CN114086077A - Cast iron-based austenite creep-resistant steel and preparation method and application thereof - Google Patents

Cast iron-based austenite creep-resistant steel and preparation method and application thereof Download PDF

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CN114086077A
CN114086077A CN202210024961.0A CN202210024961A CN114086077A CN 114086077 A CN114086077 A CN 114086077A CN 202210024961 A CN202210024961 A CN 202210024961A CN 114086077 A CN114086077 A CN 114086077A
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creep
resistant steel
austenitic
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austenite
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CN114086077B (en
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王寅杰
宫高全
陈小华
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Kehua Holdings Co ltd
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Priority to PCT/CN2022/131885 priority patent/WO2023134292A1/en
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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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D25/00—Component parts, details, or accessories, not provided for in, or of interest apart from, other groups
    • F01D25/005—Selecting particular materials
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D25/00—Component parts, details, or accessories, not provided for in, or of interest apart from, other groups
    • F01D25/24—Casings; Casing parts, e.g. diaphragms, casing fastenings
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/08—Other arrangements or adaptations of exhaust conduits
    • F01N13/10—Other arrangements or adaptations of exhaust conduits of exhaust manifolds
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/16—Selection of particular materials
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
    • F04D—NON-POSITIVE-DISPLACEMENT PUMPS
    • F04D29/00—Details, component parts, or accessories
    • F04D29/02—Selection of particular materials
    • F04D29/023—Selection of particular materials especially adapted for elastic fluid pumps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
    • F04D—NON-POSITIVE-DISPLACEMENT PUMPS
    • F04D29/00—Details, component parts, or accessories
    • F04D29/40—Casings; Connections of working fluid
    • F04D29/403—Casings; Connections of working fluid especially adapted for elastic fluid pumps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2220/00—Application
    • F05D2220/40—Application in turbochargers
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2240/00—Components
    • F05D2240/10—Stators
    • F05D2240/14—Casings or housings protecting or supporting assemblies within
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2300/00—Materials; Properties thereof
    • F05D2300/10—Metals, alloys or intermetallic compounds
    • F05D2300/17—Alloys
    • F05D2300/171—Steel alloys

Abstract

The invention belongs to the technical field of austenite creep-resistant steel, and particularly relates to cast iron-based austenite creep-resistant steel, and a preparation method and application thereof. The austenitic creep-resistant steel comprises the following components in percentage by mass: c: 0.2 to 0.5; si: 0.5-2.0, Mn < 0.5; cr: 20-28; ni: 8-13; p is less than or equal to 0.04; s is less than or equal to 0.3; w: 0.5 to 2; n: 0.2 to 0.4; the balance being iron and other unavoidable impurity elements. The austenitic creep-resistant steel prepared by the method inhibits a high-temperature ferrite phase, and eliminates the defect of precipitation type nitrogen pores; the addition range of nitrogen and carbon elements is optimized, so that the processing cost of the casting is lower than that of common chromium-nickel austenitic heat-resistant steel; excellent mechanical performance at high temperature and long creep rupture time.

