WO2017052005A1 - 페라이트계 스테인리스강 및 이의 제조 방법 - Google Patents
페라이트계 스테인리스강 및 이의 제조 방법 Download PDFInfo
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- WO2017052005A1 WO2017052005A1 PCT/KR2016/001638 KR2016001638W WO2017052005A1 WO 2017052005 A1 WO2017052005 A1 WO 2017052005A1 KR 2016001638 W KR2016001638 W KR 2016001638W WO 2017052005 A1 WO2017052005 A1 WO 2017052005A1
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- Prior art keywords
- stainless steel
- niobium
- ferritic stainless
- less
- nitrogen
- Prior art date
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 79
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 238000005096 rolling process Methods 0.000 claims abstract description 40
- 239000010955 niobium Substances 0.000 claims description 148
- 239000002244 precipitate Substances 0.000 claims description 83
- 229910052758 niobium Inorganic materials 0.000 claims description 71
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 68
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 62
- 239000010936 titanium Substances 0.000 claims description 61
- 229910052757 nitrogen Inorganic materials 0.000 claims description 34
- 229910052799 carbon Inorganic materials 0.000 claims description 33
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 31
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 30
- 229910052719 titanium Inorganic materials 0.000 claims description 30
- 239000010935 stainless steel Substances 0.000 claims description 27
- 239000011651 chromium Substances 0.000 claims description 25
- 239000011572 manganese Substances 0.000 claims description 23
- 229910001068 laves phase Inorganic materials 0.000 claims description 17
- 239000002245 particle Substances 0.000 claims description 15
- 239000012535 impurity Substances 0.000 claims description 14
- 229910052750 molybdenum Inorganic materials 0.000 claims description 13
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 12
- 239000011733 molybdenum Substances 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 11
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 11
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 11
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 11
- 229910052748 manganese Inorganic materials 0.000 claims description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims description 11
- 239000011574 phosphorus Substances 0.000 claims description 11
- 229910052710 silicon Inorganic materials 0.000 claims description 11
- 239000010703 silicon Substances 0.000 claims description 11
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 238000003303 reheating Methods 0.000 claims description 10
- 238000004804 winding Methods 0.000 claims description 10
- 238000009826 distribution Methods 0.000 claims description 8
- -1 FeCrNb Substances 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 claims description 4
- 238000000034 method Methods 0.000 claims description 3
- 229910000859 α-Fe Inorganic materials 0.000 claims description 3
- CFJRGWXELQQLSA-UHFFFAOYSA-N azanylidyneniobium Chemical compound [Nb]#N CFJRGWXELQQLSA-UHFFFAOYSA-N 0.000 claims description 2
- 239000010960 cold rolled steel Substances 0.000 abstract 5
- 238000000137 annealing Methods 0.000 abstract 1
- 238000005554 pickling Methods 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 29
- 239000010959 steel Substances 0.000 description 29
- 230000000052 comparative effect Effects 0.000 description 22
- 239000000463 material Substances 0.000 description 13
- 239000000203 mixture Substances 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
- 238000007670 refining Methods 0.000 description 7
- 230000005540 biological transmission Effects 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 4
- 239000011593 sulfur Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 2
- 208000027418 Wounds and injury Diseases 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 239000004566 building material Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 2
- 208000025599 Heat Stress disease Diseases 0.000 description 1
- 229910001275 Niobium-titanium Inorganic materials 0.000 description 1
- 235000002597 Solanum melongena Nutrition 0.000 description 1
- 244000061458 Solanum melongena Species 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- RJSRQTFBFAJJIL-UHFFFAOYSA-N niobium titanium Chemical compound [Ti].[Nb] RJSRQTFBFAJJIL-UHFFFAOYSA-N 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Images
Classifications
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- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- 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
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
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- 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
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- 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
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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%
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- 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
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- 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
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- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- 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
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a ferritic stainless steel and a method for manufacturing the same, and more particularly, high temperature characteristics such as high temperature strength and thermal fatigue characteristics through the control of the distribution and components of precipitates in the stainless steel by the control of alloy components and manufacturing methods This improved ferritic stainless steel and method for producing the same.
- ferritic stainless steels are widely used in automobile exhaust system parts, building materials, kitchen containers, and home appliances.
