EP2257652A2 - Procede de fabrication de tôles d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenues - Google Patents
Procede de fabrication de tôles d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenuesInfo
- Publication number
- EP2257652A2 EP2257652A2 EP09722337A EP09722337A EP2257652A2 EP 2257652 A2 EP2257652 A2 EP 2257652A2 EP 09722337 A EP09722337 A EP 09722337A EP 09722337 A EP09722337 A EP 09722337A EP 2257652 A2 EP2257652 A2 EP 2257652A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- hot
- stainless steel
- product
- austenitic stainless
- steel
- 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.)
- Granted
Links
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 20
- 238000000034 method Methods 0.000 title claims description 10
- 230000008569 process Effects 0.000 title claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 28
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 27
- 239000000203 mixture Substances 0.000 claims abstract description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 239000000126 substance Substances 0.000 claims abstract description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 46
- 239000010955 niobium Substances 0.000 claims description 46
- 229910000831 Steel Inorganic materials 0.000 claims description 40
- 239000010959 steel Substances 0.000 claims description 40
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 25
- 238000005096 rolling process Methods 0.000 claims description 18
- 239000000047 product Substances 0.000 claims description 17
- 239000011265 semifinished product Substances 0.000 claims description 17
- 230000009467 reduction Effects 0.000 claims description 10
- 230000001186 cumulative effect Effects 0.000 claims description 9
- 229910001220 stainless steel Inorganic materials 0.000 claims description 9
- 239000002244 precipitate Substances 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- 239000010935 stainless steel Substances 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 4
- 238000003723 Smelting Methods 0.000 abstract 1
- 238000005098 hot rolling Methods 0.000 description 13
- 239000011651 chromium Substances 0.000 description 8
- 229910052804 chromium Inorganic materials 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 238000007493 shaping process Methods 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 238000005266 casting Methods 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 230000004807 localization Effects 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- -1 silicon Chemical compound 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000003475 lamination Methods 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 101150087698 alpha gene Proteins 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000012736 aqueous medium Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
Definitions
- the present invention relates to the manufacture of hot rolled sheets of austenitic stainless steels having high mechanical characteristics, and in particular a combination of mechanical strength and very advantageous distributed elongation.
- the parts are made from sheets of thickness ranging from 1 to 3 mm. For some parts, however, we would like to simultaneously have a higher corrosion resistance combined with a large capacity of deformation so
- austenitic stainless steels are commonly used because of their excellent resistance to corrosion and their mechanical characteristics, in particular their high ductility.
- known austenitic stainless steels designated according to EN 10088-1 0 by the reference 1.4318 whose composition contains (content expressed by weight): C ⁇ 0.030%, Si ⁇ 1.00%, Mn ⁇ 2 , 00%, P ⁇ 0.045%, S ⁇ 0.015%, Cr: 16.50 to 18.50%, Ni: 6.00 to 8.00%, N: 0.10 to 0.20%. These steels have high mechanical properties due to the formation of martensite during deformation at room temperature.
- yield strength Rp o , 2 yield strength corresponding to 0.2% elongation
- A> 45% Rm (maximum strength)> 700 MPa.
- the product P then reaches about 18,000 MPa. These characteristics are satisfactory for some applications. They remain nevertheless insufficient in the case where one wishes high resistance in service, for example for a gain in relief, and a great aptitude for prior shaping operations.
- An alternative method to cold rolling hardening is hot rolling work at a sufficiently low temperature. This method confers a better compromise elongation - resistance, but has the major disadvantage of leading to localizations of the deformation during shaping, resulting in vermiculures. To avoid these vermiculures on standard steel 1.4318 not recrystallized after hot rolling, it is necessary to anneal after hot rolling.
- the object of the invention is therefore to have hot-rolled sheets of austenitic stainless steel with mechanical characteristics greater than or equivalent to those of the grades of the type 1.4318 presented above, which are inexpensive to manufacture, and which have no sensitivity to appearance of vermiculures.
- Another object of the invention is to provide hot-rolled sheets of austenitic stainless steel having a product P greater than 21000 MPa.%, Which can be associated with a yield strength Rpo, 2 greater than 650 MPa, or a distributed elongation greater than 45%.
