EP2890825A1 - Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability - Google Patents
Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formabilityInfo
- Publication number
- EP2890825A1 EP2890825A1 EP13759947.8A EP13759947A EP2890825A1 EP 2890825 A1 EP2890825 A1 EP 2890825A1 EP 13759947 A EP13759947 A EP 13759947A EP 2890825 A1 EP2890825 A1 EP 2890825A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- ferritic stainless
- stainless steel
- oxidation resistance
- less
- titanium
- 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
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 40
- 230000003647 oxidation Effects 0.000 title abstract description 17
- 238000007254 oxidation reaction Methods 0.000 title abstract description 17
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 239000011572 manganese Substances 0.000 claims abstract description 11
- 239000010955 niobium Substances 0.000 claims abstract description 11
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 10
- 239000010703 silicon Substances 0.000 claims abstract description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 239000010949 copper Substances 0.000 claims abstract description 8
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 38
- 239000010936 titanium Substances 0.000 claims description 27
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 26
- 229910052719 titanium Inorganic materials 0.000 claims description 25
- 229910052757 nitrogen Inorganic materials 0.000 claims description 19
- 229910052782 aluminium Inorganic materials 0.000 claims description 18
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 17
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 8
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 6
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 239000011651 chromium Substances 0.000 claims description 3
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 239000011574 phosphorus Substances 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 claims description 2
- 239000011593 sulfur Substances 0.000 claims description 2
- 229910006639 Si—Mn Inorganic materials 0.000 abstract description 2
- 229910052758 niobium Inorganic materials 0.000 abstract 1
- 239000000155 melt Substances 0.000 description 25
- 229910000831 Steel Inorganic materials 0.000 description 19
- 239000010959 steel Substances 0.000 description 19
- 238000000034 method Methods 0.000 description 11
- 239000000203 mixture Substances 0.000 description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 238000000137 annealing Methods 0.000 description 9
- 238000005266 casting Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- 238000005261 decarburization Methods 0.000 description 7
- 238000007670 refining Methods 0.000 description 6
- VVTSZOCINPYFDP-UHFFFAOYSA-N [O].[Ar] Chemical compound [O].[Ar] VVTSZOCINPYFDP-UHFFFAOYSA-N 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 239000010935 stainless steel Substances 0.000 description 5
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 4
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 229910052742 iron Inorganic materials 0.000 description 4
- 230000006641 stabilisation Effects 0.000 description 4
- 238000011105 stabilization Methods 0.000 description 4
- 230000000087 stabilizing effect Effects 0.000 description 4
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 238000007792 addition Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000004901 spalling Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 2
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 2
- 239000001166 ammonium sulphate Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000010891 electric arc Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000005272 metallurgy Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 230000004584 weight gain Effects 0.000 description 2
- 235000019786 weight gain Nutrition 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000003466 anti-cipated effect Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- -1 e.g. Chemical compound 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 1
- 235000013980 iron oxide Nutrition 0.000 description 1
- VBMVTYDPPZVILR-UHFFFAOYSA-N iron(2+);oxygen(2-) Chemical class [O-2].[Fe+2] VBMVTYDPPZVILR-UHFFFAOYSA-N 0.000 description 1
- 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 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000161 steel melt Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 150000003609 titanium compounds Chemical class 0.000 description 1
- 238000011144 upstream manufacturing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- 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
- C21D8/0226—Hot rolling
-
- 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
- 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
- C21D8/0236—Cold rolling
-
- 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
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- 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
- C21D8/0273—Final recrystallisation annealing
Definitions
- ferritic stainless steel with oxidation resistance, high temperature strength, and good formability characteristics. Columbium and copper are added in amounts to provide high temperature strength, and silicon and manganese are added in amounts to provide oxidation resistance.
- the present ferritic stainless steel provides better oxidation resistance than known stainless steels such as 18Cr-2Mo and 15Cr-Cb-Ti-Si-Mn. In addition, the present ferritic stainless steel is less expensive to manufacture than other stainless steels such as 18Cr-2Mo and can be produced without a hot band annealing step.
- the present ferritic stainless steel are produced with titanium additions and low aluminum concentration to provide room temperature formability from equiaxed as-cast grain structures, as disclosed in U.S. Patent Nos. 6,855,213 and 5,868,875, the complete disclosures of which are each incorporated by reference herein.
