CN116411157A - Preparation method of high-strength high-nitrogen austenitic stainless steel plate - Google Patents
Preparation method of high-strength high-nitrogen austenitic stainless steel plate Download PDFInfo
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- CN116411157A CN116411157A CN202111667461.0A CN202111667461A CN116411157A CN 116411157 A CN116411157 A CN 116411157A CN 202111667461 A CN202111667461 A CN 202111667461A CN 116411157 A CN116411157 A CN 116411157A
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N nitrogen Substances N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 title claims abstract description 87
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 75
- 229910052757 nitrogen Inorganic materials 0.000 title claims abstract description 73
- 238000002360 preparation method Methods 0.000 title abstract description 5
- 238000005096 rolling process Methods 0.000 claims abstract description 55
- 238000010438 heat treatment Methods 0.000 claims abstract description 24
- 238000011282 treatment Methods 0.000 claims abstract description 23
- 238000001816 cooling Methods 0.000 claims abstract description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 6
- 238000003825 pressing Methods 0.000 claims abstract description 3
- 238000000034 method Methods 0.000 claims description 26
- 229910045601 alloy Inorganic materials 0.000 claims description 16
- 239000000956 alloy Substances 0.000 claims description 16
- 229910000831 Steel Inorganic materials 0.000 claims description 14
- 239000010959 steel Substances 0.000 claims description 14
- 239000011651 chromium Substances 0.000 claims description 7
- SJKRCWUQJZIWQB-UHFFFAOYSA-N azane;chromium Chemical compound N.[Cr] SJKRCWUQJZIWQB-UHFFFAOYSA-N 0.000 claims description 5
- 230000006698 induction Effects 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 238000005303 weighing Methods 0.000 claims description 5
- 238000003723 Smelting Methods 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000000843 powder Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 20
- 238000012545 processing Methods 0.000 abstract description 6
- 239000000243 solution Substances 0.000 description 15
- 230000000052 comparative effect Effects 0.000 description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 229910001566 austenite Inorganic materials 0.000 description 10
- 238000005260 corrosion Methods 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 8
- 229910001220 stainless steel Inorganic materials 0.000 description 7
- 239000010935 stainless steel Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 5
- 230000000087 stabilizing effect Effects 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000003287 optical effect Effects 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 230000000930 thermomechanical effect Effects 0.000 description 2
- 206010020751 Hypersensitivity Diseases 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007123 defense Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009026 tissue transition Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/56—Elongation control
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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Abstract
The invention discloses a preparation method of a high-strength high-nitrogen austenitic stainless steel plate, which comprises the steps of carrying out solution treatment on the high-nitrogen austenitic stainless steel plate in a heating furnace at 1150+/-50 ℃ for 6-8 h, and then cooling the high-nitrogen austenitic stainless steel plate by water to quickly cool the high-nitrogen austenitic stainless steel plate to room temperature; after the solution treatment is finished, the high-nitrogen austenitic stainless steel plate is firstly placed into a heating furnace at 300 ℃ to be kept for 10 min, and then is placed into the heating furnace at 300 ℃ to be kept for 5min before each rolling, and the accumulated pressing quantity is 40-75%. The invention uses warm rolling technology, compared with the room temperature rolling, the rolling force required by the room temperature rolling is smaller, the strength of the obtained material is equivalent to that of the room temperature rolling material, and the processing is easier.
Description
Technical Field
The invention belongs to the field of austenitic stainless steel plate manufacturing, and particularly relates to a method for preparing a high-strength plate by adopting warm rolling after solution treatment of high-nitrogen austenitic stainless steel.
Background
The high-nitrogen austenitic stainless steel has the characteristics of good toughness, creep resistance, strong pitting corrosion resistance, no magnetism and the like. Nitrogen element is dissolved in austenitic stainless steel in a gap atom form, occupies octahedral gap positions of face-centered cubes, causes lattice distortion to have pinning effect on dislocation, and can replace nickel element to play a role in stabilizing austenite; and meanwhile, the corrosion resistance of the austenitic steel can be improved. The excellent properties of the high-nitrogen austenitic stainless steel lead the high-nitrogen austenitic stainless steel to have wide application prospects in the fields of transportation, biomedicine, energy chemical industry, national defense and military industry and the like. Although the yield strength of high nitrogen steels (around 465 MPa) is higher than 316L (around 250 MPa), there is still a need to increase the strength to meet the application requirements under more severe service conditions, for which specific process treatments are required to increase the strength.
