0.05; zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing the raw materials (the purity of the raw materials is more than or equal to 99.9 percent), smelting the mixture by a vacuum argon arc furnace for at least four times, and casting the mixture to obtain the alloy with the thickness of 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot. Wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 5.0x10 -3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1100 ℃ at a speed of 15 ℃/min, preserving heat for 150min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And (3) heating the rolled ingot to 1160 ℃ at a speed of 40 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 550 ℃ at a speed of 40 ℃/min, preserving heat for 2 hours, and cooling in air to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 3
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 46.84 Cr 16 Ni 26 Ti 6 Al 5 (at%) and a small amount of B:0.1; si:0.05; zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (C, N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot; wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 4.0 multiplied by 10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 4.0 multiplied by 10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1050 ℃ at a speed of 20 ℃/min, preserving heat for 180min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And (3) heating the rolled ingot to 1150 ℃ at a speed of 50 ℃/min, and preserving the temperature for 1.5min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 50 ℃/min, preserving heat for 1h, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 4
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 34.29 Cr 24 Ni 30 Ti 6 Al 5 (at%) and a small amount of Mn:0.5, B:0.1, si:0.1, zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (C, N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot; wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 5.0x10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1150 ℃ at a speed of 15 ℃/min, preserving heat for 120min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And heating the rolled ingot to 1150 ℃ at a speed of 40 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 40 ℃/min, preserving heat for 1h, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 5
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 41.84 Cr 16 Ni 28 Ti 7 Al 7 (at%) and a small amount of B:0.1, si:0.05, zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (C, N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot; wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 5.0x10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, when the oxygen content and the nitrogen content are both lower than 0.002% in 150min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1150 ℃ at a speed of 15 ℃/min, preserving heat for 120min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And heating the rolled ingot to 1150 ℃ at a speed of 40 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 40 ℃/min, preserving heat for 1h, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 6
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components:Fe 38.29 Cr 20 Ni 30 Ti 6 Al 5 (at%) and a small amount of Mn:0.5, B:0.1, si:0.1, zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (C, N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot; wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 5.0x10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1150 ℃ at a speed of 15 ℃/min, preserving heat for 120min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And heating the rolled ingot to 1150 ℃ at a speed of 40 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 40 ℃/min, preserving heat for 1h, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 7
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 46.29 Cr 16 Ni 26 Ti 6 Al 5 (at%) and a small amount of Mn:0.5, B:0.1, si:0.1, zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (C, N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
The preparation method of the high-heat-strength low-cost austenitic heat-resistant steel comprises the following steps:
(1) Weighing the raw materials according to the proportion, mixing the raw materials (the purity of the raw materials is more than or equal to 99.9 percent), and smelting at least four raw materials by a vacuum magnetic levitation furnaceSecondary casting to obtain 120×120×30mm 3 Is a block ingot; wherein, in the smelting process of the magnetic suspension smelting furnace, the air pressure in the smelting furnace is pumped to 3.0 multiplied by 10 -3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, smelting is started when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 150 min.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1150 ℃ at a speed of 5 ℃/min, preserving heat for 480min, and then quenching with water. And (3) carrying out hot rolling deformation on the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 1mm, and the total reduction is 50%. And heating the rolled ingot to 1150 ℃ at a speed of 30 ℃/min, and preserving the temperature for 10min to finish recrystallization. And (3) heating the recrystallized cast ingot to 600 ℃ at a speed of 30 ℃/min, preserving heat for 4 hours, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Example 8
A high-heat-strength low-cost high/medium-entropy austenitic heat-resistant steel comprises the following chemical components: fe (Fe) 41.78 Cr 20 Ni 30 Ti 2 Al 5 Nb 0.5 Ta 0.5 (at%) and a small amount of C:0.01, B:0.1, si:0.1, zr:0.01 (at%) in which the introduction of unavoidable and extremely small amounts of impurity elements (N, O, S, etc.) during the smelting process and the heat treatment process has negligible effect on the material properties.
(1) Weighing the raw materials according to the proportion, mixing (the purity of the raw materials is more than or equal to 99.9 percent), smelting at least four times by a vacuum argon arc furnace, and casting to obtain 60 multiplied by 20 multiplied by 5mm 3 Is a sheet ingot; wherein, in the smelting process of the argon arc furnace, the argon arc furnace is arranged at a temperature of 5.0x10 - 3 Argon is filled below Pa to ensure that the air pressure in the furnace reaches 5.0x10 3 After Pa, when the oxygen content and the nitrogen content are both lower than 0.002% in 150min, melting pure Ti starts smelting after oxygen inhalation.