- Columbium and copper are added to the ferritic stainless steel for high temperature strength and silicon and manganese are added to improve oxidation resistance.
- the ferritic stainless steel is produced using process conditions known in the art for use in manufacturing ferritic stainless steels, such as the processes described in U.S. Patent Nos. 6,855,213 and 5,868,875. Columbium and copper are added to the ferritic stainless steel for high temperature strength and silicon and manganese are added to improve oxidation resistance. It can be produced from material having an as-cast structure of fine equiaxed grains.
- a ferrous melt for the ferritic stainless steel is provided in a melting furnace such as an electric arc furnace.
- This ferrous melt may be formed in the melting furnace from solid iron bearing scrap, carbon steel scrap, stainless steel scrap, solid iron containing materials including iron oxides, iron carbide, direct reduced iron, hot briquetted iron, or the melt may be produced upstream of the melting furnace in a blast furnace or any other iron smelting unit capable of providing a ferrous melt.
- the ferrous melt then will be refined in the melting furnace or transferred to a refining vessel such as an argon-oxygen-decarburization vessel or a vacuum- oxygen-decarburization vessel, followed by a trim station such as a ladle metallurgy furnace or a wire feed station.
- the steel is cast from a melt containing sufficient titanium and nitrogen but a controlled amount of aluminum for forming small titanium oxide inclusions to provide the necessary nuclei for forming the as-cast equiaxed grain structure so that an annealed sheet produced from this steel also has enhanced ridging characteristics and formability.
- titanium is added to the melt for deoxidation prior to
- titanium oxide inclusions that provide the nuclei that result in an as-cast equiaxed fine grain structure.
- aluminum oxide A1 2 0 3; in some embodiments aluminum may not be added to this refined melt as a deoxidant and in other embodiments aluminum may be added to this refined melt in a small fraction.
- titanium and nitrogen can be present in the melt prior to casting so that the ratio of the product of titanium and nitrogen divided by residual aluminum is at least about 0.14.
- titanium nitride inclusions before solidification.
- the maximum amount of titanium for "sub-equilibrium" is generally illustrated in FIG. 4 of U.S. Pat. No. 4,964,926, the disclosure of which is incorporated herein by reference.
- one or more stabilizing elements such as columbium, zirconium, tantalum and vanadium can be added to the melt as well.
- the cast steel is hot processed into a sheet.
- sheet is meant to include continuous strip or cut lengths formed from continuous strip and the term “hot processed” means the as-cast steel will be reheated, if necessary, and then reduced to a predetermined thickness such as by hot rolling. If hot rolled, a steel slab is reheated to 2000° to 2350°F (1093°-1288°C), hot rolled using a finishing temperature of 1500 - 1800°F (816 - 982°C) and coiled at a temperature of 1000 - 1400°F (538 - 760°C).
- the hot rolled sheet is also known as the "hot band.”
- the hot band may be annealed at a peak metal temperature of 1700 - 2100°F (926 - 1149°C). In other embodiments, the sheet does not undergo a hot band annealing step.
- the hot band may be descaled and cold reduced at least 40% to a desired final sheet thickness. In other embodiments, the hot band may be descaled and cold reduced at least 50% to a desired final sheet thickness. Thereafter, the cold reduced sheet can be final annealed at a peak metal temperature of 1800 - 2100°F (982-1149°C).
- the ferritic stainless steel can be produced from a hot processed sheet made by a number of methods.
- the sheet can be produced from slabs formed from ingots or continuous cast slabs of 50-200 mm thickness which are reheated to 2000° to 2350°F (1093°-1288°C) followed by hot rolling to provide a starting hot processed sheet of 1 - 7 mm thickness or the sheet can be hot processed from strip continuously cast into thicknesses of 2 - 52 mm.
- the present process is
- Titanium is used for deoxidation of the ferritic stainless steel melt prior to casting.