Description

Cast iron-based austenite creep-resistant steel and preparation method and application thereof
Technical Field
The invention belongs to the technical field of austenite creep-resistant steel, and particularly relates to cast iron-based austenite creep-resistant steel, and a preparation method and application thereof.
Background
An austenitic steel is a steel having an austenitic structure after normalizing. The alloying elements (Ni, Mn, N, Cr, etc.) added to the steel can make the normalized metal have a stable austenite structure.
The iron-based austenitic creep-resistant steel is heat-resistant steel which has an austenitic structure at normal temperature and has special requirements on high-temperature creep property of materials. The steel contains about 20-25% of Cr, about 9-40% of Ni, about 0.3-0.5% of C, about 0.5-2% of Nb and certain amounts of Mo, W and B elements based on Fe. Among three kinds of austenitic matrix heat-resistant steel (high-temperature alloy) of Fe, Co and Ni, the iron-based heat-resistant raw material cost is the lowest, but the austenitic matrix has the worst thermal stability, and the TCP phase is precipitated at the fastest speed when the austenitic matrix is used at a high temperature for a long time, so the creep resistance is the worst.
Disclosure of Invention
The invention provides cast iron-based austenite creep-resistant steel, and a preparation method and application thereof.
In order to solve the technical problems, the invention provides austenite creep-resistant steel which comprises the following components in percentage by mass: c: 0.2 to 0.5; si: 0.5-2.0, Mn < 0.5; cr: 20-28; ni: 8-13; p is less than or equal to 0.04; s is less than or equal to 0.3; w: 0.5 to 2; n: 0.2 to 0.4; the balance being iron and other unavoidable impurity elements.
In another aspect, the invention also provides a preparation method of the austenite creep-resistant steel, which comprises the steps of adding the raw materials into a medium-frequency furnace, smelting, and casting into a mold to obtain the austenite creep-resistant steel.
In a third aspect, the invention also provides the use of an austenitic creep resistant steel as described above in an exhaust manifold or turbocharger housing of an automotive engine.
The austenitic creep-resistant steel prepared by the method inhibits a high-temperature ferrite phase and eliminates the defect of precipitation type nitrogen pores; the addition range of nitrogen and carbon elements is optimized, so that the processing cost of the casting is lower than that of common chromium-nickel austenitic heat-resistant steel; excellent mechanical performance at high temperature and long creep rupture time. Under the condition that the cost of raw materials is reduced by more than 60 percent, the high-temperature creep rupture time, the thermal conductivity and the linear expansion coefficient reach the level of 1.4849 heat-resistant steel.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and drawings.
In order to make the aforementioned and other objects, features and advantages of the present invention comprehensible, preferred embodiments accompanied with figures are described in detail below.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and other drawings can be obtained by those skilled in the art without creative efforts.
FIG. 1 is a sample plot of an austenitic creep resistant steel made in accordance with example 1 of the present invention;
FIG. 2 is a sample plot of an austenitic creep resistant steel made according to comparative example 1 of the present invention.
Detailed Description
To make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions of the present invention will be clearly and completely described below with reference to the accompanying drawings, and it is apparent that the described embodiments are some, but not all embodiments of the present invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
In the iron-based austenitic steel, nickel is a main austenitizing element, and the main function of the nickel is to form and stabilize austenite, so that the austenitic steel obtains good high-temperature mechanical properties, oxidation resistance and corrosion resistance, and not only is phase change prevented from occurring when the austenitic steel is cooled to room temperature, but also TCP phase is prevented from being separated out when the austenitic steel is used for a long time at high temperature. Nickel is a precious metal element and belongs to strategic resources, and a large amount of nickel element is consumed in the production of the austenitic creep-resistant steel, so that the product price is high. The development of the low-nickel austenitic creep-resistant steel which replaces nickel with other cheap alloy elements completely or partially is beneficial to reducing the cost and improving the market competitiveness of heat-resistant steel products.
Nitrogen and carbon are strong austenite forming elements, and when the nitrogen and carbon are interstitial solid solution elements, the effect of stabilizing austenite is about 30 times that of nickel, so that the use amount of nickel in the austenite creep-resistant steel can be greatly reduced, and the raw material cost can be reduced. However, in actual production, the addition of nitrogen often causes the defects of nitrogen pores on castings, and seriously affects the machining and cutting performance of materials, and carbon can also form carbide when being excessive, so that the cost of machining tools is increased, and the comprehensive production cost is increased and cannot be paid back.