Austenitic stainless steel is generally subjected to plastic deformation treatment to improve its strength, and rolling is one of the most commonly used methods. However, since the high-nitrogen austenitic stainless steel has strong work hardening capacity, the rolling force required by the rolling at room temperature is huge, the requirement on the rolling mill is high, the energy loss is large, the rolling mill is easy to overload and influence the service life of equipment when the rolling with large deformation is carried out, and the industrial mass production difficulty is large. FIG. 1 shows the work hardening rate versus true stress curve and true stress-strain curve for high nitrogen austenitic stainless steel at various temperatures, which can be found to be very high at room temperature, well above 300 ℃ and 600 ℃; meanwhile, the yield strength of the high-nitrogen austenitic stainless steel at room temperature is 465MPa, the yield strength at 300 ℃ and 600 ℃ is 252 MPa, and the yield strength is reduced by about 2 times. In this regard, if the high-nitrogen austenitic stainless steel is subjected to heat treatment in advance so as to reduce the deformation resistance of the material, the rolling difficulty of the high-nitrogen austenitic stainless steel is expected to be reduced, and a new idea is provided for the production of high-strength high-nitrogen steel.
Disclosure of Invention
In order to solve the problems, the invention provides a method for preparing a high-strength high-nitrogen austenitic stainless steel plate by a warm rolling process. The yield strength of the plate obtained by the method is more than or equal to 1430 MPa, the tensile strength is more than or equal to 1525 MPa, and the uniform elongation is about 0.03.
The technical scheme for realizing the purpose of the invention is as follows: the high-strength high-nitrogen austenitic stainless steel plate comprises the following alloy components in percentage by mass: c is less than or equal to 0.068, si is less than or equal to 0.42, ni is less than or equal to 1.48, cr is less than or equal to 21.74, mn is less than or equal to 15.12, N is less than or equal to 0.85, and the balance is Fe.
Preferably, the alloy comprises the following components in percentage by mass: 0.05-0.07% of C, 0.40-0.45% of Si, 1.40-1.5% of Ni, 20-22% of Cr, 15-15.5% of Mn, 0.77-0.85% of N and the balance of Fe.
More preferably, the alloy comprises the following components in percentage by mass: C0.068,Si 0.42,Ni 1.48,Cr 21.74,Mn 15.12,N 0.85, the balance being Fe.
The preparation method of the high-strength high-nitrogen austenitic stainless steel plate comprises the following steps:
(1) Weighing corresponding high-purity metal powder according to the alloy components of the high-strength high-nitrogen austenitic stainless steel plate, wherein the introduction of nitrogen adopts high-purity chromium nitride, a steel ingot is smelted by using a pressurized vacuum induction furnace, and then the steel ingot is continuously rolled at 1000-1100 ℃ to obtain a plate with the thickness of 15-20 mm;
(2) Solution treatment: carrying out solution treatment on the obtained plate in a heating furnace at 1150+/-50 ℃ for 6-8 h, and then cooling the plate by water to quickly cool the plate to room temperature to obtain a single-phase high-nitrogen austenitic stainless steel plate with a single austenitic structure;
(3) Warm rolling: and after the solution treatment is finished, performing warm rolling on the single-phase high-nitrogen austenitic stainless steel plate.
Preferably, the warm rolling comprises the following specific processes: firstly, placing the high-nitrogen austenitic stainless steel plate into a heating furnace at 300 ℃ for heat preservation for 10 min, and then placing the high-nitrogen austenitic stainless steel plate into the heating furnace at 300 ℃ for heat preservation for 5min before each rolling, wherein the accumulated pressing quantity is 40-75%.
Compared with the prior art, the invention has the remarkable advantages that:
(1) Compared with the room temperature rolling, the warm rolling process has smaller rolling force, the strength of the obtained material is equivalent to that of the room temperature rolling material, and the processing is easier;
(2) The equipment used by the invention is simple, is easy to operate, and is beneficial to large-scale industrial production;
(3) The yield strength of the high-nitrogen austenitic stainless steel prepared by the method is more than or equal to 1430 MPa, the tensile strength is more than or equal to 1525 MPa, and the uniform elongation is about 0.03.