- exhaust manifolds among automotive exhaust system components are directly exposed to high temperature exhaust gas of 700 ° C. or higher, and require very high safety in a long operating environment. Therefore, many studies on the alloying component and the manufacturing method which improve the high temperature characteristic conventionally have been performed.
- Patent Document 0001 Korean Laid-Open Patent Publication No. 10-2006-0007441
- Embodiments of the present invention are to provide a ferritic stainless steel with improved high temperature properties such as high temperature strength and thermal fatigue properties through the control of alloy components of ferritic stainless steel, and the distribution and composition of precipitates in the ferritic stainless steel do.
- embodiments of the present invention to provide a method of manufacturing a ferritic stainless steel by controlling the reheating, rough rolling and finishing rolling process of stainless steel.
- Ferritic stainless steel in weight%, carbon (C) 0.02% or less, nitrogen (N) 0.02% or less, silicon (Si) 1.0% or less, manganese (Mn) 1.20% or less, 0.05% or less of phosphorus (P), 10.0 to 25.0% of chromium (Cr), 0.5 to 2.0% of molybdenum (Mo), 0.01 to 0.30% of titanium (Ti), and 0.30 to 0.70% of niobium (Nb), Remaining iron (Fe) and other unavoidable impurities.
- the ferritic stainless steel includes a niobium (Nb) laves phase precipitate, a precipitate containing niobium (Nb) and carbon (C) or nitrogen (N), and the precipitates are 1 ⁇ m from the grain boundary. 30 to 70% of the distribution within the region, the average particle size of the precipitates are 0.5 ⁇ m or less.
- the weight ratio of niobium (Nb) / titanium (Ti) may be 2 to 10.
- the niobium (Nb) Laves phase precipitate may include any one or more selected from the group consisting of Fe 2 Nb, FeCrNb, Cr 2 Nb.
- the niobium (Nb) Laves phase precipitate may include any one or more selected from the group consisting of Fe 2 Nb, FeCrNb, Cr 2 Nb.
- the average particle size of the precipitates may be less than 0.35 ⁇ m.
- the niobium (Nb) and carbon (C) or nitrogen (N) may be less than 30%.
- the ferritic stainless steel may have a tensile strength of 30MPa or more at 900 °C.
- the ferritic stainless steel, the thermal fatigue cycle may be 500 or more times in a temperature range of 200 to 900 °C at 50% restraint.
- Method for producing a ferritic stainless steel in weight%, carbon (C) 0.02% or less, nitrogen (N) 0.02% or less, silicon (Si) 1.0% or less, manganese (Mn) 1.20% Or less, 0.05% or less of phosphorus (P), 10.0 to 25.0% of chromium (Cr), 0.5 to 2.0% of molybdenum (Mo), 0.01 to 0.30% of titanium (Ti), and 0.30 to 0.70% of niobium (Nb) And reheating the stainless steel containing the remaining iron (Fe) and other unavoidable impurities to 1,100 to 1,300 ° C., roughly rolling the stainless steel a plurality of times, and finishing rolling the stainless steel.
- the last two rough rollings are performed at a total reduction ratio of 50% or more, and are maintained for the time of the following equation (1) before the finishing rolling after the rough rolling.
- the weight ratio of niobium (Nb) / titanium (Ti) may be 2 to 10.
- the winding temperature may be 500 to 700 °C.
- the ferritic stainless steel by adjusting the composition of the stainless steel, the size and distribution of the precipitate in the stainless steel, fine precipitates to fix the grain boundary at a high temperature to suppress the sliding of the grain boundary and the rapid movement of dislocations high temperature strength and heat High temperature characteristics, such as a fatigue characteristic, can be improved.
- embodiments of the present invention in the process of manufacturing ferritic stainless steel, by controlling the reheating, rough rolling and finishing rolling process, to prevent coarsening of grains, and thus fine precipitates are distributed in the region adjacent to the grains Can be controlled.
- TEM transmission electron microscope
- TEM 2 is a photograph taken through a transmission electron microscope (TEM) of stainless steel according to a comparative example.