- the subject of the invention is a hot-rolled sheet of austenitic stainless steel whose product P (Rpo, 2 (MPa) x extended elongation (%)) is greater than 21000 MPa.% And whose chemical composition comprises , the contents being expressed by 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%, the Nb and N contents being such that:
- the niobium and nitrogen contents of the steel are such that: 0.20% ⁇ Nb ⁇ 0.31%, 0.12% ⁇ N ⁇ 0.16%.
- the invention also relates to a hot-rolled sheet made of austenitic stainless steel according to any one of the above compositions, whose yield strength Rp o , 2 is greater than 650 MPa, characterized in that the average size The austenitic grain of the steel is less than 6 microns, the non-recrystallized surface fraction is between 30 and 70%, and the niobium is completely in the form of precipitates.
- the invention also relates to a hot rolled sheet of austenitic stainless steel according to any one of the above characteristics, the distributed elongation of which is greater than 45%, characterized in that the niobium is not totally precipitated. .
- the invention also relates to a method of manufacturing a hot rolled sheet of austenitic stainless steel whose yield strength Rp o , 2 is greater than 650 MPa, according to which a semi-finished steel product is supplied. according to any one of the above compositions, then the semi-finished product is heated to a temperature of between 1250 ° C. and 1320 ° C., and then the semi-finished product is rolled out with a rolling end temperature of less than 990 ° C. and a cumulative reduction rate ⁇ on the last two finishing cages, greater than 30%.
- a semi-finished product of steel containing 0.20% ⁇ Nb ⁇ 0.31%, 0.12% ⁇ N ⁇ 0.16% is supplied, then the half produced with an end-of-lamination temperature below 970 ° C.
- the invention also relates to a method for manufacturing a hot-rolled sheet of austenitic stainless steel, the distributed elongation of which is greater than 45%, according to which a semi-finished product of steel is supplied according to one of any of the above compositions, then the semi-finished product is heated to a temperature between 1250 0 C and 132O 0 C, then the semi-finished product is rolled with a temperature of end of rolling greater than 1000 0 C.
- the invention also relates to a method for manufacturing a hot-rolled sheet of austenitic stainless steel whose product P (Rpo, 2 (MPa) x distributed elongation (%)) is greater than 21000 MPa.%, According to which supplying a semi-finished product of steel according to any one of the above compositions ⁇ and then heating the semi-finished product to a temperature of between 1250 ° C. and 1320 ° C., and the half product.
- Another object of the invention is the use of a stainless steel hot rolled sheet according to any of the above features, or manufactured by any of the above methods, for the manufacture of elements in the automotive field.
- the carbon content must be less than or equal to 0.030% in order to avoid the risk of sensitization to intergranular corrosion. In order to obtain a yield strength greater than 650 MPa, the carbon content must be greater than or equal to 0.015%.
- Manganese like silicon, is an element known for its deoxidative properties in the liquid state and to increase the hot ductility, especially by combining with sulfur. On the other hand, at room temperature, it promotes the stability of the austenitic phase and reduces the stacking fault energy. It also increases the solubility of nitrogen. These favorable effects are obtained economically when the manganese content is between 0.5 and 2%.
- silicon is an element usually added for the purpose of deoxidizing liquid steel. Silicon also increases the yield strength and the resistance, by hardening in solid solution or by its action on the ⁇ ferrite content. However, beyond 2%, the weldability and the hot ductility are reduced.
- Chromium is a well-known element for increasing resistance to oxidation and corrosion in aqueous media. This effect is satisfactorily obtained when its content is between 16.5% and 18%.
- Nickel is an indispensable element to ensure sufficient stability of the austenitic structure of steel at room temperature.
- the optimum content should be determined in relation to other elements of the alphagene composition such as chromium, or those with a gamma-like character such as carbon and nitrogen. Its effect on the stability of the structure is sufficient when its content is greater than or equal to 6%. Above 7%, the cost of production increases excessively because of the high cost of this element of addition.
- Molybdenum increases the resistance to pitting.
- molybdenum addition up to 0.6% can be carried out.
- Boron improves the forgeability of steel.
- boron in an amount between 0.0005 and 0.0025% can be carried out. Addition in greater quantity would critically decrease the burn temperature.
- Sulfur is an element that particularly degrades hot forgeability and corrosion resistance, its content must be maintained less than or equal to 0.015%.
- Phosphorus likewise degrades hot ductility, its content must be less than 0.045% to obtain satisfactory results.
- Aluminum is a powerful deoxidation agent for the liquid metal. In combination with the silicon and manganese contents mentioned above, an optimal effect is obtained when its content is less than or equal to 0.050%.
