CN101965416A - Preparation method and the sheet material that obtains like this with austenite stainless steel plate material of strong mechanical performance - Google Patents
Preparation method and the sheet material that obtains like this with austenite stainless steel plate material of strong mechanical performance Download PDFInfo
- Publication number
- CN101965416A CN101965416A CN2009801073261A CN200980107326A CN101965416A CN 101965416 A CN101965416 A CN 101965416A CN 2009801073261 A CN2009801073261 A CN 2009801073261A CN 200980107326 A CN200980107326 A CN 200980107326A CN 101965416 A CN101965416 A CN 101965416A
- Authority
- CN
- China
- Prior art keywords
- steel
- stainless steel
- hot rolled
- rolled sheet
- austenitic stainless
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to the hot rolled plate made by austenitic stainless steel, its chemical constitution comprises, and content is represented with weight: 0.015%≤C≤0.030%; 0.5%≤Mn≤2%; Si≤2%; 16.5%≤Cr≤18%; 6%≤Ni≤7%; S≤0.015%; P≤0.045%; Al≤0.050%; 0.15%≤Nb≤0.31%; 0.12%≤N≤0.16%; Nb and N content make: Nb/8+0.1%≤N≤Nb/8+0.12%, randomly: 0.0005%≤B≤0.0025%, Mo≤0.6%, the surplus of composition is made up of iron and the unavoidable impurities that is derived from melting.
Description
The present invention relates to the preparation of the hot rolled sheet made by austenitic stainless steel, this austenitic stainless steel has strong mechanical performance, and the particularly very favorable combination of mechanical strength and uniform elongation.
For the preparation of the structure unit in the automotive industry, common practice is to adopt the carbon steel sheet material of the coating of different stage, and the carbon steel sheet material of described coating has complicated microstructure more or less.By having the thick sheet production part of 1-3mm.Yet for some part, people wish to have the more combination of high corrosion resistance and high deformability, so that use complicated calendering operation manufactured parts.And well-known, austenitic stainless steel is used widely, owing to its excellent erosion resistance and its mechanical property, especially its high ductibility.For example, 1.4318 the austenitic stainless steel of being called according to EN 10088-1 canonical representation is well-known, its composition contains (content is represented with weight): C≤0.030%, Si≤1.00%, Mn≤2.00%, P≤0.045%, S≤0.015%, Cr:16.50-18.50%, Ni:6.00-8.00%, N 0.10-0.20%.Owing to during deformation at room temperature, form martensite, so this class steel has strong mechanical performance.This class steel is as follows in the typical mechanical property of annealed state: yield strength R
P0.2(corresponding to the conventional yield strength of 0.2% strained): 300-400MPa; Uniform elongation: A 〉=45%, R
m(maximum strength) 〉=700MPa; Product P=R
P0.2(MPa) * uniform elongation=about 15750MPa.%.Can be using these steel grades: C850 by the cold rolling work-hardened condition that is in, the C1000-EN-10088-2 standard, these trades mark correspond respectively to minimum strength 850 and 1000MPa.Raising (the R of the yield strength that this operation is given
P0.2〉=600MPa) also confirm by the unit elongation (A=30%) that reduces simultaneously.Thereby product P has reached about 18000MPa.%.To some application, these performances are gratifying.Yet if require high strength in use, for example for the increase of loss of weight and for the high ability owing to existing shaping operation, these performances still are not enough so.
By cold rolling and alternative method work hardening is by carry out hot rolling and work hardening under enough low temperature.This method has been given the compromise of better unit elongation-intensity, but main drawback is to cause local deformaton in the forming process, causes vermiform (vermiculures) defective.In order to avoid this class vermiform defective in standard 1.4318 steel that after hot rolling, do not have recrystallize, must after this hot rolling, carry out annealing operation.
Therefore, the purpose of this invention is to provide the austenitic stainless steel hot rolled sheet, this austenitic stainless steel has the mechanical property that surpasses or equal above-mentioned 1.4318 type steel grades, and this steel is made cheapness and insensitive to the appearance of vermiform defective.