- Ferritic stainless steel in weight%, carbon (C) 0.02% or less, nitrogen (N) 0.02% or less, silicon (Si) 1.0% or less, manganese (Mn) 1.20% or less, 0.05% or less of phosphorus (P), 10.0 to 25.0% of chromium (Cr), 0.5 to 2.0% of molybdenum (Mo), 0.01 to 0.30% of titanium (Ti), and 0.30 to 0.70% of niobium (Nb), Remaining iron (Fe) and other unavoidable impurities.
- the ferritic stainless steel includes a niobium (Nb) laves phase precipitate, a precipitate containing niobium (Nb) and carbon (C) or nitrogen (N), and the precipitates are 1 ⁇ m from the grain boundary. 30 to 70% of the distribution within the region, the average particle size of the precipitates are 0.5 ⁇ m or less.
- the ferritic stainless steel by weight, carbon (C) 0.02% or less, nitrogen (N) 0.02% or less, silicon (Si) 1.0% or less, manganese (Mn) 1.20% or less Phosphorus (P) 0.05% or less, chromium (Cr) 10.0 to 25.0%, molybdenum (Mo) 0.5 to 2.0%, titanium (Ti) 0.02 to 0.30%, and niobium (Nb) 0.30 to 0.70% , Remaining iron (Fe) and other unavoidable impurities.
- the amount of carbon (C) is 0.02% or less. More preferably, the amount of carbon is 0.0005% to 0.02%. If the amount of carbon (C) is less than 0.0005%, the refining price for making high-purity products is expensive, and if the amount of carbon (C) is more than 0.02%, the impurities of the material increase, so the elongation rate and work hardening index (n value) decrease. The soft brittle transition temperature (DBTT) rises and the impact characteristics deteriorate.
- DBTT soft brittle transition temperature
- the amount of nitrogen (N) is 0.02% or less. More preferably, the amount of nitrogen (N) is 0.005% to 0.02%. If the amount of nitrogen (N) is less than 0.005%, TiN crystallization is lowered, and the isotropic crystallinity of slabs is lowered. If the amount of nitrogen (N) is more than 0.02%, impurities of the material increase, the elongation is lowered, and the ductile brittle transition temperature (DBTT) ) Rises and the impact characteristics deteriorate.
- DBTT ductile brittle transition temperature
- the amount of silicon (Si) is 1.0% or less. More preferably, the amount of silicon (Si) is 0.01% to 1.0%. If the amount of silicon (Si) is less than 0.01%, the refining price is expensive. If the amount of silicon (Si) exceeds 1.0%, impurities of the material increase, so that the elongation and work hardening index (n value) fall and the Si-based Inclusion increases and processability worsens.
- the amount of manganese (Mn) is 1.20% or less. More preferably, the amount of manganese (Mn) is 0.01% to 1.20% or less. If the amount of manganese (Mn) is less than 0.01%, there is a problem that the refining price is expensive, if the amount of manganese (Mn) exceeds 1.2% there is a problem that the elongation is lowered due to an increase in impurities of the material.
- the amount of phosphorus (P) is 0.05% or less. More preferably, the amount of phosphorus (P) is 0.001% to 0.05%. If the amount of phosphorus (P) is less than 0.001%, the refining price is expensive. If the amount of phosphorus (P) is more than 0.05%, impurities of the material increase, so that the elongation and work hardening index (n value) fall. have.
- the amount of sulfur (S) is 0.005% or less. More preferably, the amount of sulfur (S) is 0.0001% to 0.005%. If the amount of sulfur (S) is less than 0.0001%, the refining price is expensive, and if the amount of sulfur (S) exceeds 0.005%, there is a problem of poor corrosion resistance.
- the amount of chromium (Cr) is 10.0 to 25.0%. If the amount of chromium (Cr) is less than 10.0%, there is a problem of poor corrosion resistance and oxidation resistance, and if the amount of chromium (Cr) is more than 25.0%, the elongation is lowered and a hot rolled sticking defect occurs. .
- the amount of nickel (Ni) is 0.01 to 0.50%. If the amount of nickel (Ni) is less than 0.01%, there is a problem that the refining price is expensive, if the amount of nickel (Ni) is more than 0.50% there is a problem that the elongation is lowered due to an increase in impurities of the material.
