CN111118411B - High-strength stainless steel and manufacturing method thereof - Google Patents
High-strength stainless steel and manufacturing method thereof Download PDFInfo
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses a high-strength stainless steel which comprises the following components in percentage by mass: 0.04-0.09 mass%, Si: 1.5 to 2.5 mass%, Mn: less than 1.0 mass%, Cr: 13.0 to 15.0 mass%, Ni: 6.0-7.0 mass%, N: less than 0.010 mass%, Mo: 0.6 to 1.0 mass%, Cu: 0.6 to 1.0 mass%, Ti: 0.3-0.8 mass%, B: less than 0.03 mass%, V: less than 0.3 mass%, P: 0.030 mass% or less, S: less than or equal to 0.005 mass%, and the balance of Fe and inevitable impurity elements; wherein, Cr + Mo +0.5Ti is Creq; ni +30 × (C + N) +0.5Mn +0.25Cu ═ Nieq; Creq/Nieq is more than or equal to 1.4 and less than or equal to 1.8. The high-strength stainless steel disclosed by the invention has the advantages that the hot working process is a full-austenite structure through reasonable component design, the structure after solution treatment is a dual-phase structure of austenite and martensite, high-temperature ferrite is preferentially precipitated during solidification, the generation of welding hot cracks is effectively reduced, and meanwhile, the strength of a welding seam after welding is ensured to be equivalent to that of a base metal.
Description
Technical Field
The invention relates to the technical field of high-strength stainless steel and preparation thereof, in particular to high-strength stainless steel and a manufacturing method thereof.
Background
The stainless steel is continuously expanded in the development and application field for more than one hundred years, but is greatly limited as a structural functional material due to low strength.
One of the ways to improve the strength is work hardening, for example, the yield strength of 300 series stainless steel is less than 300MPa, and cold working is adopted to improve the strength, for example, patents CN101259483A and CN101234395A, the strength of the stainless steel base material after work hardening is improved, but the strength of the welding seam after welding as a structural part is rapidly reduced, the yield strength of the welding seam is close to the strength of the base material in a solid solution state, and the yield strength is generally less than 300 MPa. The other is the solid solution strengthening and the grain refinement of nitrogen, such as duplex stainless steel and high-nitrogen stainless steel, and the yield strength of the solid solution state can reach more than 500 MPa. However, nitrogen precipitates in a hot working temperature range, and the hot working performance is reduced, so that the industrial production of dual-phase steel and high-nitrogen austenitic stainless steel strip steel has serious edge cracks. The third is martensite precipitation hardening stainless steel, the solid solution strength can reach more than 700MPa, but the martensite precipitation hardening stainless steel has large difficulty in industrial production, poor welding adaptability and easy occurrence of defects such as hot cracks and the like on a welding line.
In the prior art, the patent with the publication number of CN 110129658 is to add cheap Mn to reduce the Ms point on the basis of 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo, and the specific chemical components are as follows: c < 0.05%, Si < 0.50%, Mn: 6-10%, Cr: 12-16%, Ni: 4.5-6.5, Mo: 0.5-3%, S < 0.01%, P < 0.03%;
the chemical components of patent with publication number CN 106636901 are: c: 0.02-0.04%, Cr: 11.6-11.9%, Si: 0.25 to 0.29%, Mn: 0.52-0.63%, Ni: 0.45-0.52%, Re: 0.15-0.17%, Zr: 0.45-0.62%, etc., and the yield strength is more than or equal to 450 MPa;
the patent with publication number CN101984123 is to perform different flexible treatment processes on 301L stainless steel to obtain high-strength stainless steel for 5 strength grades for high-speed trains;
patent publication No. CN101386962 is a high manganese high nitrogen austenitic stainless steel.
Therefore, it is necessary to develop a high strength stainless steel having a yield strength of more than 700MPa, which is easy to industrially produce and weld.
Based on the above situation, the present invention provides a high strength stainless steel and a method for manufacturing the same, which can effectively solve the above problems.