Purpose of the present invention also provides the hot rolled sheet of being made by austenitic stainless steel, and this austenitic stainless steel has the product P greater than 21000MPa.%, its can with the yield strength R greater than 650MPa
P0.2Make up or can also make up with uniform elongation greater than 45%.
For this purpose, theme of the present invention is the hot rolled sheet of being made by austenitic stainless steel, its product P (R
P0.2(MPa) * and uniform elongation (%)) comprise greater than 21000MPa.% and its chemical constitution, content is represented with weight: 0.015%≤C≤0.030%, 0.5%≤Mn≤2%, Si≤2%, 16.5%≤Cr≤18%, 6%≤Ni≤7%, S≤0.015%, P≤0.045%, Al≤0.050%, 0.15%≤Nb≤0.31%, 0.12%≤N≤0.16%, Nb and N content make:
Nb/8+0.1%≤N≤Nb/8+0.12%, optional: 0.0005%≤B≤0.0025%, Mo≤0.6%, the surplus of composition is made up of iron and the unavoidable impurities that is derived from melting.
According to embodiment preferred, the niobium of this steel and nitrogen content are represented with weight, make: 0.20%≤Nb≤0.31%, 0.12%≤N≤0.16%.
Theme of the present invention is still by the hot rolled sheet of making according to arbitrary above-mentioned austenitic stainless steel of forming, its yield strength R
P0.2Greater than 650MPa, the average austenite grain size that it is characterized in that this steel is that also the non-recrystallization fractional surface is 30-70% and is that also niobium is entirely the form of precipitate less than 6 microns.
Theme of the present invention is still by the hot rolled sheet of making according to the austenitic stainless steel of arbitrary above-mentioned feature, and its uniform elongation is greater than 45%, it is characterized in that niobium do not separate out fully.
Theme of the present invention still prepares the method for the hot rolled sheet of being made by austenitic stainless steel, the yield strength R of this austenitic stainless steel
P0.2Greater than 650MPa, wherein: the work in-process that are formed from steel are provided, and this steel has the composition according to arbitrary above-mentioned composition; Then, with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; Then described work in-process are being lower than under 990 ℃ the rolling finishing temperature rolling and accumulative total draft ε latter two finishing stand (cages finisseuses) greater than 30%.
According to a special embodiment, provide by having the work in-process that the above-mentioned steel of forming is made, it contains 0.20%≤Nb≤0.31%, 0.12%≤N≤0.16%, then with described work in-process be lower than under 970 ℃ the rolling finishing temperature rolling.
Theme of the present invention still prepares the method for the hot rolled sheet of being made by austenitic stainless steel, and the uniform elongation of this austenitic stainless steel is greater than 45%, wherein: the work in-process that are formed from steel are provided, and this steel has the composition according to arbitrary above-mentioned composition; Then, with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; Then with described work in-process be higher than under 1000 ℃ the rolling finishing temperature rolling.
Theme of the present invention still prepares the method for the hot rolled sheet of being made by austenitic stainless steel, the product P (R of this austenitic stainless steel
P0.2(MPa) * uniform elongation (%)) greater than 21000MPa.%, wherein: the work in-process that are formed from steel are provided, and this steel has the composition according to arbitrary above-mentioned composition; Then, with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; Then with described work in-process hot rolling.
Theme of the present invention still is used for purposes at automotive field preparation structure unit by the hot-rolled steel sheet material of making according to the stainless steel of arbitrary above-mentioned feature or by the hot-rolled steel sheet material of arbitrary method for preparing.
By the following description process that provides with by way of example, it is distincter that further feature of the present invention and advantage will become.
After a large amount of tests, the contriver has shown by satisfied above-mentioned difference requirement in accordance with following condition:
About the chemical constitution of steel, carbon content must be equal to or less than 0.030% to avoid the risk to the intergranular corrosion sensitivity.In order to obtain the purpose greater than the yield strength of 650MPa, carbon content must be equal to or greater than 0.015%.
Manganese as silicon, is to have deoxy performance and can improve the well-known element of high-temperature ductility (particularly with the sulphur combination) in liquid state because of it.And at ambient temperature, manganese promotes the stability of austenite phase and reduces stacking fault energy.It also increases the solubleness of nitrogen.When manganese content is 0.5-2%, can obtain these favourable effects at an easy rate.