- the amount of titanium in the melt can be 0.30% or less. Unless otherwise expressly stated, all concentrations stated as “%" are percent by weight. In some embodiments, titanium can be present in a sub-equilibrium amount. As used herein, the term "sub-equilibrium” means the amount of titanium is controlled so that the solubility product of the titanium compounds formed are below the saturation level at the steel liquidus temperature thereby avoiding excessive titanium nitride precipitation in the melt. Excessive nitrogen is not a problem for those manufacturers that refine ferritic stainless steel melts in an argon oxygen decarburization vessel. Nitrogen substantially below 0.010% can be obtained when refining the stainless steel in an argon oxygen decarburization vessel thereby allowing increased amount of titanium to be tolerated and still be at sub- equilibrium.
- Sufficient nitrogen should be present in the steel prior to casting so that the ratio of the product of titanium and nitrogen divided by aluminum is at least about 0.14. In some embodiments, the amount of nitrogen present in the melt is ⁇
- nitrogen concentrations after melting in an electric arc furnace may be as high as 0.05%, the amount of dissolved N can be reduced during argon gas refining in an argon oxygen decarburization vessel to less than 0.02%.
- Precipitation of excessive TIN can be avoided by reducing the sub-equilibrium amount of Ti to be added to the melt for any given nitrogen content.
- the amount of nitrogen in the melt can be reduced in an argon oxygen decarburization vessel for an anticipated amount of Ti contained in the melt.
- Total residual aluminum can be controlled or minimized relative to the amounts of titanium and nitrogen.
- Minimum amounts of titanium and nitrogen must be present in the melt relative to the aluminum.
- the ratio of the product of titanium and nitrogen divided by residual aluminum can be at least about 0.14 in some embodiments, and at least 0.23 in other embodiments.
- the amount of aluminum is ⁇ 0.020% in some embodiments. In other embodiments, the amount of aluminum is ⁇ 0.013% and in other embodiments, it is reduced to ⁇ 0.010%. If aluminum is not purposefully alloyed with the melt during refining or casting such as for deoxidation immediately prior to casting, total aluminum can be controlled or reduced to less than 0.020%).
- Titanium alloys may contain as much as 20% Al which may contribute total Al to the melt.
- stabilizing elements may also include columbium, zirconium, tantalum, vanadium or mixtures thereof.
- this second stabilizing element may be limited to ⁇ 0.50% when deep formability is required.
- Some embodiments include columbium in concentrations of 0.5% or less.
- Some embodiments include columbium in concentrations of 0.28 - 0.43%.
- Vanadium can be present in amounts less than 0.5%.
- Some embodiments of the ferritic stainless steels include 0.008 - 0.098% vanadium.
- Some embodiments include 1.16-1.31% copper.
- Silicon is generally present in the ferritic stainless steels in an amount of 1.0 -
- silicon is present in an amount of 1.27 - 1.35%.
- a small amount of silicon generally is present in a ferritic stainless steel to promote formation of the ferrite phase. Silicon also enhances high temperature oxidation resistance and provides high temperature strength. In most embodiments, silicon does not exceed about 1.7% because the steel can become too hard and the elongation can be adversely affected.
- Manganese is present in the ferritic stainless steel in an amount of 0.4 - 1.5%. In some embodiments, manganese is present in an amount of 0.97 - 1.00%.
- Manganese improves oxidation resistance and spalling resistance at high temperatures. Accordingly, some embodiments include manganese in amounts of at least 0.4%. However, manganese is an austenite former and affects the stabilization of the ferrite phase. If the amount of manganese exceeds about 1.5%, the stabilization and formability of the steel can be affected.
- Carbon is present in the ferritic stainless steel in an amount of up to 0.02%. In some embodiments, the carbon content is ⁇ 0.02%. In still other embodiments, it is 0.0054-0.0133%.
- Chromium is present in some embodiments of the ferritic stainless steels in an amount of 15-20%). If chromium is greater than about 25%, the formability of the steel can be reduced.
- oxygen is present in the steel in an amount ⁇ 100 ppm.
- oxygen in the melt can be within the range of 10-60 ppm thereby providing a very clean steel having small titanium oxide inclusions that aid in forming the nucleation sites responsible for the fine as-cast equiaxed grain structure.
- Sulfur is present in the femtic stainless steel in an amount of ⁇ 0.01%.
- Phosphorus can deteriorate formability in hot rolling and can cause pitting. It is present in the ferritic stainless steel in an amount of ⁇ 0.05%.
- nickel is an austenite former and affects the stabilization of the ferrite phase. Accordingly, in some embodiments, nickel is limited to ⁇ 1.0%. In some embodiments, nickel is present in amounts of 0.13- 0.19%.