Disclosure of Invention
The invention aims to provide high-strength stainless steel and a manufacturing method thereof. The high-strength stainless steel disclosed by the invention has the advantages that the hot working process is a full-austenite structure through reasonable component design, the structure after solution treatment is a dual-phase structure of austenite and martensite, high-temperature ferrite is preferentially precipitated during solidification, the generation of welding hot cracks is effectively reduced, and meanwhile, the strength of a welding seam after welding is ensured to be equivalent to that of a base metal.
In order to solve the technical problems, the technical scheme provided by the invention is as follows:
a high-strength stainless steel comprising, in mass%,
c: 0.04 to 0.09 mass%,
Si: 1.5 to 2.5 mass%,
Mn: less than 1.0 mass%,
Cr: 13.0 to 15.0 mass%,
Ni: 6.0 to 7.0 mass%,
N: less than 0.010 mass%,
Mo: 0.6 to 1.0 mass%,
Cu: 0.6 to 1.0 mass%,
Ti: 0.3 to 0.8 mass%,
B: less than 0.03 mass%,
V: less than 0.3% by mass
P: less than or equal to 0.030 mass%,
S: less than or equal to 0.005 mass%,
The balance of Fe and inevitable impurity elements;
wherein, Cr + Mo +0.5Ti is Creq;
Ni+30*(C+N)+0.5Mn+0.25Cu＝Nieq；
1.4≤Creq/Nieq≤1.8。
in the invention, Creq is chromium equivalent of stainless steel, Nieq is nickel equivalent, and the ratio Creq/Nieq of the two needs to be kept in a certain range. The Creq/Nieq is more than or equal to 1.4, so that ferrite is preferentially precipitated in the welding solidification process, the generation of welding hot cracks is reduced, and the strength of a welding seam after welding is equivalent to that of a base metal. The Creq/Nieq is less than or equal to 1.8, so that the hot working process is a full austenite structure and the hot working is easy. 1.4 to 1.8 of Creq/Nieq, and the structure after solution treatment can be a dual-phase structure of austenite and martensite.
The high-strength stainless steel disclosed by the invention has the advantages that the hot working process is a full-austenite structure through reasonable component design, the structure after solution treatment is a dual-phase structure of austenite and martensite, high-temperature ferrite is preferentially precipitated during solidification, the generation of welding hot cracks is effectively reduced, and meanwhile, the strength of a welding seam after welding is ensured to be equivalent to that of a base metal; the high-strength stainless steel of the invention has the following advantages:
1. the strength is improved without work hardening, and the welding seam strength after the strip steel is welded can be ensured to be equivalent to that of the base metal.
2. The hot working process is a full austenite structure, and the hot working performance is improved.
3. Ferrite is preferentially precipitated in the solidification process during welding, the generation of welding thermal cracks is reduced, and the weldability is improved.
Among the components of the high-strength stainless steel of the present invention,
c is a solid solution strengthening element and can effectively improve the strength at room temperature. However, too high carbon content forms carbide with Cr element and distributes at grain boundary, which reduces corrosion resistance of stainless steel. At the same time, carbon is also a strong austenite stabilizing element, and excessively high carbon content requires an increase in cooling rate to transform austenite into martensite. Therefore, the C content is defined as 0.04% to 0.09% by mass.
Si is a strong deoxidizing element and also a strong ferrite forming element, and the Si content is defined as less than 1.5 to 2.5 mass% in order to favor the preferential formation of high-temperature ferrite during solidification.
Mn is a weak austenite forming and strongly stabilizing austenite element, and can improve the strength of a solid solution state parent material. However, excessive Mn lowers the martensitic transformation temperature, resulting in lower weld strength. Therefore, the Mn content is defined as less than 1.0 mass%.
Cr is an element that strongly forms ferrite, reduces the austenite phase region, and improves the corrosion resistance of stainless steel by forming a dense layer of chromium oxide with oxygen in the air. However, excessive Cr causes excessive ferrite content in the solidification process, and reduces the strength of the weld joint. Cr is defined as 13.0 to 15.0 mass%.