As manganese, silicon is the element that adds usually for the purpose that makes the liquid steel deoxidation.By solution hardening or its effect on ferrite δ content, silicon also increases yield strength and tensile strength.Yet, be higher than 2%, reduce weldability and high-temperature ductility.
Chromium is because of improving oxidation-resistance and the well-known element of erosion resistance in aqueous medium.When its content is 16.5-18%, obtained this effect satisfactorily.
Nickel is the sufficiently stable at ambient temperature important element of austenite structure of guaranteeing steel.It optimizes content must be determined that described element is the element that promotes that α forms mutually by other relevant in forming element, and as chromium, perhaps those promote the element that γ forms mutually, as carbon and nitrogen.When its content was equal to or greater than 6%, its effect on structure stability was enough.Be higher than 7%, production cost will excessively increase because of the cost of this interpolation element.
Molybdenum can increase corrosion resistance.Randomly, can carry out the interpolation of molybdenum by 0.6% amount at the most.
Boron is used to improve the forging of steel.Randomly, can carry out the interpolation of boron by the amount of 0.0005-0.0025%.Add bigger quantity and will seriously reduce firing temperature.
Sulphur is the element of special deterioration forge hot and erosion resistance, and its content must keep being equal to or less than 0.015%.
Similarly, phosphorus deterioration high-temperature ductility, its content must be less than 0.045% to obtain gratifying result.
Aluminium is the strong reagent that makes the liquid metal deoxidation.Silicon and the combination of manganese content with above-mentioned obtain the effect of optimizing when its content is equal to or less than 0.050%.
Niobium and nitrogen are the important elements that the present invention is used to prepare the austenitic stainless steel purpose with strong mechanical performance.
Niobium delays the recrystallize during the hot rolling, for given rolling finishing temperature, and the work hardening factor that its interpolation causes keeping higher (it is said that this hot rolling is " work hardening "), thereby increased the tensile strength of this steel.As Ti, niobium is commonly used to resist the formation (EN1.4580 and EN 1.4550Nb stabilization austenitic stainless steel) of chromium carbide.Finally, it can cause the formation in the intermetallic phase of giving improvement aspect the heat resistanceheat resistant creep property.
Nitrogen is hardened element in interstitial solid solution, and it has increased yield strength the most in this regard.Also know, in sosoloid as the strong stability agent of austenite phase with as chromium carbide Cr
23C
6The delayed-action activator of separating out.In solidification stages, the solubleness of nitrogen has experienced maximum, and this content is too high to cause the formation of a large amount of defectives in the metal.
Be that niobium is added in the combination of sclerosis purpose and nitrogen is slightly different ordinary in austenitic stainless steel.Within the scope of the invention, shown that the composition that has adds near the particular combinations that the stainless steel of above-mentioned 1.4318 steel advantageously has benefited from niobium and nitrogen, optimized that these situations are mentioned as follows in order under situation accurately, to obtain the purpose of certain mechanical property:
At first, shown that nitrogen content is 0.12-0.16%, and content of niobium is 0.15-0.31%, niobium and nitrogen content make: Nb/8+0.1%≤N≤Nb/8+0.12% (concerning 1), the hot rolled sheet to be rolled that feasible preparation has strong mechanical performance becomes possibility, and do not need as 1.4318 conventional steel at rolling after annealing, the calendering parts are without undergoing the formation of vermiform defective.
Nitride NbN separate out (it occurs in during the hot rolling end of a period) reduced the amount of nitrogen in the sosoloid.After all obtainable niobiums were separated out fully, above-mentioned relation formula (1) kept having the nitrogen as (N 〉=0.1%) as much in 1.4318 steel grades in sosoloid.
Therefore, this makes that obtaining same metastable austenite in envrionment temperature becomes possibility.Because it is, limited by the possibility that increases N content reduction Ni content in the solubility limit of solidificating period nitrogen in steel.For Cr, Mn in the steel according to the present invention and Ni content, nitrogen content must be equal to or less than 0.16%.