- Molybdenum also improves corrosion resistance. Some embodiments include
- molybdenum 3.0% or less molybdenum. Some embodiments include 0.03 - 0.049%) molybdenum.
- boron in the steels of the present invention in an amount of ⁇ 0.010%. In some embodiments, boron is present in an amount of 0.0001 - 0.002%). Boron can improve the resistance to secondary work embrittlement of steel so that the steel sheet will be less likely to split during deep drawing applications and multi-step forming applications.
- the ferritic stainless steels may also include other elements known in the art of steelmaking that can be made either as deliberate additions or present as residual elements, i.e., impurities from steelmaking process.
- each ingot was reheated to a temperature of 2300°F (1260°C). It was hot rolled to a strip thickness of 0.200" (5.08 mm). It was then hot band annealed at a temperature of 1825-1975°C (996 - 1079°C). It was then cold rolled to a thickness of 0.079 - 0.098" (2.0 - 2.5mm). The cold rolled strip was final annealed to a temperature of 1885 - 1950°F (1029 1066°C).
- HT #831187 is Type 444 stainless steel
- HT #830843 is 15 CrCb stainless steel, which is a product of AK Steel Corporation, West Chester, Ohio.
- Example 1 were tested according to the procedure of ASTM Standard E8/E8M test. In addition, the stretch-r values were tested according to the procedure of ASTM Standard E517. Ridging resistance of the compositions was also determined on a qualitative scale of 0-6, where 0 is the best and 6 is unacceptable. The results of these tests are set forth below:
- HT #930354 One plant produced hot band coil with the composition set forth in Table 1 (HT #930354, CL #681 158-03) was finish-processed without hot band annealing to 1.5 mm gauge.
- a hot band annealing step was included, the plant-produced coils of HT#930354 resulted in r-bar values of 1.34, 1.31, 1.38, and 1.34, as shown in Table 5.
- the hot band annealing step was not included, it resulted in higher r- bar of 1.46, as shown by Table 7 below.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PL13759947T PL2890825T3 (en) | 2012-08-31 | 2013-08-28 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
SI201331448T SI2890825T1 (en) | 2012-08-31 | 2013-08-28 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
RS20190532A RS58807B1 (en) | 2012-08-31 | 2013-08-28 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
HRP20190864TT HRP20190864T1 (en) | 2012-08-31 | 2019-05-09 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US201261695771P | 2012-08-31 | 2012-08-31 | |
US13/837,500 US20140065005A1 (en) | 2012-08-31 | 2013-03-15 | Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability |
PCT/US2013/056999 WO2014036091A1 (en) | 2012-08-31 | 2013-08-28 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2890825A1 true EP2890825A1 (en) | 2015-07-08 |
EP2890825B1 EP2890825B1 (en) | 2019-04-03 |
Family
ID=49151344
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP13759947.8A Active EP2890825B1 (en) | 2012-08-31 | 2013-08-28 | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability |
Country Status (19)
Country | Link |
---|---|
US (2) | US20140065005A1 (en) |
EP (1) | EP2890825B1 (en) |
JP (1) | JP6194956B2 (en) |
KR (2) | KR20200028502A (en) |
CN (2) | CN108823509A (en) |
AU (1) | AU2013308922B2 (en) |
BR (1) | BR112015004228A2 (en) |
CA (1) | CA2882361C (en) |
ES (1) | ES2728229T3 (en) |
HR (1) | HRP20190864T1 (en) |
HU (1) | HUE043997T2 (en) |
MX (1) | MX2015002677A (en) |
MY (1) | MY172722A (en) |
PL (1) | PL2890825T3 (en) |
RS (1) | RS58807B1 (en) |
RU (1) | RU2650467C2 (en) |
SI (1) | SI2890825T1 (en) |
WO (1) | WO2014036091A1 (en) |
ZA (1) | ZA201502075B (en) |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20140065005A1 (en) * | 2012-08-31 | 2014-03-06 | Eizo Yoshitake | Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability |
EP3333277B1 (en) | 2015-08-05 | 2019-04-24 | Sidenor Investigación y Desarrollo, S.A. | High-strength low-alloy steel with high resistance to high-temperature oxidation |
CN107675075A (en) * | 2017-09-05 | 2018-02-09 | 王业双 | A kind of high-performance high temperature resistant ferritic stainless steel and preparation method thereof |