- the amount of molybdenum (Mo) is 0.5 to 2.0%. If the amount of molybdenum (Mo) is less than 0.5%, the amount of molybdenum (Mo) employed in the material is too small, thereby increasing the high temperature strength and thermal fatigue characteristics of the material and the probability of occurrence of abnormal oxidation, and the molybdenum (Mo) ) When the amount of) exceeds 2.0%, the impact property is lowered, which increases the risk of breakage and increases the cost of the material.
- the amount of titanium (Ti) is 0.01 to 0.30%. If the amount of titanium (Ti) is less than 0.01%, the cost of ultra low impurity refining is high, and if the amount of titanium (Ti) exceeds 0.3%, there is a problem that the nozzle is clogged when the slab is manufactured due to an increase in Ti-based oxide.
- the amount of niobium (Nb) is 0.30 to 0.70%. If the amount of niobium (Nb) is less than 0.30%, there is a problem that the high temperature strength of the material is low due to the small amount of Nb dissolved in the material, and if the amount of niobium (Nb) exceeds 0.70%, the Nb precipitates and the solid solution amount are excessively There is a problem that the elongation and impact properties worsen.
- the weight ratio of niobium (Nb) / titanium (Ti) is 2 to 10.
- titanium (Ti) and niobium (Nb) are important elements in securing the high temperature properties of the material, and affect the amount and distribution of internal precipitates depending on the addition ratio of the two elements. This will affect the fatigue properties.
- the weight ratio of niobium (Nb) / titanium (Ti) is less than 2, the amount of titanium (Ti) is relatively too large, and precipitates containing coarse titanium (Ti) are precipitated, and most of the niobium (Ti) Nb) is precipitated as a precipitate containing niobium (Nb) and carbon (C) or nitrogen (N) to form niobium (Nb) in the precipitate containing niobium (Nb) and carbon (C) or nitrogen (N). ) When the mass is 30% or more, the amount of precipitates of niobium (Nb) laves phase having a fine size decreases, and thus, the high temperature strength and the thermal fatigue characteristics decrease.
- the ferritic stainless steel is the niobium (Nb) Laves phase precipitate, the precipitate containing the niobium (Nb) and carbon (C) or nitrogen (N), the titanium (Ti) It includes a precipitate containing).
- the niobium (Nb) Laves phase precipitate may include any one or more selected from the group consisting of Fe 2 Nb, FeCrNb, Cr 2 Nb.
- the composition of the Laves phase (laves phase) is an intermetallic compound having a densely packed structure with A 2 B type.
- the particle size of the niobium (Nb) Laves phase precipitate is less than 0.2 ⁇ m has a relatively fine size.
- the precipitate containing carbon (C) or nitrogen (N) may be formed of niobium nitride (NbN), niobium carbide (NobC), and niobium carbonitride (NbCN). It may include any one or more selected from the group consisting of.
- the particle size of the precipitate containing carbon (C) or nitrogen (N) has a size of about 0.5 ⁇ m.
- the precipitate containing titanium (Ti) may include titanium nitride (TiN), titanium carbide (TiC), titanium carbonitride (TiCN), and niobium titanium (Tiobium titanium).
- NbTi) may include any one or more selected from the group consisting of.
- the particle size of the precipitate containing titanium (Ti) has a relatively coarse size of about 1 to 2 ⁇ m.
- the average particle size of the precipitate inside the material becomes 0.5 ⁇ m or less to suppress the formation of coarse precipitates. More preferably, the average particle size of the precipitates may be 0.35 ⁇ m or less.
- the precipitates are distributed in the range of 30 to 70% in the region within 1 ⁇ m from the grain boundary.
- the precipitates are distributed in a region within 1 ⁇ m from the grain boundary, and may play a role of pinning the grain boundary at a high temperature, and rapid movement of grain boundary sliding (GBS) and dislocations occurring at a high temperature. By suppressing the high temperature strength and thermal fatigue characteristics can be improved.
- niobium (Nb) and carbon (C) or nitrogen (N) with respect to the total mass of the precipitate including niobium (Nb) and carbon (C) or nitrogen (N).
- the mass of niobium (Nb) may be less than 30%.