Ni is an austenite forming element and is effective in improving toughness. However, since nickel is relatively expensive and strongly forms and stabilizes austenite, an excessive amount of Ni is disadvantageous for improving the strength of a weld after welding. Ni is defined as 6.0 to 7.0 mass%.
N is a strong austenite forming element and can improve the hardness and corrosion resistance of the solid solution austenitic stainless steel, but excessive N content can form TiN particles and reduce the castability in the smelting process. Nitrogen also tends to form oxides with chromium, reducing hot workability. Therefore, the N content is controlled to be less than 0.01%.
Mo is a ferrite forming element and is beneficial to improving the pitting corrosion resistance. Meanwhile, Mo is a precious metal, and the increase of Mo content causes the increase of cost. Therefore, Mo is defined as 0.6 to 1.0 mass%.
Cu is an austenite forming element and improves cold workability, but too high Cu content results in a decrease in high-temperature hot workability. Therefore, Cu is defined as 0.6 to 1.0 mass%.
Ti is also a ferrite forming element, is easy to combine with C, N in steel to form precipitates, and can be used as a nucleation point in the welding process to refine grains and improve the strength of a welding seam due to high dissolving temperature of TiN. However, too high a Ti content may deteriorate castability during smelting and deteriorate the surface quality of the cast steel slab. Therefore, Ti is defined as 0.3 to 0.8 mass%.
B and V are selected elements, and the grains of the parent metal and the welding seam can be refined by a certain adding amount, so that the strength of the parent metal and the welding seam is improved. However, excessive amounts are easily aggregated at grain boundaries to deteriorate hot workability, and are therefore defined as less than 0.03 and 0.3 mass%, respectively.
P and S are both unavoidable impurity elements, but adversely affect the performance, and should be less than 0.03 mass% and 0.005 mass%, respectively. The balance being Fe.
The high-strength stainless steel is mainly applied to the fields of packaging mechanical equipment, conveying equipment, laminated plates and the like with high requirements on the performance of the stainless steel.
The invention also provides a manufacturing method of the high-strength stainless steel, which comprises the following steps:
A. selecting a steel slab meeting the composition requirements of the high-strength stainless steel components;
B. carrying out temperature grinding on the steel plate blank;
C. heating the steel plate blank subjected to temperature grinding at the heating rate of 2-4 ℃/min to a target temperature of 1220-1230 ℃, and then preserving heat;
D. c, hot rolling the steel plate blank treated in the step C by adopting a hot continuous rolling mill or a steckel mill to 3-10 mm to obtain a hot rolled coil (black skin coil);
E. carrying out solution treatment and acid pickling on the hot-rolled coil to obtain a white skin coil;
F. cold rolling the white skin coil on a twenty-high rolling mill or a continuous rolling mill to obtain a cold-rolled coil;
G. carrying out solution treatment and acid pickling on the cold-rolled coil again to obtain strip steel;
H. and D, improving the plate shape of the strip steel obtained in the step G through a leveling roller with a large roller diameter to obtain the high-strength stainless steel.
Preferably, in the step a, the steel slab meeting the composition requirements of the high-strength stainless steel is smelted by adding alloy into full scrap steel or molten iron, and then is cast into the steel slab after microalloying at a refining station.
Preferably, in the step B, the temperature after the sharpening with the temperature is higher than 200 ℃.
In order to ensure the surface quality of the steel plate blank, temperature grinding is adopted, and the temperature after grinding is more than 200 ℃.
Preferably, in the step C, the steel slab polished with temperature is heated in a walking beam or a chamber type heating furnace.
Preferably, in the step C, the heat preservation time is calculated according to the thickness of the installed steel plate blank and is calculated according to the heat preservation time of 0.2-0.4 min/mm.
Preferably, in the step D, the steel slab treated in the step C is hot-rolled by using a hot continuous rolling mill or a steckel mill.