JP6420893B1 (en) * | 2017-12-26 | 2018-11-07 | 日新製鋼株式会社 | Ferritic stainless steel |
JP2023507264A (en) * | 2019-12-18 | 2023-02-22 | エリコン メテコ(ユーエス)インコーポレイテッド | Iron-based high corrosion resistance and wear resistance alloy |
Family Cites Families (21)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CA899A (en) * | 1871-03-24 | D. Cameron | Composition of matter for making fire brick, and in the art of burning the same | |
JPH01165752A (en) * | 1987-12-22 | 1989-06-29 | Kawasaki Steel Corp | Ferritic stainless steel having superior corrosion resistance in highly concentrated halide solution |
JPH02115346A (en) * | 1988-10-21 | 1990-04-27 | Kawasaki Steel Corp | Ferritic stainless steel having excellent corrosion resistance in high concentrated halide |
US5426039A (en) * | 1993-09-08 | 1995-06-20 | Bio-Rad Laboratories, Inc. | Direct molecular cloning of primer extended DNA containing an alkane diol |
FR2720410B1 (en) * | 1994-05-31 | 1996-06-28 | Ugine Savoie Sa | Ferritic stainless steel with improved machinability. |
JP3439866B2 (en) * | 1995-03-08 | 2003-08-25 | 日本冶金工業株式会社 | Ferritic stainless steel with excellent corrosion resistance and weldability |
US6426039B2 (en) * | 2000-07-04 | 2002-07-30 | Kawasaki Steel Corporation | Ferritic stainless steel |
JP3886785B2 (en) * | 2001-11-22 | 2007-02-28 | 日新製鋼株式会社 | Ferritic stainless steel for petroleum fuel reformers |
JP3942876B2 (en) * | 2001-11-22 | 2007-07-11 | 日新製鋼株式会社 | Ferritic stainless steel for hydrocarbon fuel reformer |
JP3989790B2 (en) * | 2002-07-30 | 2007-10-10 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet with excellent press formability and manufacturing method thereof |
JP3920185B2 (en) * | 2002-09-27 | 2007-05-30 | 日新製鋼株式会社 | Stainless steel tire rim material and motorcycle frame material with excellent flexibility |
JP4463663B2 (en) * | 2004-11-04 | 2010-05-19 | 日新製鋼株式会社 | Ferritic steel material excellent in high temperature steam oxidation resistance and method of use thereof |
US7732733B2 (en) * | 2005-01-26 | 2010-06-08 | Nippon Welding Rod Co., Ltd. | Ferritic stainless steel welding wire and manufacturing method thereof |
JP5236158B2 (en) * | 2005-01-26 | 2013-07-17 | 日本ウエルディング・ロッド株式会社 | Ferritic stainless steel welding wire and manufacturing method thereof |
JP4302678B2 (en) * | 2005-09-01 | 2009-07-29 | 日新製鋼株式会社 | Ferritic stainless steel sheet for fuel tanks |
JP4761993B2 (en) * | 2006-02-14 | 2011-08-31 | 日新製鋼株式会社 | Manufacturing method of ferritic stainless steel welded pipe for spinning |
JP4948998B2 (en) * | 2006-12-07 | 2012-06-06 | 日新製鋼株式会社 | Ferritic stainless steel and welded steel pipe for automotive exhaust gas flow path members |
JP5349153B2 (en) * | 2009-06-15 | 2013-11-20 | 日新製鋼株式会社 | Ferritic stainless steel for brazing and heat exchanger members |
RU2415963C2 (en) * | 2009-07-13 | 2011-04-10 | Открытое акционерное общество "Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения", ОАО НПО "ЦНИИТМАШ" | Heat resistant steel |
KR20180017220A (en) * | 2010-09-16 | 2018-02-20 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Heat-resistant ferrite-type stainless steel plate having excellent oxidation resistance |
US20140065005A1 (en) * | 2012-08-31 | 2014-03-06 | Eizo Yoshitake | Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability |
-
2013
- 2013-03-15 US US13/837,500 patent/US20140065005A1/en not_active Abandoned
- 2013-08-27 US US14/010,646 patent/US20140065006A1/en not_active Abandoned
- 2013-08-28 RS RS20190532A patent/RS58807B1/en unknown
- 2013-08-28 PL PL13759947T patent/PL2890825T3/en unknown
- 2013-08-28 KR KR1020207006567A patent/KR20200028502A/en not_active IP Right Cessation
- 2013-08-28 MY MYPI2015000506A patent/MY172722A/en unknown
- 2013-08-28 AU AU2013308922A patent/AU2013308922B2/en not_active Ceased
- 2013-08-28 SI SI201331448T patent/SI2890825T1/en unknown
- 2013-08-28 RU RU2015108849A patent/RU2650467C2/en not_active IP Right Cessation
- 2013-08-28 CA CA2882361A patent/CA2882361C/en active Active
- 2013-08-28 ES ES13759947T patent/ES2728229T3/en active Active