- a niobium (Nb) laves phase precipitate having a fine size The amount of ⁇ decreases, and accordingly, the high temperature strength and the thermal fatigue property decrease.
- the amount of titanium (Ti) is relatively too large or the amount of niobium (Nb) is relatively too large
- most of the niobium (Nb) is the niobium (Nb) and carbon (C) Or precipitated as a precipitate containing nitrogen (N), so that the niobium (Nb) mass in the precipitate containing niobium (Nb) and carbon (C) or nitrogen (N) is 30% or more, thereby providing a fine size.
- Eggplants reduce the amount of the Niobium (Nb) laves phase precipitates, and therefore, the high temperature strength and thermal fatigue characteristics are reduced.
- the ferritic stainless steel according to the exemplary embodiment of the present invention may have a tensile strength of 30 MPa or more at 900 ° C.
- the thermal fatigue cycle may be at least 500 times in a temperature range of 200 to 900 °C at 50% restraint.
- compositions of the inventive and comparative steels are shown in Table 1 below.
- Comparative steel 1 is out of the content of molybdenum (Mo)
- Comparative steel 2 is out of the weight ratio of niobium (Nb) / titanium (Ti)
- Comparative steel 3 is out of the content of niobium (Nb)
- Comparative steel 4 is out of the weight ratio of niobium (Nb) / titanium (Ti).
- the stainless steel having the composition of the inventive steel and the comparative steel was carried out under the same conditions according to the method of manufacturing the ferritic stainless steel according to the embodiment of the present invention which will be described below, and the physical properties of the ferritic stainless steel according to the following are shown in Table 2 below. It was.
- TEM 1 is a photograph taken through a transmission electron microscope (TEM) of stainless steel according to an embodiment of the present invention.
- 2 is a photograph taken through a transmission electron microscope (TEM) of stainless steel according to a comparative example.
- FIG. 1 is a photograph of the inventive steel 1 of the present invention through a transmission electron microscope (TEM).
- 2 is a photograph taken with a transmission electron microscope (TEM) of Comparative Steel 2.
- fine precipitates 10 having a fine size are distributed adjacent to grain boundaries, and the average particle size of such fine precipitates 10 is 0.5 ⁇ m or less.
- coarse precipitates 20 are distributed regardless of grain boundaries, and the average particle size of such coarse precipitates is about 1 ⁇ m.
- the composition of the ferritic stainless steel satisfies the composition according to an embodiment of the present invention
- the average particle size of the precipitate is 0.5 ⁇ m or less
- the precipitates are distributed in 30 ⁇ 70% in the region within 1 ⁇ m from the grain boundary
- the tensile strength is more than 30MPa at 900 °C
- the thermal fatigue cycle at least 500 times in the temperature range of 200 to 900 °C at 50% restraint rate. Therefore, high temperature properties, such as high temperature strength and thermal fatigue characteristics of the ferritic stainless steel according to an embodiment of the present invention is improved.
- the size and distribution of fine precipitates must be controlled, which requires not only component control but also control of the hot rolling process.
- the manufacturing method of the ferritic stainless steel in weight%, carbon (C) 0.02% or less, nitrogen (N) 0.02% or less, silicon (Si) 1.0% or less, manganese (Mn) 1.20% or less, phosphorus (P) 0.05% or less, chromium (Cr) 10.0 to 25.0%, molybdenum (Mo) 0.5 to 2.0%, titanium (Ti) 0.01 to 0.30%, niobium (Nb) 0.30 to 0.70%, the remaining iron (Fe) )
- slabs are prepared using molten steel containing other unavoidable impurities. The slab is reheated, hot rough rolling, hot finishing rolling, and coiled according to the following conditions.
- the slabs are reheated at a temperature of 1,100 to 1,300 ° C. in the furnace.
- the stainless steel is provided in the form of a slab, the slab has a hot rolled reheating temperature of the slab of 1,100 ° C. or more to re-decompose coarse precipitates generated during the casting of the slab, and to coarsen the internal grains.
- the reheating temperature is set at 1,300 ° C or lower.
- the stainless steel is subjected to hot rough rolling a plurality of times.
- the last two rough rolling is performed at a total reduction rate of 50% or more, and is maintained for the time of the following formula (1) before rough rolling after rough rolling the stainless steel.