In order to solve the technical problems, the invention provides austenite creep-resistant steel which comprises the following components in percentage by mass: c: 0.2 to 0.5; si: 0.5-2.0, Mn < 0.5; cr: 20-28; ni: 8-13; p is less than or equal to 0.04; s is less than or equal to 0.3; w: 0.5 to 2; n: 0.2 to 0.4; the balance being iron and other unavoidable impurity elements.
Specifically, the austenitic creep-resistant steel eliminates the defect of precipitation type nitrogen pores by inhibiting a high-temperature ferrite phase; the addition range of nitrogen and carbon elements is optimized, and a proper amount of free-cutting elements are added, so that the processing cost of the casting is lower than that of common chromium-nickel austenite creep-resistant steel; the creep rupture time at 1000 ℃ and 35MPa is better than that of 1.4849 heat-resistant steel, and the cost of raw materials is greatly reduced.
In the austenitic creep-resistant steel, C and Cr and W elements form carbides with high thermal stability at grain boundaries, so that the grain boundaries are subjected to precipitation strengthening, the grain boundary creep speed is reduced, and the service life of parts is prolonged. Meanwhile, in the invention, C and N replace noble metal Ni together, which plays the roles of stabilizing austenite matrix and reducing raw material cost. According to the invention, when the content of C is less than 0.2%, the base body contains about 3% (volume percentage) of TCP phase in an as-cast state, and more TCP phases (>5%) are precipitated after aging treatment at 900-1000 ℃, so that the creep rupture time of the material at 1000 ℃ is shortened by about 80%. When the content of C exceeds 0.4 percent, carbide appears in the interior of crystal grains, the processing performance is seriously deteriorated, and the cost of processing the cutter is increased by 100 to 900 percent. Based on the above, the mass percent of C in the austenitic creep-resistant steel is controlled to be 0.2-0.5%.
In the austenitic creep-resistant steel of the present invention, Si functions as an auxiliary deoxidation during melting to improve the fluidity of molten steel, reduce the defects of cast slag holes, and slightly improve the high-temperature oxidation resistance and corrosion resistance. When Si is more than 2.0% or less than 0.5%, the fluidity of molten steel is greatly reduced, and the defects of casting slag holes are increased rapidly. Si is a main ferrite forming element, and the ferrite phase appears in an as-cast state due to excessively high content of Si, so that the high-temperature stability of an austenite matrix and carbide is reduced, and the service life of parts is shortened. In the austenitic creep-resistant steel, the mass percent of Si is controlled to be 0.5-2.0%.
In the austenitic creep resistant steel of the present invention, Mn needs to be controlled to a content of < 0.5%. Generally, Mn has an effect of reducing the cost of raw materials instead of Ni, and can also react with S to form spherical MnS, thereby reducing the hot brittleness of grain boundary FeS. However, in the present invention, when the mass percentage is more than 0.5%, the precipitable pore defects are significantly increased, and the N absorption rate during melting is significantly reduced. Because the N element is added into the molten steel through the N-containing alloy, other alloy elements can be brought in, the addition amount of the N-containing alloy is increased due to the reduction of the N absorption rate, and the brought other alloy elements are also increased, so that the adjustment of the components of the molten steel is more difficult. During mass production, because the casting return material also contains N, when Mn is too high, the N in the return material is seriously lost in the molten steel smelting process, and part of N also needs to be supplemented by the alloy containing N, so that the use proportion of the casting return material is reduced, and the casting return material is accumulated when the actual process yield is low, and cannot be recycled. According to Pauling's theory, the electron vacancy number of Mn is 3.66, which is the highest among austenite forming elements, and the formation of TCP phase is significantly promoted in the iron-based austenitic creep-resistant steel with low nickel equivalent, reducing the stability of the austenite matrix, so that the creep speed is increased. So a low manganese source must be used to reduce the Mn content.
In the austenitic creep-resistant steel, Cr mainly has the effects of providing the oxidation resistance and the corrosion resistance at 900-1050 ℃ and improving the solubility of N in molten steel, so that the N absorption rate is improved when an N-containing alloy is added, the boiling phenomenon of the molten steel at high temperature is reduced, and the defect of casting pores is reduced. However, Cr is a ferrite-forming element, and if the content of Cr is too high, a ferrite phase appears in an as-cast state, and the tensile strength of ferrite at a temperature of over 900 ℃ is less than one tenth of that of austenite, so that the high-temperature mechanical properties of the part are seriously reduced. Cr is also an element forming a TCP phase, the electron vacancy number reaches 4.66, and when the mass percent of Cr is less than 20%, the solubility of N in molten steel is less than 0.3%, so that the sigma phase appears in an as-cast structure, and the defect of casting pores is increased. When the mass percentage of Cr is more than 28%, a ferrite phase may also appear in an as-cast state when the content of the remaining alloying elements satisfies the requirement. Based on this, in the technical scheme of the invention, the mass percent of Cr is controlled to be 20-28%.