Preferably, in the steps E and G, the temperature of the solution treatment is 1000-1100 ℃, and the pickling process adopts an austenitic stainless steel pickling process.
Preferably, in step F, the cold rolling reduction is more than 30% in order to ensure the surface finish of the final product.
Preferably, in the step H, the strip steel obtained in the step G is subjected to leveling roller with a large roller diameter to improve the plate shape, and the leveling elongation is less than 1%.
Compared with the prior art, the invention has the following advantages and beneficial effects:
the high-strength stainless steel disclosed by the invention has the advantages that the hot working process is a full-austenite structure through reasonable component design, the structure after solution treatment is a dual-phase structure of austenite and martensite, high-temperature ferrite is preferentially precipitated during solidification, the generation of welding hot cracks is effectively reduced, and meanwhile, the strength of a welding seam after welding is ensured to be equivalent to that of a base metal; the high-strength stainless steel of the invention has the following advantages:
1. the strength is improved without work hardening, and the welding seam strength after the strip steel is welded can be ensured to be equivalent to that of the base metal.
2. The hot working process is a full austenite structure, and the hot working performance is improved.
3. Ferrite is preferentially precipitated in the solidification process during welding, the generation of welding thermal cracks is reduced, and the weldability is improved.
Among the components of the high-strength stainless steel of the present invention,
c is a solid solution strengthening element and can effectively improve the strength at room temperature. However, too high carbon content forms carbide with Cr element and distributes at grain boundary, which reduces corrosion resistance of stainless steel. At the same time, carbon is also a strong austenite stabilizing element, and excessively high carbon content requires an increase in cooling rate to transform austenite into martensite. Therefore, the C content is defined as 0.04% to 0.09% by mass.
Si is a strong deoxidizing element and also a strong ferrite forming element, and the Si content is defined as less than 1.5 to 2.5 mass% in order to favor the preferential formation of high-temperature ferrite during solidification.
Mn is a weak austenite forming and strongly stabilizing austenite element, and can improve the strength of a solid solution state parent material. However, excessive Mn lowers the martensitic transformation temperature, resulting in lower weld strength. Therefore, the Mn content is defined as less than 1.0 mass%.
Cr is an element that strongly forms ferrite, reduces the austenite phase region, and improves the corrosion resistance of stainless steel by forming a dense layer of chromium oxide with oxygen in the air. However, excessive Cr causes excessive ferrite content in the solidification process, and reduces the strength of the weld joint. Cr is defined as 13.0 to 15.0 mass%.
Ni is an austenite forming element and is effective in improving toughness. However, since nickel is relatively expensive and strongly forms and stabilizes austenite, an excessive amount of Ni is disadvantageous for improving the strength of a weld after welding. Ni is defined as 6.0 to 7.0 mass%.
N is a strong austenite forming element and can improve the hardness and corrosion resistance of the solid solution austenitic stainless steel, but excessive N content can form TiN particles and reduce the castability in the smelting process. Nitrogen also tends to form oxides with chromium, reducing hot workability. Therefore, the N content is controlled to be less than 0.01%.
Mo is a ferrite forming element and is beneficial to improving the pitting corrosion resistance. Meanwhile, Mo is a precious metal, and the increase of Mo content causes the increase of cost. Therefore, Mo is defined as 0.6 to 1.0 mass%.
Cu is an austenite forming element and improves cold workability, but too high Cu content results in a decrease in high-temperature hot workability. Therefore, Cu is defined as 0.6 to 1.0 mass%.
Ti is also a ferrite forming element, is easy to combine with C, N in steel to form precipitates, and can be used as a nucleation point in the welding process to refine grains and improve the strength of a welding seam due to high dissolving temperature of TiN. However, too high a Ti content may deteriorate castability during smelting and deteriorate the surface quality of the cast steel slab. Therefore, Ti is defined as 0.3 to 0.8 mass%.