- the last two rough rolling may be performed at a total reduction ratio of 50% or more to precipitate fine precipitates in the grain boundary.
- the time maintained before finishing rolling is given 8000 / (reheating temperature -1,000) seconds or more to give sufficient recrystallization time, and the rough rolling after rough rolling of the stainless steel. It is possible to prevent the coarsening of the grains by controlling the time maintained until 120 seconds or less.
- the grains By controlling the grains as described above it is possible to provide a site (site) in which fine precipitates can be produced in the grain boundary, and to produce a fine niobium (Nb) Laves phase precipitate in the region within 1 ⁇ m from the grain boundary. .
- the fine precipitates formed around the grain boundary play a role of pinning the grain boundary at high temperature, thereby suppressing grain boundary sliding (GBS) and rapid movement of dislocation at high temperature, thereby improving high temperature strength and thermal fatigue characteristics. It plays a role.
- the finishing-rolled stainless steel can be wound.
- the winding temperature may be 500 to 700 °C.
- the winding temperature is controlled to 700 ° C. or lower to prevent coarsened precipitates during the hot rolling process according to the above, and the winding temperature is controlled to 500 ° C. or higher for plate shape and surface quality.
- Slabs were prepared according to the compositions of the inventive steels 1 to 3, respectively, and then reheated at a temperature of 1,200 ° C. in a heating furnace. Then, hot rough rolling was performed, and the last two rough rolling were performed at a total reduction rate of 70%. After rough rolling, the inventive steels were held for 60 seconds before finishing rolling. After finishing rolling, the inventive steels were cooled and wound, and the winding temperature was maintained at 550 ° C.
- Slabs were prepared according to the compositions of Inventive Steels 1 to 3, respectively, and then reheated at a temperature of 1,000 ° C. in a heating furnace. Then, hot rough rolling was performed, and the last two rough rolling were performed at a total reduction of 40%. After rough rolling, filamentous rolling, cooling and winding were performed continuously, and the winding temperature was maintained at 550 degreeC.
- the precipitates are distributed 30 to 70% in the region within 1 ⁇ m from the grain boundary, the average particle size of the precipitate is 0.5 ⁇ m or less Accordingly, it can be seen that the high temperature characteristics such as high temperature strength and thermal fatigue characteristics are improved by fixing the grain boundaries at high temperature to suppress grain boundary sliding and rapid movement of dislocations.