- Niobium and nitrogen are important elements of the invention for the manufacture of austenitic stainless steels with high mechanical properties.
- Niobium retards recrystallization during hot rolling: for a given hot rolling end temperature, its addition leads to maintain a higher rate of work hardening (it is called hot rolling "hardening"), thus increasing the strength of the steel. It is generally used as Ti to combat the formation of chromium carbides (austenitic stainless steels stabilized with EN 1.4580 and EN 1.4550). Finally, it can lead to intermetallic phase formation conferring an improvement in creep resistance.
- Nitrogen is a hardening element in interstitial solid solution, which particularly increases the yield strength in this respect. It is also known, in solid solution, as a powerful stabilizer of the austenitic phase and as a retarder of the precipitation of Cr 23 C 6 chromium carbides. The solubility of the nitrogen during the solidification knows a maximum. Too high a content leads to the formation of volume defects in the metal. The joint addition of niobium and nitrogen for curing is unusual in austenitic stainless steels.
- stainless steels the composition of which is close to that of the 1.4318 steels mentioned above, advantageously benefit from a particular joint addition of niobium and nitrogen, optimized for to obtain certain mechanical properties under specific conditions that will be exposed:
- the preceding relation (1) ensures that as much solid solution nitrogen remains after complete precipitation of all available niobium as in 1.4318 (N> 0.1%). This makes it possible to obtain the same metastability of the austenite at room temperature.
- the possibility of decreasing the Ni content by increasing the N content is limited by the solubility limit of nitrogen in the steel during solidification.
- the nitrogen content must be less than or equal to 0.16%.
- niobium must be present to achieve a hardening effect and delay recrystallization. This amount must be adapted to obtain a NbN solvus higher than the end of rolling temperature to obtain precipitation at the end of hot rolling.
- niobium and nitrogen make it possible to obtain a high precipitation of NbN after hot rolling.
- the rest of the composition consists of unavoidable impurities resulting from the preparation, such as for example Sn or Pb.
- a steel is produced whose composition has been explained above. This development can be followed by casting in ingots or, in the most general case, continuously, for example in the form of slabs ranging from 150 to 250 mm thick. It is also possible to perform the casting in the form of thin slabs of a few tens of millimeters thick between contra-rotating steel rolls. These cast semifinished products are first brought to a temperature of between 1250 and 1320 ° C. The purpose of the 1250 ° C. temperature is to dissolve any niobium-based precipitates (nitrides, carbonitrides).
- the temperature must be less than 1320 ° C or it may be too close to the solidus temperature that could be reached in any segregated areas and cause a local start to pass through a liquid state that would be harmful for hot shaping.
- the step of hot rolling of these semi-products starting at a temperature below 1250 ° C. can be done directly after casting so that one step intermediate heating is not necessary in this case.
- the rolling is generally carried out on a continuous hot stream comprising in particular roughing cages and finishing cages. It has been demonstrated that a particularly high yield strength Rp o , 2 is obtained by controlling in particular the reduction ratio in the two last finishing stands: if e N- 2 denotes the thickness of the sheet at the entrance of the penultimate finishing cage, and by e N the thickness of the sheet at the exit of the last finishing cage, the cumulative reduction ratio is defined on the two last finishing stands by: ⁇ _ _ j t 2. - N 5 e
- end of rolling temperature is less than 990 ° C. and that the cumulative reduction rate ⁇ is greater than 30%, the yield strength Rpo, 2 of the final product obtained was greater than 650 MPa, the Nb then being totally under form of precipitates.
- this minimum value of 650 MPa is obtained when the end-of-rolling temperature is less than 970 ° C. C and ⁇ greater than 30%.
- Table 1 Composition of steels (percentage by weight)
- the semi-finished steel products were heated at 1280 ° C. for 30 minutes. Hot rolling was then carried out by varying the end-of-rolling temperature between 900 and 1100 ° C. as well as the cumulative reduction ratio ⁇ , to reach a final thickness of 3 mm.
- the sheets 11-1, 11-2, 11-3 ... designate sheets from the same half-product 11, laminated under different conditions.
- the microstructure of the steel obtained was characterized by measuring in particular the recrystallized austenitic phase surface fraction, the fraction of niobium precipitated relative to the total niobium, and the average grain size. In the case of a structure not completely recrystallized, the latter measurement is performed on the recrystallized part of the structure.