B and V are selected elements, and the grains of the parent metal and the welding seam can be refined by a certain adding amount, so that the strength of the parent metal and the welding seam is improved. However, excessive amounts are easily aggregated at grain boundaries to deteriorate hot workability, and are therefore defined as less than 0.03 and 0.3 mass%, respectively.
P and S are both unavoidable impurity elements, but adversely affect the performance, and should be less than 0.03 mass% and 0.005 mass%, respectively. The balance being Fe.
In the invention, Creq is chromium equivalent of stainless steel, Nieq is nickel equivalent, and the ratio Creq/Nieq of the two needs to be kept in a certain range. The Creq/Nieq is more than or equal to 1.4, so that ferrite is preferentially precipitated in the welding solidification process, the generation of welding hot cracks is reduced, and the strength of a welding seam after welding is equivalent to that of a base metal. The Creq/Nieq is less than or equal to 1.8, so that the hot working process is a full austenite structure and the hot working is easy. 1.4 to 1.8 of Creq/Nieq, and the structure after solution treatment can be a dual-phase structure of austenite and martensite.
The high-strength stainless steel is mainly applied to the fields of packaging mechanical equipment, conveying equipment, laminated plates and the like with high requirements on the performance of the stainless steel.
The manufacturing method has simple process and simple and convenient operation, and saves manpower and equipment cost.
Drawings
FIG. 1 is a process flow diagram of a method of manufacturing the present invention.
Detailed Description
In order that those skilled in the art will better understand the technical solutions of the present invention, the following description of the preferred embodiments of the present invention is provided in connection with specific examples, which should not be construed as limiting the present patent.
The test methods or test methods described in the following examples are conventional methods unless otherwise specified; the reagents and materials, unless otherwise indicated, are conventionally obtained commercially or prepared by conventional methods.
Example 1:
a high-strength stainless steel comprising, in mass%,
c: 0.04 to 0.09 mass%,
Si: 1.5 to 2.5 mass%,
Mn: less than 1.0 mass%,
Cr: 13.0 to 15.0 mass%,
Ni: 6.0 to 7.0 mass%,
N: less than 0.010 mass%,
Mo: 0.6 to 1.0 mass%,
Cu: 0.6 to 1.0 mass%,
Ti: 0.3 to 0.8 mass%,
B: less than 0.03 mass%,
V: less than 0.3% by mass
P: less than or equal to 0.030 mass%,
S: less than or equal to 0.005 mass%,
The balance of Fe and inevitable impurity elements;
wherein, Cr + Mo +0.5Ti is Creq;
Ni+30*(C+N)+0.5Mn+0.25Cu＝Nieq；
1.4≤Creq/Nieq≤1.8。
the invention also provides a manufacturing method of the high-strength stainless steel, which comprises the following steps:
A. selecting a steel slab meeting the composition requirements of the high-strength stainless steel components;
B. carrying out temperature grinding on the steel plate blank;
C. heating the steel plate blank subjected to temperature grinding at the heating rate of 2-4 ℃/min to a target temperature of 1220-1230 ℃, and then preserving heat;
D. c, hot rolling the steel plate blank treated in the step C by adopting a hot continuous rolling mill or a steckel mill to 3-10 mm to obtain a hot rolled coil;
E. carrying out solution treatment and acid pickling on the hot-rolled coil to obtain a white skin coil;
F. cold rolling the white skin coil on a twenty-high rolling mill or a continuous rolling mill to obtain a cold-rolled coil;
G. carrying out solution treatment and acid pickling on the cold-rolled coil again to obtain strip steel;
H. and D, improving the plate shape of the strip steel obtained in the step G through a leveling roller with a large roller diameter to obtain the high-strength stainless steel.
Preferably, in the step a, the steel slab meeting the composition requirements of the high-strength stainless steel is smelted by adding alloy into full scrap steel or molten iron, and then is cast into the steel slab after microalloying at a refining station.
Preferably, in the step B, the temperature after the sharpening with the temperature is higher than 200 ℃.
In order to ensure the surface quality of the steel plate blank, temperature grinding is adopted, and the temperature after grinding is more than 200 ℃.