Drawings
FIG. 1 is a graph of tensile properties of high nitrogen austenitic stainless steel at various temperatures; (a) A work hardening rate-true stress curve, and (b) a true stress-strain curve.
Fig. 2 is a schematic diagram of a process flow.
FIG. 3 is a photograph of the optical structure of example 1 after solution treatment at various magnification.
FIG. 4 shows the mirror structure of the room temperature rolled and warm rolled samples, wherein (a) and (b) are respectively 40% of the room temperature rolled sample of comparative example 1 and 75% of the room temperature rolled sample of comparative example 3; (c) (d) were each 45% warm rolled at 300℃in example 1 and 75% warm rolled at 300℃in example 3.
Fig. 5 is an engineering stress-strain curve of the sheet stretching experiments after the treatments of examples 1, 2, 3 and comparative examples 1, 2, 3.
Fig. 6 is a graph of the schiff tissue transition after Hull modification.
Detailed Description
The present invention will be described in further detail with reference to examples.
The design principle of the alloy element composition of the invention is as follows:
ni is a powerful austenite stabilizing element in the existing commercial austenitic stainless steel, and can enlarge the austenitic phase region as N. However, since Ni resources are limited and are noble metals, and Ni easily causes allergic reactions in human bodies, ni-containing austenitic stainless steel has limited applications in the food and medical fields.
The element C is one of the austenite forming elements and has a stronger stabilizing effect than Ni, and is present in the stainless steel in the form of a interstitial solid solution, and has a solid solution strengthening effect. However, the existence of the C element easily causes carbide precipitation of the stainless steel in the thermo-mechanical processing process, and the mechanical properties of the stainless steel are seriously affected.
The N element has the following three main roles in austenitic stainless steel: (1) The N element can improve the stability of an austenite structure, enlarge an austenite phase region and partially or completely replace the effect of Ni. (2) The yield strength and tensile strength of the steel are improved by solid solution strengthening, grain boundary strengthening and precipitation strengthening. (3) The N element can improve the local corrosion resistance of the austenitic stainless steel, and particularly improves the pitting corrosion resistance and crevice corrosion resistance. The aim of obtaining stable austenitic structure and reducing the production cost of stainless steel can be achieved by reducing the content of nickel element and adding enough nitrogen element.
The excellent corrosion resistance of austenitic stainless steel is achieved by adding a high content of Cr element. However, cr has a strong effect on ferrite formation to strongly reduce the austenite phase region, which is disadvantageous for the formation of austenite structure. An increase in the Cr content will lead to an increased tendency for the formation of detrimental intermetallic compounds (sigma phases) during the thermo-mechanical treatment. In high nitrogen austenitic stainless steel, cr also forms CrN, cr with nitrogen 2 Compounds such as N; cr also forms M with carbon when the carbon content is high 23 C 6 And the like. The precipitation of such intermetallic compounds and carbonitrides both reduce the corrosion resistance and mechanical properties of the material.
Mn is also a typical austenite stabilizing element, but its austenite stabilizing ability is weak compared with N. In the Fe-Cr-Mn alloy, if the Cr content exceeds 14%, a single austenite structure cannot be obtained by the effect of Mn alone, and the excessive Mn content adversely affects the corrosion resistance of the steel.
Si is enriched in the oxidizing solution to form SiO on the surface of the stainless steel 2 The pitting potential of the stainless steel is increased. However, too much silicon may deteriorate the mechanical properties of the stainless steel.
When designing the alloy composition of the high-nitrogen austenitic stainless steel, not only the independent action of each alloy element, but also the coordination influence action among each alloy element are considered, so that the high-quality high-nitrogen austenitic stainless steel is obtained. The alloy composition of the high-strength high-nitrogen austenitic stainless steel sheet was determined according to the Hull-corrected schiff transformation diagram (see fig. 6) and formulas (1) and (2).
The following examples and FIG. 2 illustrate the preparation of the high strength high nitrogen austenitic stainless steel sheet material of the present invention.