Must there be the niobium of sufficient amount so that obtain hardening effect and postpone recrystallize.Must make this content suitable to obtain to be higher than the NbN solvus of rolling finishing temperature, so that obtain to separate out in the hot rolling end of a period.
Can make that according to niobium of the present invention and nitrogen content a large amount of NbN of acquisition separates out after hot rolling.
The combination of the nitrogen of the niobium of 0.15-0.31% (preferred 0.20-0.31% niobium) and 0.12-0.16% adds that (niobium and nitrogen content make, and: Nb/8+0.1%≤N≤Nb/8+0.12%) makes the possibility that is combined into of yield strength/unit elongation that acquisition is favourable, and its product P is greater than 21000MPa.%.
Except iron, the surplus of composition is made up of the unavoidable impurities that is derived from melting, for example Sn or Pb.
Preparation in accordance with the present invention is implemented as follows:
The steel melting that will have above-mentioned composition.Steel can be cast billet after this melting, or in prevailing situation continuous casting precedent such as the thick slab form of 150-250mm.Can also between the steel reverse roll, the thin slab form with tens mm thick cast.These casting work in-process at first are heated to 1250-1320 ℃ temperature.The purpose of 1250 ℃ of temperature is dissolving any niobium base precipitates (nitride and carbonitride).Yet temperature must be lower than 1320 ℃, in order to avoid too near solidus temperature, can reach this solidus temperature in some line of segragation and cause the appearance of local liquid phase, and this will be harmful to thermoforming.Between reverse roll directly in the situation of casting thin sheet base, can after casting, be lower than under 1250 ℃ the temperature and directly beginning to carry out these half-finished steps of hot rolling, so not need intermediary reheat step in this case.
Rollingly carry out on the Continuous Heat milling train usually, this hot rolls is particularly including pony roughing mill and finishing stand.Show, by special control the draft of latter two finishing stand will obtain extra high yield strength R
P02: if the thickness that enters the sheet material of penult finishing stand is expressed as e
N-2And the thickness that leaves the sheet material of last finishing stand is expressed as e
N, the accumulative total draft of latter two finishing stand top is expressed as so:
According to the present invention, shown when rolling finishing temperature be lower than 990 ℃ and when accumulative total draft ε greater than 30% the time, finally obtain the yield strength R of product
P0.2Greater than 650MPa, at this moment niobium is entirely the form of precipitate.
For the Nb content of 0.20-0.31% and the nitrogen content of 0.12-0.16%,, obtained this minimum value of 650MPa when rolling finishing temperature is lower than 970 ℃ and ε greater than 30% the time.
According to the present invention, shown when rolling finishing temperature is higher than 1000 ℃, can obtain uniform elongation greater than 45% hot rolled sheet.In this case, niobium is partly separated out.
After the hot rolling, the sheet material of acquisition is insensitive and do not need process annealing to the appearance of vermiform defective.
As unrestricted embodiment, following result will show the favourable characteristic that the present invention gives.
Embodiment:
Have the steel of forming shown in the following table by casting and produced work in-process (in wt%):
Table 1: the composition of steel (in wt%)
Underlined value: be not according to the present invention.
With the steel work in-process 1280 ℃ of following reheat 30 minutes.Carry out hot-rolled manipulation by between 900-1100 ℃, changing rolling finishing temperature and adding up draft ε then, so that reach the final thickness of 3mm.Steel sheets I1-1, I1-2, the sheet material that expressions such as I1-3 are obtained by identical work in-process I1 rolling under different condition.The microstructure of the steel that is obtained is by measure characterizing, and particularly measures the fractional surface of recrystallize austenite phase, with respect to the mark of separating out niobium and the average grain size of total niobium.For incomplete recrystallized tissue, the measurement of back is partly carried out at the recrystallize of tissue.Also measured tensile mechanical properties, particularly yield strength R
P0.2And uniform elongation.Also write down the local deformaton that during tension test, can occur.As everyone knows, the vermiform defective that occurs during the appearance of this local deformaton and the shaping operation is relevant.
The result is as shown in table 2 below.