(2) And (3) placing the cast ingot into a furnace for solution treatment, heating to 1150 ℃ at a speed of 15 ℃/min, preserving heat for 120min, and then quenching with water. And (3) adopting a cold rolling deformation process for the ingot after solution treatment, wherein the rolling process is as follows: the reduction per pass is not more than 0.2mm, and the total reduction is 70%. And heating the rolled ingot to 1150 ℃ at a speed of 40 ℃/min, and preserving the temperature for 1min to finish recrystallization. And (3) heating the recrystallized cast ingot to 550 ℃ at a speed of 40 ℃/min, preserving heat for 2 hours, and then performing water quenching to finish ageing treatment to obtain the high/medium entropy heat-resistant steel.
Performance testing
The high/medium entropy heat resistant steels prepared in examples 1 to 8 were sampled and tested for yield strength R at room temperature, 600 ℃,700 ℃ and 800 DEG C eL Tensile strength R m The elongation at break E and the test results are shown in Table 1. Wherein each sample in the table was tested three times, using a random sampling pattern.
Table 1 performance data for high/medium entropy heat resistant steels of examples 1-8
As can be seen from Table 1 above, the high/medium entropy austenitic heat-resistant steels prepared in examples 1 to 8 of the present invention maintained very high levels of both yield strength and tensile strength in the high temperature range, as compared to the existing heat-resistant steels.
FIG. 1 is a graph of the yield strength (ReL) of the high/medium entropy austenitic heat resistant steel of the present invention versus the prior art materials at different temperature temperatures; fig. 2 is a graph showing the comparison of the tensile strength (Rm) of the high/medium entropy austenitic heat-resistant steel of the present invention with that of the prior art at different temperatures, and as shown in fig. 1-2, the yield strength and tensile strength of the high/medium entropy austenitic heat-resistant steel of the present invention are superior to those of most commercial heat-resistant steels in the 800 ℃ range, showing great application potential.
The high/medium entropy heat resistant steels prepared in examples 1 to 8 were arbitrarily sampled and measured for density (g/cm) by Archimedes drainage 3 ) The results are shown in Table 2. Wherein each sample in the table was tested three times, using a random sampling pattern.
Table 2 alloy density data for high/medium entropy heat resistant steels of examples 1-8
It can be seen from Table 2 that the trace addition of Mo and C elements has no significant effect on the change of alloy density, and at the same time, the densities of the high/medium entropy austenitic heat-resistant steels prepared in examples 1 to 8 are all kept at a low level.
Cost estimates were made for the high/medium entropy austenitic heat resistant steel compositions of examples 1-8, to rule out the difference in alloy raw material cost from elemental raw material cost, all alloys were estimated using elemental raw material prices derived from Shanghai futures exchange (www.shfe.com.cn) and Chinese wire mesh (www.metalchina.com).
Fig. 3 is a graph showing the comparison of the costs of the high/medium entropy austenitic heat-resistant steel obtained in some embodiments of the present invention with the costs of the conventional heat-resistant steel, some high/medium entropy alloys and several ultra supercritical technology candidate materials, and as can be seen from fig. 3, the cost of the high/medium entropy austenitic heat-resistant steel of the present invention is reduced due to the removal of most of the expensive and high specific gravity alloy elements.
Considering that the creep performance test time is too long, the system of the embodiment 3 is simple and the performance is better, the high/medium entropy austenitic heat-resistant steel prepared in the embodiment 3 is selected, the high/medium entropy austenitic heat-resistant steel is arbitrarily sampled from the high/medium entropy austenitic heat-resistant steel, and the tensile creep test is carried out under different stresses at 750 ℃.
FIG. 3 is a graph showing the steady creep rate of the high/medium entropy austenitic heat-resistant steel obtained in example 3 of the present invention compared with the steady creep rates of the conventional heat-resistant steel and the several ultra-supercritical candidate materials, and as can be seen from FIG. 3, the creep resistance of the high/medium entropy austenitic heat-resistant steel of the present invention is superior to that of the conventional heat-resistant steel and the several ultra-supercritical candidate materials, and has a great advantage in the comparison of the ultra-supercritical candidate materials due to the lower cost.
Fig. 4 is a graph showing the comparison of the specific strength (ratio of tensile strength to density) of the high/medium entropy heat resistant steel obtained in some embodiments of the present invention with that of the conventional heat resistant steel and several ultra supercritical technology candidate materials, and as can be seen from fig. 4, the specific strength advantage of the high/medium entropy austenitic heat resistant steel of the present invention is obvious, and will not be limited by weight factors when applied.