Example 1
(1) Weighing raw materials according to the alloy components of the high-strength high-nitrogen austenitic stainless steel plate, wherein the nitrogen element is introduced into the high-strength high-nitrogen austenitic stainless steel plate by using high-purity chromium nitride, smelting the high-strength high-nitrogen austenitic stainless steel plate by using a pressurized vacuum induction furnace to obtain a steel ingot, and then continuously rolling the steel ingot at 1000-1100 ℃ to obtain a plate with the thickness of 15-20 mm;
(2) Solution treatment: the material was put into a 1150 ℃ oven for solution treatment 8 h, followed by water cooling. Removing oxide skin on the surface of the material, processing the material into a plate with the thickness of 10 mm, and carrying out solution treatment to obtain a single-phase high-nitrogen austenitic stainless steel plate with uniform structure, wherein the mirror structure is shown in figure 3;
(3) Warm rolling: the materials are firstly put into a heating furnace at 300 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness is rolled for 6 times to limit 5.5 mm, the total rolling amount is about 45 percent, and the sample optical lens structure is shown in figure 4 c;
(4) The high-nitrogen austenitic stainless steel plate obtained by the method in the example has yield strength of 1430 MPa, tensile strength of 1525 MPa and uniform elongation of 0.03. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Example 2
(1) Weighing raw materials according to the alloy components of the high-strength high-nitrogen austenitic stainless steel plate, wherein the nitrogen element is introduced into the high-strength high-nitrogen austenitic stainless steel plate by using high-purity chromium nitride, smelting the high-strength high-nitrogen austenitic stainless steel plate by using a pressurized vacuum induction furnace to obtain a steel ingot, and then continuously rolling the steel ingot at 1000-1100 ℃ to obtain a plate with the thickness of 15-20 mm;
(2) Solution treatment: the plate was put into a 1150 ℃ heating furnace for solution treatment 8 h, followed by water cooling. Removing oxide skin on the surface of the material, processing the material into a plate with the thickness of 10 mm, and carrying out solution treatment to obtain a single-phase high-nitrogen austenitic stainless steel plate with uniform structure, wherein the mirror structure is the same as that of example 1;
(3) Warm rolling: the materials are firstly put into a heating furnace at 300 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness is rolled for 4 mm in 9 passes, and the total rolling amount is about 60%;
(4) The high-nitrogen austenitic stainless steel plate obtained by the method in the example has the yield strength of 1592 MPa, the tensile strength of 1764 MPa and the uniform elongation of 0.03. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Example 3
(1) Weighing raw materials according to the alloy components of the high-strength high-nitrogen austenitic stainless steel plate, wherein the nitrogen element is introduced into the high-strength high-nitrogen austenitic stainless steel plate by using high-purity chromium nitride, smelting the high-strength high-nitrogen austenitic stainless steel plate by using a pressurized vacuum induction furnace to obtain a steel ingot, and then continuously rolling the steel ingot at 1000-1100 ℃ to obtain a plate with the thickness of 15-20 mm;
(2) Solution treatment: the plate was put into a 1150 ℃ heating furnace for solution treatment 8 h, followed by water cooling. Removing oxide skin on the surface of the material, processing the material into a plate with the thickness of 10 mm, and carrying out solution treatment to obtain a single-phase high-nitrogen austenitic stainless steel plate with uniform structure, wherein the mirror structure is the same as that of example 1;
(3) Warm rolling: the materials are firstly put into a heating furnace at 300 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness was rolled by about 2.5 mm in 12 passes, the total rolling amount was about 75%, and the sample mirror structure was as shown in FIG. 4 d;
(4) The high-nitrogen austenitic stainless steel sheet obtained by the method in the example has the yield strength of 1613 MPa, the tensile strength of 1788 MPa and the uniform elongation of 0.03. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Comparative example 1
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method of the embodiment 1;
(2) And (3) rolling at room temperature: the plate thickness is rolled for 6 mm in 8 passes at room temperature, the total rolling amount is about 40%, and the sample optical lens structure is shown in fig. 4 a;
(3) The high-nitrogen austenitic stainless steel sheet obtained by the method of the comparative example has the yield strength of 1370 MPa, the tensile strength of 1534 MPa and the uniform elongation of 0.03. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Comparative example 2
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method of the embodiment 2;
(2) And (3) rolling at room temperature: the plate thickness is rolled by about 4 mm in 12 passes at room temperature, and the total rolling amount is about 60%;
(3) The high-nitrogen austenitic stainless steel sheet obtained by the method of the comparative example has the yield strength of 1594 MPa, the tensile strength of 1706 MPa and the uniform elongation of 0.025. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Comparative example 3
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method of the embodiment 1;
(2) And (3) rolling at room temperature: the plate thickness was rolled at room temperature in 16 passes to about 2.5 and mm, the total rolling amount was about 75%, and the sample optical lens structure was as shown in FIG. 4 b;
(3) The high nitrogen austenitic stainless steel sheet obtained by the above method of this comparative example has a yield strength of 1688 MPa, a tensile strength of 1830 MPa, and a uniform elongation of 0.025. The engineering stress-strain curve of the treated sheet is shown in fig. 5.