- the mechanical tensile characteristics in particular the yield strength Rpo, 2 and the distributed elongation were also determined.
- the presence of a localization of the deformation during the tensile test has also been noted. It is known that the presence of such a location is associated with the appearance of vermiculides during shaping operations.
- hot-rolled steel sheets according to the invention will be advantageously used for applications requiring good shaping and a high resistance to corrosion.
- their advantages will be exploited for the economic manufacture of structural elements.
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
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP20090722337 EP2257652B1 (fr) | 2008-03-21 | 2009-03-03 | Procede de fabrication de tôles d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenues |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP08290267A EP2103705A1 (fr) | 2008-03-21 | 2008-03-21 | Procédé de fabrication de tôles d'acier inoxydable austenitique à hautes caractèristiques mécaniques |
PCT/FR2009/000225 WO2009115702A2 (fr) | 2008-03-21 | 2009-03-03 | Procede de fabrication de t^les d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenues |
EP20090722337 EP2257652B1 (fr) | 2008-03-21 | 2009-03-03 | Procede de fabrication de tôles d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenues |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2257652A2 true EP2257652A2 (fr) | 2010-12-08 |
EP2257652B1 EP2257652B1 (fr) | 2015-04-29 |
Family
ID=39642753
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08290267A Withdrawn EP2103705A1 (fr) | 2008-03-21 | 2008-03-21 | Procédé de fabrication de tôles d'acier inoxydable austenitique à hautes caractèristiques mécaniques |
EP20090722337 Active EP2257652B1 (fr) | 2008-03-21 | 2009-03-03 | Procede de fabrication de tôles d'acier inoxydable austenitique a hautes caracteristiques mecaniques, et tôles ainsi obtenues |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08290267A Withdrawn EP2103705A1 (fr) | 2008-03-21 | 2008-03-21 | Procédé de fabrication de tôles d'acier inoxydable austenitique à hautes caractèristiques mécaniques |
Country Status (10)
Country | Link |
---|---|
US (1) | US20110061776A1 (fr) |
EP (2) | EP2103705A1 (fr) |
JP (1) | JP2011528751A (fr) |
KR (1) | KR20100124774A (fr) |
CN (1) | CN101965416A (fr) |
BR (1) | BRPI0908996B1 (fr) |
CA (1) | CA2714218C (fr) |
ES (1) | ES2543356T3 (fr) |
TW (1) | TWI405858B (fr) |
WO (1) | WO2009115702A2 (fr) |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112609126A (zh) * | 2020-11-13 | 2021-04-06 | 宁波宝新不锈钢有限公司 | 一种核电设备用奥氏体不锈钢及其制备方法 |
CN113430455B (zh) * | 2021-05-31 | 2022-05-17 | 中国科学院金属研究所 | 一种耐液态铅铋腐蚀的高强度奥氏体不锈钢及其制备方法 |
CN114934240B (zh) * | 2022-04-25 | 2023-10-10 | 中国科学院金属研究所 | 一种超高强高耐蚀高氮奥氏体不锈钢的制备方法 |
CN115537672B (zh) * | 2022-07-19 | 2023-08-18 | 燕山大学 | 一种屈服强度大于1000 MPa的低成本奥氏体钢及其温轧制备工艺 |
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US3284250A (en) * | 1964-01-09 | 1966-11-08 | Int Nickel Co | Austenitic stainless steel and process therefor |
JPS5915979B2 (ja) * | 1980-07-03 | 1984-04-12 | 新日本製鐵株式会社 | 熱間圧延において圧延による疵発生の少ないステンレス合金 |