In the austenitic creep-resistant steel of the present invention, Ni is a main austenite forming element, the number of electron vacancies is 0.66, and is the strongest element inhibiting the TCP phase among the main alloying elements of the iron-based heat-resistant steel. Ni is the alloy element that accounts for the highest proportion of raw material costs. Ni also decreases the solubility of N, and at higher levels of both elements, increases the cast porosity defects. When the content of other alloy elements meets the requirement, when the mass percent of Ni is less than 8%, the material matrix contains about 1% (volume percent) of TCP phase in an as-cast state, more TCP phases (3%) are precipitated after aging treatment at 900-1000 ℃, and the creep rupture time of the material at 1000 ℃ can be shortened by about 60% by the proportion of the TCP phases. However, when the Ni content exceeds 13%, the Ni content is continuously increased, and the creep rupture time starts to decrease. Based on this, in the technical scheme of the invention, the mass percent of Ni is controlled to be 8-13%.
In the austenitic creep-resistant steel of the present invention, W mainly functions to form carbide with C to perform precipitation strengthening, and W solid-dissolved in the matrix can perform solid-solution strengthening, thereby improving creep rupture time and suppressing nitrogen pore defects. W has a smaller chromium equivalence coefficient and less adverse effect on the stability of the austenitic matrix than Mo having a similar effect. When the addition amount of W exceeds 2%, the creep rupture time is not increased, the equivalent of chromium and the average electron vacancy number of the material are increased, and based on the fact that the mass percent of W is controlled to be 0.5-2%.
In the austenitic creep-resistant steel of the present invention, N is a main austenite forming element, and solid-dissolved N can replace about 30 times Ni. However, when the mass percentage of N is more than 0.4%, addition of Cr of more than 25% and W of more than 2% does not suppress the precipitated nitrogen gas hole defects and deteriorates the workability. Based on this, in the technical scheme of the invention, the mass percent of N is controlled to be 0.2-0.4%.
Wherein the tensile strength of the austenitic creep-resistant steel at 1000 ℃ is not lower than 110MPa, the yield strength is not lower than 40MPa, and the elongation after fracture is not lower than 15%.
The creep rupture time of the austenitic creep-resistant steel at 1000 ℃ and 35MPa is not less than 77 h.
The austenitic creep-resistant steel has a thermal conductivity of 22-24W/(m.K) at 800 ℃ and a thermal conductivity of 26-27W/(m.K) at 1000 ℃.
The average linear expansion coefficient of the austenitic creep-resistant steel at 25-800 ℃ is (17-18) x 10～6An average linear expansion coefficient of (17 to 19). times.10 at 25 to 1000 DEG C～6。
In another aspect, the invention also provides a preparation method of the austenite creep-resistant steel, wherein the austenite creep-resistant steel is prepared by adding the raw materials into a medium frequency furnace, smelting the raw materials, and casting the molten raw materials into a mold.
The invention also provides the application of the austenitic creep-resistant steel in an exhaust manifold or a turbocharger housing of an automobile engine.
Wherein the working temperature of the austenitic creep-resistant steel can reach 1050 ℃.
Austenitic creep resistant steels were prepared with reference to the components and proportions in table 1.
Figure 516210DEST_PATH_IMAGE001
After testing the relevant properties in the examples and comparative examples in table 1, the data are summarized in table 2.
Figure 442578DEST_PATH_IMAGE002
As can be seen from the data in fig. 1 and 2 and table 2, the austenitic creep-resistant steel produced by the present invention suppresses the high-temperature ferrite phase and eliminates the precipitation-type nitrogen pore defect; the addition range of nitrogen and carbon elements is optimized, so that the processing cost of the casting is lower than that of common chromium-nickel austenitic heat-resistant steel; excellent mechanical performance at high temperature and long creep rupture time.
In conclusion, the austenitic creep-resistant steel prepared by the method inhibits a high-temperature ferrite phase, and eliminates the defect of precipitation type nitrogen holes; the addition range of nitrogen and carbon elements is optimized, so that the processing cost of the casting is lower than that of common chromium-nickel austenitic heat-resistant steel; excellent mechanical performance at high temperature and long creep rupture time. Under the condition that the cost of raw materials is reduced by more than 60 percent, the high-temperature creep rupture time, the thermal conductivity and the linear expansion coefficient reach the level of 1.4849 heat-resistant steel.
In light of the foregoing description of the preferred embodiment of the present invention, many modifications and variations will be apparent to those skilled in the art without departing from the spirit and scope of the invention. The technical scope of the present invention is not limited to the content of the specification, and must be determined according to the scope of the claims.