Comparative example 4
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method of the embodiment 1;
(2) Warm rolling: the materials are firstly put into a heating furnace at 600 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness is rolled for 6 times to restrict 6 mm, and the total rolling amount is about 40%;
(3) The high-nitrogen austenitic stainless steel sheet obtained by the method in the example has the yield strength of 1262 MPa, the tensile strength of 1413 MPa and the uniform elongation of 0.034.
Comparative example 5
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method of the embodiment 2;
(2) Warm rolling: the materials are firstly put into a heating furnace at 600 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness is rolled for 4 mm in 9 passes, and the total rolling amount is about 60%;
(3) The high-nitrogen austenitic stainless steel sheet obtained by the method in the example has the yield strength of 1369 MPa, the tensile strength of 1515 MPa and the uniform elongation of 0.03.
Comparative example 6
(1) A single-phase high-nitrogen austenitic stainless steel sheet with uniform structure and thickness of 10 mm is obtained in the first and second steps according to the method described in the embodiment 3;
(2) Warm rolling: the materials are firstly put into a heating furnace at 600 ℃ to be kept for 10 min, and then are kept for 5min in the heating furnace before each pass of rolling. The plate thickness is rolled by about 3 mm in 12 passes, and the total rolling amount is about 70%;
(3) The high-nitrogen austenitic stainless steel sheet obtained by the method in the example has the yield strength of 1530 MPa, the tensile strength of 1625 MPa and the uniform elongation of 0.03.
Claims (5)
1. The high-strength high-nitrogen austenitic stainless steel plate is characterized by comprising the following alloy components in percentage by mass: c is less than or equal to 0.068, si is less than or equal to 0.42, ni is less than or equal to 1.48, cr is less than or equal to 21.74, mn is less than or equal to 15.12, N is less than or equal to 0.85, and the balance is Fe.
2. The austenitic stainless steel sheet according to claim 1, wherein the alloy composition, in mass%, is: 0.05-0.07% of C, 0.40-0.45% of Si, 1.40-1.5% of Ni, 20-22% of Cr, 15-15.5% of Mn, 0.77-0.85% of N and the balance of Fe.
3. The austenitic stainless steel sheet according to claim 1, wherein the alloy composition, in mass%, is: C0.068,Si 0.42,Ni 1.48,Cr 21.74,Mn 15.12,N 0.85, the balance being Fe.
4. A method of producing an austenitic stainless steel sheet according to any of claims 1-3, characterized in that it comprises the steps of:
(1) Weighing corresponding high-purity metal powder according to the alloy components of the austenitic stainless steel plate, wherein the nitrogen element is introduced by adopting high-purity chromium nitride, smelting by using a pressurized vacuum induction furnace to obtain a steel ingot, and then continuously rolling at 1000-1100 ℃ to obtain a plate with the thickness of 15-20 mm;
(2) Solution treatment: carrying out solution treatment on the obtained plate in a heating furnace at 1150+/-50 ℃ for 6-8 h, and then cooling the plate by water to quickly cool the plate to room temperature to obtain a single-phase high-nitrogen austenitic stainless steel plate with a single austenitic structure;
(3) Warm rolling: and after the solution treatment is finished, performing warm rolling on the single-phase high-nitrogen austenitic stainless steel plate.
5. The method according to claim 4, wherein the warm rolling comprises the following steps: firstly, placing the high-nitrogen austenitic stainless steel plate into a heating furnace at 300+/-5 ℃ for heat preservation for 10 min, and then placing the high-nitrogen austenitic stainless steel plate into the heating furnace at 300+/-5 ℃ for heat preservation for 5min before each rolling, wherein the accumulated pressing quantity is 40-75%.
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