The preparation condition of table 2 hot rolled sheet, microstructure characteristics and mechanical property
TFL: rolling finishing temperature;
R
P0.2: in the conventional yield strength of 0.2% strain place
A: uniform elongation;
ε: the accumulative total draft of latter two rolling pass.
Thereby last showing according to steel I1 of the present invention and I2 has particularly advantageous product R greater than 21000MPa.%
P0.2* A (MPa.%), and reference R steel does not possess such product, irrelevant with rolling condition.
This table also shows, when the non-recrystallization mark is 30-70% and average grain size during less than 6 microns, and yield strength R
P0.2Greater than 650MPa (test I1-1, I1-2, I2-1, I2-2).And, when the non-recrystallization mark greater than 70% the time, rate elongation is tending towards reducing.
Obtained these performances for the steel with 0.15-0.31% content of niobium and 0.12-0.16% nitrogen content: wherein niobium and nitrogen make: Nb/8+0.1%≤N≤Nb/8+0.12%, rolling finishing temperature is lower than 990 ℃ and accumulative total draft ε greater than 30%.
For having 0.20-0.31% content of niobium and 0.12-0.16% nitrogen content, niobium and nitrogen content make: the steel of Nb/8+0.1%≤N≤Nb/8+0.12% has obtained these performances (test I2-1 and I2-2) greater than 30% the time when rolling finishing temperature is lower than 970 ℃ and accumulative total draft ε.
When niobium is not exclusively separated out (test I1-3, I1-4, I2-4, I2-5), uniform elongation is greater than 45%.Form for steel according to the present invention, when rolling finishing temperature is higher than 1000 ℃, obtained such result.As a comparison, reference steel does not provide such performance.
Therefore, according to whether wanting to produce the steel that steel with extra high yield strength or alternate have the high-elongation ability, select certain preparation condition (rolling finishing temperature and accumulative total draft) more especially.
And, do not show the platform that shows local deformaton according to the stress-strain curve of steel of the present invention, and regardless of hot-rolled condition, by contrast, local deformaton appears in reference steel, no matter its recrystallize (test R-1, R-2, R-3) when partly.This point by guaranteeing not have the vermiform defective for the shaping operation particularly advantageous.
Thereby, because the extra high mechanical property of hot-rolled steel sheet material of the present invention, particularly its very favorable yield strength * uniform elongation product, so it is advantageously used in the application that requires high formability and high corrosion resistance.When using it for automotive industry, its advantage will advantageously obtain appreciating because of the economy preparation of structure unit.
Claims (9)
1. the hot rolled sheet of making by austenitic stainless steel, its product P (R
P0.2(MPa) * and uniform elongation (%)) comprise greater than 21000MPa.% and its chemical constitution, content is represented with weight:
0.015％≤C≤0.030％
0.5％≤Mn≤2％
Si≤2％
16.5％≤Cr≤18％
6％≤Ni≤7％
S≤0.015％
P≤0.045％
Al≤0.050％
0.15％≤Nb≤0.31％
0.12％≤N≤0.16％
Nb and N content make:
Nb/8+0.1％≤N≤Nb/8+0.12％
Randomly:
0.0005％≤B≤0.0025％
Mo≤0.6％，
The surplus of forming is made up of iron and the unavoidable impurities that is derived from melting.
2. the hot rolled sheet of making according to the austenitic stainless steel of claim 1 is characterized in that the niobium of described steel and nitrogen content represent to make with weight:
0.20％≤Nb≤0.31％
0.12％≤N≤0.16％。
3. according to the hot rolled sheet of making by austenitic stainless steel of claim 1 or 2, its yield strength R
P0.2Greater than 650MPa, the average austenite grain size that it is characterized in that described steel is that also the non-recrystallization fractional surface is 30-70% and is that also niobium is entirely the form of precipitate less than 6 microns.
4. according to the hot rolled sheet of being made by austenitic stainless steel of claim 1 or 2, its uniform elongation is greater than 45%, it is characterized in that niobium do not separate out fully.