- 2013-08-28 BR BR112015004228A patent/BR112015004228A2/en not_active Application Discontinuation
- 2013-08-28 WO PCT/US2013/056999 patent/WO2014036091A1/en active Application Filing
- 2013-08-28 EP EP13759947.8A patent/EP2890825B1/en active Active
- 2013-08-28 MX MX2015002677A patent/MX2015002677A/en active IP Right Grant
- 2013-08-28 CN CN201810791340.9A patent/CN108823509A/en active Pending
- 2013-08-28 JP JP2015529983A patent/JP6194956B2/en active Active
- 2013-08-28 KR KR1020157008118A patent/KR20150080485A/en active Search and Examination
- 2013-08-28 CN CN201380045477.5A patent/CN104769147A/en active Pending
- 2013-08-28 HU HUE13759947A patent/HUE043997T2/en unknown
-
2015
- 2015-03-26 ZA ZA2015/02075A patent/ZA201502075B/en unknown
-
2019
- 2019-05-09 HR HRP20190864TT patent/HRP20190864T1/en unknown
Non-Patent Citations (1)
Title |
---|
See references of WO2014036091A1 * |
Also Published As
Publication number | Publication date |
---|---|
ZA201502075B (en) | 2016-03-30 |
US20140065005A1 (en) | 2014-03-06 |
KR20150080485A (en) | 2015-07-09 |
US20140065006A1 (en) | 2014-03-06 |
JP2015532684A (en) | 2015-11-12 |
EP2890825B1 (en) | 2019-04-03 |
AU2013308922B2 (en) | 2016-08-04 |
KR20200028502A (en) | 2020-03-16 |
CN104769147A8 (en) | 2018-10-09 |
RS58807B1 (en) | 2019-07-31 |
CA2882361A1 (en) | 2014-03-06 |
AU2013308922A1 (en) | 2015-03-05 |
ES2728229T3 (en) | 2019-10-23 |
HRP20190864T1 (en) | 2019-06-28 |
PL2890825T3 (en) | 2019-09-30 |
CN104769147A (en) | 2015-07-08 |
CA2882361C (en) | 2019-06-18 |
RU2015108849A (en) | 2016-10-20 |
MX2015002677A (en) | 2015-05-12 |
HUE043997T2 (en) | 2019-09-30 |
WO2014036091A1 (en) | 2014-03-06 |
MY172722A (en) | 2019-12-11 |
RU2650467C2 (en) | 2018-04-13 |
JP6194956B2 (en) | 2017-09-13 |
BR112015004228A2 (en) | 2017-07-04 |
CN108823509A (en) | 2018-11-16 |
SI2890825T1 (en) | 2019-06-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
TWI404808B (en) | Boron steel sheet with high quenching property and manufacturing method thereof | |
CN107208212B (en) | Thick-walled high-toughness high-strength steel plate and method for producing same | |
WO2015012357A1 (en) | High-strength steel material for oil well use, and oil well pipe | |
AU2013308922B2 (en) | Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability | |
TW201333223A (en) | Duplex stainless steel, duplex stainless steel slab, and duplex stainless steel material | |
JP5362582B2 (en) | Ferritic stainless steel with excellent corrosion resistance and stretch formability and method for producing the same | |
JP6842257B2 (en) | Fe-Ni-Cr-Mo alloy and its manufacturing method | |
CN111433381B (en) | High Mn steel and method for producing same | |
JP6682988B2 (en) | High-tensile steel plate with excellent ductility and method of manufacturing the same | |
CN113412337A (en) | High Mn steel and method for producing same | |
AU2013243635B2 (en) | Cost-effective ferritic stainless steel | |
AU9722598A (en) | Non-ridging ferritic chromium alloyed steel | |
JP5329632B2 (en) | Duplex stainless steel, duplex stainless steel cast, and duplex stainless steel | |
WO2020196595A1 (en) | Steel rod | |
WO2022145061A1 (en) | Steel material | |
JP6776469B1 (en) | Duplex stainless steel and its manufacturing method | |
US20230287549A1 (en) | Austenitic stainless steel with improved deep drawing | |
JPWO2021045212A1 (en) | Directional electromagnetic steel plate and its manufacturing method | |
KR20190077672A (en) | Ferritic stainless steel excellent in ridging property | |
JPH05156352A (en) | Method for controlling composition of nonmetallic inclusion in steel | |
JPH07242938A (en) | Production of hot rolled steel sheet excellent in workability |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20150326 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
DAX | Request for extension of the european patent (deleted) | ||