JPS6053726B2 (ja) * | 1981-07-31 | 1985-11-27 | 新日本製鐵株式会社 | オ−ステナイト系ステンレス鋼板及び鋼帯の製造方法 |
DE3407307A1 (de) * | 1984-02-24 | 1985-08-29 | Mannesmann AG, 4000 Düsseldorf | Verwendung einer korrosionsbestaendigen austenitischen eisen-chrom-nickel-stickstoff-legierung fuer mechanisch hoch beanspruchte bauteile |
JPS60208459A (ja) * | 1984-03-30 | 1985-10-21 | Aichi Steel Works Ltd | 高強度ステンレス鋼およびその製造法 |
JP2602015B2 (ja) * | 1986-08-30 | 1997-04-23 | 愛知製鋼株式会社 | 耐腐食疲労性、耐海水性に優れたステンレス鋼およびその製造方法 |
JPH06306464A (ja) * | 1993-04-28 | 1994-11-01 | Nippon Steel Corp | オーステナイト系ステンレス鋼熱延板の製造方法 |
JPH0860244A (ja) * | 1994-08-23 | 1996-03-05 | Nippon Steel Corp | オーステナイト系ステンレス厚鋼板の製造方法 |
JPH0987809A (ja) * | 1995-09-27 | 1997-03-31 | Kawasaki Steel Corp | 自動車排気系材料用Cr含有オーステナイト系熱延鋼板 |
JP4190617B2 (ja) * | 1998-06-23 | 2008-12-03 | 大平洋金属株式会社 | ステンレス鋼の熱間圧延板を製造する方法 |
KR100356930B1 (ko) * | 1998-09-04 | 2002-10-18 | 스미토모 긴조쿠 고교 가부시키가이샤 | 엔진 가스킷용 스테인레스강과 그 제조방법 |
JP3449282B2 (ja) * | 1999-03-04 | 2003-09-22 | 住友金属工業株式会社 | 高温強度と延性に優れたオーステナイト系ステンレス鋼 |
JP2001181734A (ja) * | 1999-12-24 | 2001-07-03 | Kawasaki Steel Corp | スケール密着性に優れたCr含有熱延鋼板の製造方法 |
JP3603726B2 (ja) * | 2000-03-03 | 2004-12-22 | 住友金属工業株式会社 | 電子機器部品用オーステナイト系ステンレス鋼板 |
JP2002194506A (ja) * | 2000-12-25 | 2002-07-10 | Sumitomo Metal Ind Ltd | ステンレス鋼板およびその製造方法 |
JP4321066B2 (ja) * | 2001-04-27 | 2009-08-26 | 住友金属工業株式会社 | 金属ガスケットとその素材およびそれらの製造方法 |
FR2864108B1 (fr) * | 2003-12-22 | 2006-01-27 | Ugine Et Alz France | Tole en acier inoxydable presentant une grande resistance et un bon allongement, et procede de fabrication |
JP4813123B2 (ja) * | 2005-08-10 | 2011-11-09 | 新日鐵住金ステンレス株式会社 | 表面品質に優れたオーステナイト系ステンレス鋼板の製造方法 |
-
2008
- 2008-03-21 EP EP08290267A patent/EP2103705A1/fr not_active Withdrawn
-
2009
- 2009-03-03 JP JP2011500247A patent/JP2011528751A/ja active Pending
- 2009-03-03 US US12/922,786 patent/US20110061776A1/en not_active Abandoned
- 2009-03-03 ES ES09722337.4T patent/ES2543356T3/es active Active
- 2009-03-03 CN CN2009801073261A patent/CN101965416A/zh active Pending
- 2009-03-03 WO PCT/FR2009/000225 patent/WO2009115702A2/fr active Application Filing
- 2009-03-03 EP EP20090722337 patent/EP2257652B1/fr active Active
- 2009-03-03 BR BRPI0908996-9A patent/BRPI0908996B1/pt active IP Right Grant
- 2009-03-03 KR KR1020107020786A patent/KR20100124774A/ko not_active Application Discontinuation
- 2009-03-03 CA CA2714218A patent/CA2714218C/fr active Active
- 2009-03-09 TW TW098107530A patent/TWI405858B/zh active
Non-Patent Citations (1)
Title |
---|
See references of WO2009115702A2 * |
Also Published As
Publication number | Publication date |
---|---|
EP2257652B1 (fr) | 2015-04-29 |
TWI405858B (zh) | 2013-08-21 |
BRPI0908996A2 (pt) | 2019-03-06 |
WO2009115702A3 (fr) | 2009-11-12 |
US20110061776A1 (en) | 2011-03-17 |
CN101965416A (zh) | 2011-02-02 |
JP2011528751A (ja) | 2011-11-24 |
KR20100124774A (ko) | 2010-11-29 |
BRPI0908996B1 (pt) | 2019-07-09 |
WO2009115702A2 (fr) | 2009-09-24 |
TW200951233A (en) | 2009-12-16 |
ES2543356T3 (es) | 2015-08-18 |
CA2714218A1 (fr) | 2009-09-24 |
EP2103705A1 (fr) | 2009-09-23 |
CA2714218C (fr) | 2013-09-24 |
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