5. the method for preparing the hot rolled sheet of making by austenitic stainless steel, its yield strength R
P0.2Greater than 650MPa, wherein:
-work in-process of making according to the steel of forming of claim 1 or 2 by having are provided; Then
-with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; And then
-with described work in-process be lower than under 990 ℃ the rolling finishing temperature rolling and in the end the accumulative total draft ε on two finishing stands greater than 30%.
6. according to the preparation method of claim 5, it is characterized in that providing by have the work in-process made according to the steel of forming of claim 2 and with described work in-process be lower than under 970 ℃ the rolling finishing temperature rolling.
7. prepare the method for the hot rolled sheet of being made by austenitic stainless steel, its uniform elongation is greater than 45%, wherein:
-work in-process of making according to the steel of forming of claim 1 or 2 by having are provided; Then
-with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; And then
-with described work in-process be higher than under 1000 ℃ the rolling finishing temperature rolling.
8. the method for preparing the hot rolled sheet of making by austenitic stainless steel, its product P (R
P0.2(MPa) * uniform elongation (%)) greater than 21000MPa.%, wherein:
-work in-process of making according to the steel of forming of claim 1 or 2 by having are provided; Then
-with the temperature of described work in-process reheat to 1250 ℃-1320 ℃; And then
-then with described work in-process hot rolling.
9. the hot rolled sheet of making according to each stainless steel among the claim 1-4, or, be used for purposes at automotive field preparation structure unit according to the hot rolled sheet of each method preparation among the claim 5-8.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP08290267A EP2103705A1 (en) | 2008-03-21 | 2008-03-21 | Method of manufacturing sheets of austenitic stainless steel with high mechanical properties |
| EP08290267.7 | 2008-03-21 | ||
| PCT/FR2009/000225 WO2009115702A2 (en) | 2008-03-21 | 2009-03-03 | Process for manufacturing austenitic stainless steel plate having high mechanical properties, and plate thus obtained |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101965416A true CN101965416A (en) | 2011-02-02 |
Family
ID=39642753
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2009801073261A Pending CN101965416A (en) | 2008-03-21 | 2009-03-03 | Preparation method and the sheet material that obtains like this with austenite stainless steel plate material of strong mechanical performance |
Country Status (10)
| Country | Link |
|---|---|
| US (1) | US20110061776A1 (en) |
| EP (2) | EP2103705A1 (en) |
| JP (1) | JP2011528751A (en) |
| KR (1) | KR20100124774A (en) |
| CN (1) | CN101965416A (en) |
| BR (1) | BRPI0908996B1 (en) |
| CA (1) | CA2714218C (en) |
| ES (1) | ES2543356T3 (en) |
| TW (1) | TWI405858B (en) |
| WO (1) | WO2009115702A2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112609126A (en) * | 2020-11-13 | 2021-04-06 | 宁波宝新不锈钢有限公司 | Austenitic stainless steel for nuclear power equipment and preparation method thereof |
| CN113430455A (en) * | 2021-05-31 | 2021-09-24 | 中国科学院金属研究所 | High-strength austenitic stainless steel resistant to liquid lead (lead bismuth) corrosion and preparation method thereof |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114934240B (en) * | 2022-04-25 | 2023-10-10 | 中国科学院金属研究所 | Preparation method of ultra-high-strength high-corrosion-resistance high-nitrogen austenitic stainless steel |
| CN115537672B (en) * | 2022-07-19 | 2023-08-18 | 燕山大学 | Low-cost austenitic steel with yield strength greater than 1000MPa and warm rolling preparation process thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4975131A (en) * | 1984-03-30 | 1990-12-04 | Aichi Steel Works, Ltd. | High strength hot worked stainless steel |