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 38/28 20060101ALI20180919BHEP Ipc: C22C 38/50 20060101ALI20180919BHEP Ipc: C22C 38/26 20060101ALI20180919BHEP Ipc: C22C 38/00 20060101ALI20180919BHEP Ipc: C21D 8/02 20060101ALI20180919BHEP Ipc: C22C 38/04 20060101ALI20180919BHEP Ipc: C21D 6/00 20060101ALI20180919BHEP Ipc: C22C 38/02 20060101AFI20180919BHEP Ipc: C22C 38/46 20060101ALI20180919BHEP Ipc: C22C 38/44 20060101ALI20180919BHEP Ipc: C22C 38/48 20060101ALI20180919BHEP Ipc: C22C 38/54 20060101ALI20180919BHEP Ipc: C22C 38/20 20060101ALI20180919BHEP Ipc: C22C 38/42 20060101ALI20180919BHEP Ipc: C22C 38/24 20060101ALI20180919BHEP Ipc: C22C 38/06 20060101ALI20180919BHEP |
|
INTG | Intention to grant announced |
Effective date: 20181010 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 602013053324 Country of ref document: DE Representative=s name: SAMSON & PARTNER PATENTANWAELTE MBB, DE |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP Ref country code: AT Ref legal event code: REF Ref document number: 1115819 Country of ref document: AT Kind code of ref document: T Effective date: 20190415 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602013053324 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: TUEP Ref document number: P20190864 Country of ref document: HR |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: RO Ref legal event code: EPE |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: T1PR Ref document number: P20190864 Country of ref document: HR |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 1115819 Country of ref document: AT Kind code of ref document: T Effective date: 20190403 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: HU Ref legal event code: AG4A Ref document number: E043997 Country of ref document: HU |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2728229 Country of ref document: ES Kind code of ref document: T3 Effective date: 20191023 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190703 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190803 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190704 Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190703 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190803 Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602013053324 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: PBON Ref document number: P20190864 Country of ref document: HR Effective date: 20190828 |
|
26N | No opposition filed |
Effective date: 20200106 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RO Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190403 Ref country code: HU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190829 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190831 Ref country code: RS Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200304 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190828 Ref country code: CZ Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190828 Ref country code: HR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190828 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190831 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20190831 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190828 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190829 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190831 |
|
REG | Reference to a national code |
Ref country code: SI Ref legal event code: KO00 Effective date: 20200722 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FI Payment date: 20200827 Year of fee payment: 8 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190403 |
|
REG | Reference to a national code |
Ref country code: FI Ref legal event code: MAE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210828 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PL Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20190828 |
|
P01 | Opt-out of the competence of the unified patent court (upc) registered |
Effective date: 20230527 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20230822 Year of fee payment: 11 Ref country code: GB Payment date: 20230828 Year of fee payment: 11 Ref country code: ES Payment date: 20230901 Year of fee payment: 11 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 20230827 Year of fee payment: 11 Ref country code: FR Payment date: 20230825 Year of fee payment: 11 Ref country code: DE Payment date: 20230829 Year of fee payment: 11 |