Claims (7)

1. The austenitic creep-resistant steel is characterized by comprising the following components in percentage by mass: c: 0.2 to 0.5; si: 0.5-2.0, Mn < 0.5; cr: 20-28; ni: 8-13; p is less than or equal to 0.04; s is less than or equal to 0.3; w: 0.5 to 2; n: 0.2 to 0.4; the balance being iron and other unavoidable impurity elements.
2. The austenitic creep resistant steel of claim 1, wherein the austenitic creep resistant steel has a tensile strength at 1000 ℃ of not less than 110MPa, a yield strength of not less than 40MPa, and a post fracture elongation of not less than 15%.
3. The austenitic creep resistant steel of claim 1, wherein the austenitic creep rupture time at 1000 ℃ and 35MPa is not less than 77 h.
4. The austenitic creep resistant steel of claim 1, wherein the austenitic creep resistant steel has a thermal conductivity of 22-24W/(m-K) at 800 ℃ and 26-27W/(m-K) at 1000 ℃.
5. The austenitic creep resistant steel according to claim 1, wherein the austenitic creep resistant steel has an average linear expansion coefficient of (17-18) x 10 at 25-800 ℃-6An average linear expansion coefficient of (17 to 19). times.10 at 25 to 1000 DEG C-6。
6. A method for preparing austenite creep-resistant steel, which is characterized in that the austenite creep-resistant steel is prepared by adding the raw materials in the claim 1 into a medium frequency furnace for smelting, and then casting into a die.
7. Use of the austenitic creep resistant steel of claim 1 in an automotive engine exhaust manifold or turbocharger housing.
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PCT/CN2022/131885 WO2023134292A1 (en) 2022-01-11 2022-11-15 Cast iron-based austenite creep-resistant steel, and preparation method and use therefor
EP22871096.8A EP4234744A1 (en) 2022-01-11 2022-11-15 Cast iron-based austenite creep-resistant steel, and preparation method and use therefor

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114807769A (en) * 2022-06-23 2022-07-29 科华控股股份有限公司 Double-phase heat-resistant steel with controllable TCP phase distribution and application thereof
CN115637393A (en) * 2022-10-28 2023-01-24 鞍钢集团矿业有限公司 Austenitic heat-resistant steel for chain grate link and preparation method thereof
WO2023134292A1 (en) * 2022-01-11 2023-07-20 科华控股股份有限公司 Cast iron-based austenite creep-resistant steel, and preparation method and use therefor

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117512474B (en) * 2023-10-24 2024-05-07 四川大学 Fe-based shielding alloy for structure/function integrated nuclear radiation protection and preparation method thereof