Preferably, in the step C, the steel slab polished with temperature is heated in a walking beam or a chamber type heating furnace.
Preferably, in the step C, the heat preservation time is calculated according to the thickness of the installed steel plate blank and is calculated according to the heat preservation time of 0.2-0.4 min/mm.
Preferably, in the step D, the steel slab treated in the step C is hot-rolled by using a hot continuous rolling mill or a steckel mill.
Preferably, in the steps E and G, the temperature of the solution treatment is 1000-1100 ℃, and the pickling process adopts an austenitic stainless steel pickling process.
Preferably, in step F, the cold rolling reduction is more than 30% in order to ensure the surface finish of the final product.
Preferably, in the step H, the strip steel obtained in the step G is subjected to leveling roller with a large roller diameter to improve the plate shape, and the leveling elongation is less than 1%.
Example 2:
and casting the smelted molten steel into a plate blank, fully grinding the plate blank at a certain temperature to remove the surface defects of the plate blank, wherein the temperature after grinding is more than 200 ℃. The chemical composition of the steel slab is shown in table 1.
TABLE 1 chemical composition of the steel slab of the present example
| Example 2 | C | Si | Mn | S | P | Cr | Ni | Cu | Mo | Ti | N | B | V | Creq/Nieq |
| 1 | 0.04 | 1.5 | 0.9 | 0.005 | 0.03 | 13.0 | 6.7 | 0.6 | 0.6 | 0.3 | 0.01 | 0 | 0.3 | 1.56 |
| 2 | 0.045 | 1.7 | 0.5 | 0.002 | 0.023 | 14.1 | 6.9 | 0.8 | 0.8 | 0.35 | 0.01 | 0.001 | 0.2 | 1.68 |
| 3 | 0.055 | 1.8 | 0.4 | 0.001 | 0.028 | 14.0 | 6.7 | 0.84 | 0.7 | 0.38 | 0.007 | 0.002 | 0.1 | 1.66 |
| 4 | 0.09 | 1.8 | 0.8 | 0.003 | 0.025 | 15.0 | 7.5 | 1 | 0.8 | 0.5 | 0.008 | 0.003 | 0 | 1.45 |
| 5 | 0.06 | 1.75 | 0.5 | 0.001 | 0.027 | 13.5 | 7.1 | 0.7 | 0.75 | 0.4 | 0.004 | 0.002 | 0.24 | 1.50 |
Heating the polished steel plate blank by a heating furnace, hot rolling, solid solution pickling of black skin coils, cold rolling, annealing pickling of white skin coils and plate shape improvement. The process parameters of this example are shown in tables 2 and 3. The strengths of the base material and the weld are shown in table 4.
TABLE 2 temperature, slab thickness, heating temperature and holding time for the grinding of this example
| Example 2 | Grinding temperature (. degree.C.) | Thickness of steel slab (mm) | Heating temperature (. degree.C.) | Incubation time (min) |
| 1 | 220 | 200 | 1220 | 60 |
| 2 | 200 | 220 | 1230 | 50 |
| 3 | 240 | 180 | 1225 | 40 |
| 4 | 245 | 190 | 1228 | 45 |
| 5 | 230 | 210 | 1225 | 55 |
Table 3 thickness of black skin coil, cold rolling reduction, solid solution temperature of black skin coil and solid solution temperature and flat elongation of white skin coil of this example.
TABLE 4 parent metal and weld strength of the present example
The above is only a preferred embodiment of the present invention, and it should be noted that the above preferred embodiment should not be considered as limiting the present invention, and the protection scope of the present invention should be subject to the scope defined by the claims. It will be apparent to those skilled in the art that various modifications and adaptations can be made without departing from the spirit and scope of the invention, and these modifications and adaptations should be considered within the scope of the invention.