Family Cites Families (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3284250A (en) * | 1964-01-09 | 1966-11-08 | Int Nickel Co | Austenitic stainless steel and process therefor |
| JPS5915979B2 (en) * | 1980-07-03 | 1984-04-12 | 新日本製鐵株式会社 | Stainless steel alloy with fewer rolling defects during hot rolling |
| JPS6053726B2 (en) * | 1981-07-31 | 1985-11-27 | 新日本製鐵株式会社 | Method for manufacturing austenitic stainless steel sheets and steel strips |
| DE3407307A1 (en) * | 1984-02-24 | 1985-08-29 | Mannesmann AG, 4000 Düsseldorf | USE OF A CORROSION-RESISTANT AUSTENITIC IRON-CHROME-NICKEL-NITROGEN ALLOY FOR MECHANICALLY HIGH-QUALITY COMPONENTS |
| JP2602015B2 (en) * | 1986-08-30 | 1997-04-23 | 愛知製鋼株式会社 | Stainless steel excellent in corrosion fatigue resistance and seawater resistance and method for producing the same |
| JPH06306464A (en) * | 1993-04-28 | 1994-11-01 | Nippon Steel Corp | Production of hot rolled austenitic stainless steel plate |
| JPH0860244A (en) * | 1994-08-23 | 1996-03-05 | Nippon Steel Corp | Production of thick austenitic stainless steel plate |
| JPH0987809A (en) * | 1995-09-27 | 1997-03-31 | Kawasaki Steel Corp | Hot rolled plate of chromium-containing austenitic stainless steel for automobile exhaust system material |
| JP4190617B2 (en) * | 1998-06-23 | 2008-12-03 | 大平洋金属株式会社 | Method for producing hot rolled sheet of stainless steel |
| KR100356930B1 (en) * | 1998-09-04 | 2002-10-18 | 스미토모 긴조쿠 고교 가부시키가이샤 | Stainless steel for engine gasket and production method therefor |
| JP3449282B2 (en) * | 1999-03-04 | 2003-09-22 | 住友金属工業株式会社 | Austenitic stainless steel with excellent high-temperature strength and ductility |
| JP2001181734A (en) * | 1999-12-24 | 2001-07-03 | Kawasaki Steel Corp | METHOD FOR PRODUCING Cr-CONTAINING HOT ROLLED STEEL SHEET EXCELLENT IN SCALE ADHESION |
| JP3603726B2 (en) * | 2000-03-03 | 2004-12-22 | 住友金属工業株式会社 | Austenitic stainless steel sheet for electronic components |
| JP2002194506A (en) * | 2000-12-25 | 2002-07-10 | Sumitomo Metal Ind Ltd | Stainless steel sheet and production method for the same |
| JP4321066B2 (en) * | 2001-04-27 | 2009-08-26 | 住友金属工業株式会社 | Metal gasket, material thereof and method for producing the same |
| FR2864108B1 (en) * | 2003-12-22 | 2006-01-27 | Ugine Et Alz France | STAINLESS STEEL SHEET HAVING HIGH RESISTANCE AND LENGTH ELONGATION, AND METHOD OF MANUFACTURE |
| JP4813123B2 (en) * | 2005-08-10 | 2011-11-09 | 新日鐵住金ステンレス株式会社 | Method for producing austenitic stainless steel sheet with excellent surface quality |
-
2008
- 2008-03-21 EP EP08290267A patent/EP2103705A1/en not_active Withdrawn
-
2009
- 2009-03-03 JP JP2011500247A patent/JP2011528751A/en active Pending
- 2009-03-03 US US12/922,786 patent/US20110061776A1/en not_active Abandoned
- 2009-03-03 ES ES09722337.4T patent/ES2543356T3/en active Active
- 2009-03-03 CN CN2009801073261A patent/CN101965416A/en active Pending
- 2009-03-03 WO PCT/FR2009/000225 patent/WO2009115702A2/en active Application Filing
- 2009-03-03 EP EP20090722337 patent/EP2257652B1/en active Active
- 2009-03-03 BR BRPI0908996-9A patent/BRPI0908996B1/en active IP Right Grant
- 2009-03-03 KR KR1020107020786A patent/KR20100124774A/en not_active Application Discontinuation
- 2009-03-03 CA CA2714218A patent/CA2714218C/en active Active
- 2009-03-09 TW TW098107530A patent/TWI405858B/en active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4975131A (en) * | 1984-03-30 | 1990-12-04 | Aichi Steel Works, Ltd. | High strength hot worked stainless steel |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112609126A (en) * | 2020-11-13 | 2021-04-06 | 宁波宝新不锈钢有限公司 | Austenitic stainless steel for nuclear power equipment and preparation method thereof |
| CN113430455A (en) * | 2021-05-31 | 2021-09-24 | 中国科学院金属研究所 | High-strength austenitic stainless steel resistant to liquid lead (lead bismuth) corrosion and preparation method thereof |