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54128922A (en) * 1978-03-22 1979-10-05 Hitachi Metals Ltd Heat resistant cast steel excellent in high temperature strength
CN103667977A (en) * 2012-09-06 2014-03-26 无锡新大中薄板有限公司 Antibacterial Austenitic stainless steel band
CN105452505A (en) * 2013-12-09 2016-03-30 新日铁住金株式会社 Austenitic stainless steel sheet and method for producing same
CN109440013A (en) * 2019-01-10 2019-03-08 福建青拓特钢技术研究有限公司 A kind of non-magnetic high corrosion low-nickel austenitic stainless steel
CN109609854A (en) * 2019-01-23 2019-04-12 福建青拓特钢技术研究有限公司 A kind of 700MPa grade high-strength metastable state austeno-martensite stainless steel
CN110144523A (en) * 2018-07-24 2019-08-20 福建青拓特钢技术研究有限公司 A kind of high intensity high corrosion resistance low-nickel austenitic stainless steel and its manufacturing method
CN113862562A (en) * 2021-09-09 2021-12-31 中车戚墅堰机车车辆工艺研究所有限公司 Antioxidant high-creep cast austenitic heat-resistant stainless steel and preparation method thereof

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3969109A (en) * 1974-08-12 1976-07-13 Armco Steel Corporation Oxidation and sulfidation resistant austenitic stainless steel
JP4985941B2 (en) * 2004-04-19 2012-07-25 日立金属株式会社 High Cr high Ni austenitic heat-resistant cast steel and exhaust system parts comprising the same
CN101946018B (en) * 2008-02-22 2013-01-16 日立金属株式会社 Austenitic heat-resistant cast steel and exhaust system components made therefrom
KR101470109B1 (en) * 2010-06-09 2014-12-05 신닛테츠스미킨 카부시키카이샤 Austenitic stainless steel tube having excellent steam oxidation resistance, and method for producing same
US9612008B2 (en) * 2011-06-28 2017-04-04 Nippon Steel & Sumitomo Metal Corporation Austenitic stainless steel tube
CN114086077B (en) * 2022-01-11 2022-05-20 科华控股股份有限公司 Cast iron-based austenite creep-resistant steel and preparation method and application thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54128922A (en) * 1978-03-22 1979-10-05 Hitachi Metals Ltd Heat resistant cast steel excellent in high temperature strength
CN103667977A (en) * 2012-09-06 2014-03-26 无锡新大中薄板有限公司 Antibacterial Austenitic stainless steel band
CN105452505A (en) * 2013-12-09 2016-03-30 新日铁住金株式会社 Austenitic stainless steel sheet and method for producing same
CN110144523A (en) * 2018-07-24 2019-08-20 福建青拓特钢技术研究有限公司 A kind of high intensity high corrosion resistance low-nickel austenitic stainless steel and its manufacturing method
CN109440013A (en) * 2019-01-10 2019-03-08 福建青拓特钢技术研究有限公司 A kind of non-magnetic high corrosion low-nickel austenitic stainless steel
CN109609854A (en) * 2019-01-23 2019-04-12 福建青拓特钢技术研究有限公司 A kind of 700MPa grade high-strength metastable state austeno-martensite stainless steel
CN113862562A (en) * 2021-09-09 2021-12-31 中车戚墅堰机车车辆工艺研究所有限公司 Antioxidant high-creep cast austenitic heat-resistant stainless steel and preparation method thereof

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023134292A1 (en) * 2022-01-11 2023-07-20 科华控股股份有限公司 Cast iron-based austenite creep-resistant steel, and preparation method and use therefor
CN114807769A (en) * 2022-06-23 2022-07-29 科华控股股份有限公司 Double-phase heat-resistant steel with controllable TCP phase distribution and application thereof
CN114807769B (en) * 2022-06-23 2022-10-25 科华控股股份有限公司 Double-phase heat-resistant steel with controllable TCP phase distribution and application thereof
CN115637393A (en) * 2022-10-28 2023-01-24 鞍钢集团矿业有限公司 Austenitic heat-resistant steel for chain grate link and preparation method thereof

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