In conclusion, the high/medium entropy heat-resistant steel has the comprehensive properties of high heat strength, creep resistance, low cost and lower specific gravity, and has great high-temperature service potential.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention and not for limiting it, and although the present invention has been described in detail with reference to the preferred embodiments, it will be understood by those skilled in the art that: the technical scheme of the invention can be modified or replaced by the same, and the modified technical scheme cannot deviate from the spirit and scope of the technical scheme of the invention.
Claims (10)
1. A high/medium entropy heat resistant steel with high strength, creep resistance and low specific gravity, which is characterized by comprising the following element components in atomic percentage: cr:5-25at%; ni:5-30at%; ti:1-7at%; al:5-15at%; mo: less than or equal to 4at%; nb: less than or equal to 2at%; ta: less than or equal to 2at%; mn: less than or equal to 2at%; c: less than or equal to 1at%; b: less than or equal to 0.15at%; zr: less than or equal to 0.01at%, si: less than or equal to 0.3at%; the balance being Fe.
2. A method for preparing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity as claimed in claim 1, comprising the steps of:
(1) Mixing the raw materials, smelting and pouring to obtain an ingot;
(2) And carrying out solution treatment on the obtained cast ingot, rolling and recrystallizing, and finally carrying out aging treatment to obtain the high/medium entropy heat-resistant steel.
3. The method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 2, wherein: smelting and pouring in the step (1) are carried out in a vacuum argon arc furnace or a vacuum magnetic levitation furnace.
4. A method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 3, wherein: when the vacuum argon arc furnace is used, the argon arc furnace is vacuumized to 1.0 multiplied by 10 -2 Pa or lower, and then argon is filled to make the gas pressure in the furnace lower than 6.0X10 3 Pa, above 3.0X10 3 After Pa, when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 120min, melting pure Ti starts smelting after oxygen inhalation.
5. A method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 3, wherein: when using the vacuum magnetic levitation furnace, the furnace is vacuumized to 3.0X10 -3 Pa or below, then argon is filled to make the air pressure in the furnace lower than 6.0X10 3 Pa, above 3.0X10 3 After Pa, melting is started when the oxygen content and the nitrogen content in the furnace are both lower than 0.002% in 150 min.
6. The method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 2, wherein the solution treatment in step (2) is: heating the cast ingot to 1000-1200 ℃ at the speed of 5-30 ℃/min, preserving heat for 1-10h, and then quenching with water or cooling in air.
7. The method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 2, wherein the rolling in the step (2) is cold rolling or hot rolling and cold rolling or hot rolling;
wherein the cold rolling is as follows: the rolling reduction of each pass is not more than 0.2-0.5mm, and the total rolling reduction is 50% -90%;
the hot rolling and cold rolling are as follows: heating at a speed of 30-60 ℃/min to a rolling temperature, wherein the rolling reduction of each pass is not more than 0.5-1.5mm, the temperature is ensured to be within a rolling temperature range in the hot rolling process, the rolling temperature is 20-150 ℃ above the dissolution temperature of a precipitated phase, if the temperature is reduced, the temperature is kept for 5-15min in the rolling temperature range after the furnace is returned, the total rolling reduction is replaced by cold rolling after the total rolling reduction is 50-70%, the rolling reduction of each pass is not more than 0.2-0.5mm, and the total rolling reduction is 70-90%;
the hot rolling is as follows: heating at a speed of 30-60 ℃/min to a rolling temperature, wherein the rolling process does not return to the furnace, the rolling reduction of each pass is not more than 0.5-1.5mm, the rolling temperature is ensured to be 20-150 ℃ above the dissolution temperature of a precipitated phase in the rolling temperature range in the hot rolling process, if the temperature is reduced, the furnace returns to keep the temperature in the rolling temperature range for 5-15min, the total rolling reduction is 50-90%, and the rolling reduction of each pass is not more than 0.5-1.5mm.
8. The method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 2, wherein the recrystallization treatment in step (2) is: and heating the rolled ingot to 1150-1200 ℃ at a speed of 30-60 ℃/min, and preserving the temperature for 1-30min to finish recrystallization.
9. The method for producing a high/medium entropy heat resistant steel having high strength, creep resistance and low specific gravity according to claim 2, wherein the aging treatment in step (2) is: heating the recrystallized cast ingot to 500-650 ℃ at a speed of 30-60 ℃/min, preserving heat for 0.5-10h, and then performing water quenching or air cooling to finish aging treatment.
10. The method for producing a high/medium entropy heat resistant steel having a high strength, creep resistance and a low specific gravity according to claim 2, wherein L1 in the high/medium entropy heat resistant steel obtained in the step (2) 2 The volume fraction of the phase is more than or equal to 10 percent, and the yield strength at room temperature is more than or equal to 800MPa; at 800 ℃, the tensile strength is more than or equal to 500Mpa.
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