| CN113430455B (en) * | 2021-05-31 | 2022-05-17 | 中国科学院金属研究所 | High-strength austenitic stainless steel resistant to liquid lead and bismuth corrosion and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2257652B1 (en) | 2015-04-29 |
| TWI405858B (en) | 2013-08-21 |
| BRPI0908996A2 (en) | 2019-03-06 |
| WO2009115702A3 (en) | 2009-11-12 |
| US20110061776A1 (en) | 2011-03-17 |
| JP2011528751A (en) | 2011-11-24 |
| KR20100124774A (en) | 2010-11-29 |
| EP2257652A2 (en) | 2010-12-08 |
| BRPI0908996B1 (en) | 2019-07-09 |
| WO2009115702A2 (en) | 2009-09-24 |
| TW200951233A (en) | 2009-12-16 |
| ES2543356T3 (en) | 2015-08-18 |
| CA2714218A1 (en) | 2009-09-24 |
| EP2103705A1 (en) | 2009-09-23 |
| CA2714218C (en) | 2013-09-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101263239B (en) | Method of producing high-strength steel plates with excellent ductility and plates thus produced | |
| US9714459B2 (en) | Heat-resistant austenitic stainless steel sheet | |
| JP3838216B2 (en) | Austenitic stainless steel | |
| CN101724789B (en) | Austenitic stainless steel medium-thick plate and manufacture method thereof | |
| JP6729823B2 (en) | Method of manufacturing wear-resistant steel | |
| JP4644076B2 (en) | High strength thin steel sheet with excellent elongation and hole expansibility and manufacturing method thereof | |
| KR20120070603A (en) | High-toughness abrasion-resistant steel and manufacturing method therefor | |
| EP1277848A1 (en) | High-strength heat-resistant steel, process for producing the same, and process for producing high-strength heat-restistant pipe | |
| EP0989196A1 (en) | High-strength heat-resistant steel, process for producing high-strength heat-resistant steel, and process for producing high-strength heat-resistant pipe | |
| CN112752862B (en) | High-strength cold-rolled steel sheet having high hole expansibility, high-strength hot-dip galvanized steel sheet, and methods for producing these | |
| CN108699656B (en) | Steel material and steel pipe for oil well | |
| JP4074555B2 (en) | Manufacturing method of steel for high strength low alloy boilers with excellent creep characteristics | |
| CN114502760B (en) | Ferritic stainless steel sheet, method for producing same, and ferritic stainless steel member | |
| CN101965416A (en) | Preparation method and the sheet material that obtains like this with austenite stainless steel plate material of strong mechanical performance | |
| JP7324361B2 (en) | Austenitic stainless steel with improved strength and method for producing the same | |
| KR20150074943A (en) | Hot rolled steel sheet having excellent deformation anisotropy in sheared edge and anti fatigue property and method for manufacturing the same | |
| EP3887556B1 (en) | Cold rolled annealed steel sheet with high hole expansion ratio and manufacturing process thereof | |
| CN114080463B (en) | High-strength steel sheet and method for producing same | |
| CN111479944A (en) | Ferrite-based stainless steel having excellent impact toughness and method for producing the same | |
| KR102463485B1 (en) | Ferritic stainless steel sheet, manufacturing method thereof, and ferritic stainless steel member | |
| JP3780956B2 (en) | High strength steel plate with excellent SR resistance and method for producing the same | |
| KR20210014055A (en) | High strength steel sheet and manufacturing method thereof | |
| JP4201310B2 (en) | High strength steel plate with excellent SR resistance and method for producing the same | |
| CN110114490A (en) | Thick steel sheet and its manufacturing method with 450MPa grades of tensile strength and excellent hydrogen-induced cracking resistance | |
| JP2000248332A (en) | Die excellent in heat resistance, and its manufacture |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C12 | Rejection of a patent application after its publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20110202 |