Claims (9)
1. A high-strength stainless steel characterized by comprising, in mass%,
c: 0.04 to 0.09 mass%,
Si: 1.5 to 2.5 mass%,
Mn: less than 1.0 mass%,
Cr: 13.0 to 15.0 mass%,
Ni: 6.0 to 7.0 mass%,
N: less than 0.010 mass%,
Mo: 0.6 to 1.0 mass%,
Cu: 0.6 to 1.0 mass%,
Ti: 0.3 to 0.8 mass%,
B: less than 0.03 mass%,
V: less than 0.3% by mass
P: less than or equal to 0.030 mass%,
S: less than or equal to 0.005 mass%,
The balance of Fe and inevitable impurity elements;
wherein Cr + Mo +0.5Ti = Creq;
Ni+30*(C+N)+0.5Mn+0.25Cu=Nieq；
1.4≤Creq/Nieq≤1.8；
the manufacturing method of the high-strength stainless steel comprises the following steps:
A. selecting a steel slab meeting the composition requirements of the high-strength stainless steel components;
B. carrying out temperature grinding on the steel plate blank;
C. heating the steel plate blank subjected to temperature grinding at the heating rate of 2-4 ℃/min to a target temperature of 1220-1230 ℃, and then preserving heat;
D. c, hot rolling the steel plate blank treated in the step C by adopting a hot continuous rolling mill or a steckel mill to 3-10 mm to obtain a hot rolled coil;
E. carrying out solution treatment and acid pickling on the hot-rolled coil to obtain a white skin coil;
F. cold rolling the white skin coil on a twenty-high rolling mill or a continuous rolling mill to obtain a cold-rolled coil;
G. carrying out solution treatment and acid pickling on the cold-rolled coil again to obtain strip steel;
H. and D, improving the plate shape of the strip steel obtained in the step G through a leveling roller with a large roller diameter to obtain the high-strength stainless steel.
2. The high-strength stainless steel according to claim 1, wherein in the step a, the steel slab meeting the composition requirements of the high-strength stainless steel is smelted by using all-scrap steel or molten iron plus alloy to obtain molten steel meeting the composition requirements, and then the molten steel is microalloyed in a refining station and cast into the steel slab.
3. The high strength stainless steel according to claim 1, wherein the temperature at which the warm tip thinning ends in step B is greater than 200 ℃.
4. The high strength stainless steel according to claim 1, wherein in step C, the slab after warm grinding is heated in a walking beam or a chamber furnace.
5. The high-strength stainless steel according to claim 1, wherein in the step C, the heat preservation time is 0.2-0.4 min/mm calculated according to the thickness of the steel slab.
6. The high strength stainless steel according to claim 1, wherein the steel slab treated in the step C is hot-rolled using a hot continuous rolling mill or a steckel mill in the step D.
7. The high-strength stainless steel according to claim 1, wherein in the steps E and G, the temperature of the solution treatment is 1000-1100 ℃, and the pickling process adopts a pickling process of austenitic stainless steel.
8. The high strength stainless steel of claim 1, wherein the cold rolling reduction in step F is greater than 30% in order to ensure the surface finish of the final product.
9. The high strength stainless steel according to claim 1, wherein in step H, the strip obtained in step G is passed through a flattening roll with a large roll diameter to improve the strip shape, and the flattened elongation is less than 1%.
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| CN101784687A (en) * | 2007-10-03 | 2010-07-21 | 住友金属工业株式会社 | Austenitic stainless steel |
| JP2011252208A (en) * | 2010-06-03 | 2011-12-15 | Nisshin Steel Co Ltd | Heat-resistant austenitic stainless steel for metal gasket |
| CN110484834A (en) * | 2019-08-21 | 2019-11-22 | 首钢集团有限公司 | A kind of Cr, Mn alloying TRIP steel and preparation method thereof |
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| JP2011252208A (en) * | 2010-06-03 | 2011-12-15 | Nisshin Steel Co Ltd | Heat-resistant austenitic stainless steel for metal gasket |
| CN110484834A (en) * | 2019-08-21 | 2019-11-22 | 首钢集团有限公司 | A kind of Cr, Mn alloying TRIP steel and preparation method thereof |
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