- Ferritic stainless steel according to embodiments of the present invention has industrial applicability applicable to automobile exhaust system parts, building materials, kitchen containers, home appliances.
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Abstract
Description
C | N | Si | Mn | P | Cr | Mo | Ti | Nb | Nb/Ti | |
발명강1 | 0.0092 | 0.0090 | 0.4 | 0.4 | 0.02 | 18.3 | 1.15 | 0.15 | 0.53 | 3.5 |
발명강2 | 0.0096 | 0.00110 | 0.4 | 0.4 | 0.02 | 21.2 | 1.54 | 0.12 | 0.56 | 4.7 |
발명강3 | 0.00134 | 0.0097 | 0.5 | 0.5 | 0.02 | 16.1 | 1.81 | 0.13 | 0.55 | 3.5 |
비교강1 | 0.0088 | 0.00114 | 0.3 | 0.4 | 0.02 | 18.2 | 0.20 | 0.11 | 0.52 | 4.7 |
비교강2 | 0.00104 | 0.0083 | 0.2 | 0.5 | 0.03 | 18.3 | 1.21 | 0.03 | 0.65 | 21.7 |
비교강3 | 0.0089 | 0.0091 | 0.3 | 0.4 | 0.02 | 19.2 | 1.55 | 0.08 | 0.21 | 2.6 |
비교강4 | 0.00123 | 0.00102 | 0.4 | 0.3 | 0.03 | 22.3 | 1.37 | 0.25 | 0.33 | 1.3 |
석출물의 크기(㎛) | 결정립계로부터 1㎛이내의 영역에 분포하는 석출물의 비율(%) | Nb와 C, N을 포함하는 석출물 내 Nb의 질량비(%) | 900℃ 인장 강도(Mpa) | 열피로 싸이클(회) | |
발명강1 | 0.28 | 58 | 11 | 34 | 564 |
발명강2 | 0.22 | 49 | 13 | 36 | 588 |
발명강3 | 0.34 | 38 | 21 | 37 | 612 |
비교강1 | 0.37 | 48 | 19 | 28 | 455 |
비교강2 | 1.21 | 12 | 78 | 27 | 472 |
비교강3 | 0.13 | 9 | 33 | 31 | 467 |
비교강4 | 0.89 | 24 | 42 | 25 | 437 |
석출물의 크기(㎛) | 결정립계로부터 1㎛이내의 영역에 분포하는 석출물의 비율(%) | Nb와 C, N을 포함하는 석출물 내 Nb의 질량비(%) | 900℃ 인장 강도(Mpa) | 열피로 싸이클(회) | |
실시예1 | 0.28 | 58 | 11 | 34 | 564 |
실시예2 | 0.22 | 49 | 13 | 36 | 588 |
실시예3 | 0.34 | 38 | 21 | 37 | 612 |
비교예1 | 0.72 | 35 | 39 | 30 | 473 |
비교예2 | 0.39 | 15 | 19 | 33 | 491 |
비교예3 | 1.34 | 24 | 49 | 31 | 479 |
Claims (11)
- 중량%로, 탄소(C) 0.02%이하, 질소(N) 0.02% 이하, 실리콘(Si) 1.0% 이하, 망간(Mn) 1.20% 이하, 인(P) 0.05% 이하, 크롬(Cr) 10.0 내지 25.0%, 몰리브데늄(Mo) 0.5 내지 2.0%, 타이타늄(Ti) 0.01 내지 0.30%, 나이오븀(Nb) 0.30 내지 0.70%로 포함하고, 나머지 철(Fe) 및 기타 불가피한 불순물을 포함하는 페라이트계 스테인리스강에 있어서,상기 페라이트계 스테인리스강은 나이오븀(Nb) 라베스상(laves phase) 석출물, 나이오븀(Nb)과 탄소(C) 또는 질소(N)을 포함하는 석출물을 포함하며, 상기 석출물들은 결정립계로부터 1㎛이내의 영역에 30 내지 70% 분포하며, 상기 석출물들의 평균 입자 크기가 0.5㎛이하인 페라이트계 스테인리스강.
- 제1항에 있어서, 나이오븀(Nb)/타이타늄(Ti)의 중량비는 2 내지 10인 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 나이오븀(Nb) 라베스상 석출물은 Fe2Nb, FeCrNb, Cr2Nb로 이루어진 그룹에서 선택되는 어느 하나 이상을 포함하는 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 나이오븀(Nb)과 탄소(C) 또는 질소(N)을 포함하는 석출물은 나이오븀 나이트라이드(niobium nitride, NbN), 나이오븀 카바이드(niobium carbide, NbC), 나이오븀 카보나이트라이드(niobium carbonitride, NbCN)로 이루어진 그룹에서 선택되는 어느 하나 이상을 포함하는 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 석출물들의 평균 입자 크기가 0.35㎛이하인 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 나이오븀(Nb)과 탄소(C) 또는 질소(N)를 포함하는 석출물 전체 질량에 대하여, 상기 나이오븀(Nb)과 탄소(C) 또는 질소(N)를 포함하는 석출물 내의 나이오븀(Nb)의 질량은 30% 미만인 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 페라이트계 스테인리스강은, 900℃에서 인장강도가 30MPa 이상인 것을 특징으로 하는 페라이트계 스테인리스강.
- 제1항에 있어서, 상기 페라이트계 스테인리스강은, 50% 구속율에서 200 내지 900℃ 온도 구간에서 열피로 싸이클이 500회 이상인 것을 특징으로 하는 페라이트계 스테인리스강.
- 중량%로, 탄소(C) 0.02%이하, 질소(N) 0.02% 이하, 실리콘(Si) 1.0% 이하, 망간(Mn) 1.20% 이하, 인(P) 0.05% 이하, 크롬(Cr) 10.0 내지 25.0%, 몰리브데늄(Mo) 0.5 내지 2.0%, 타이타늄(Ti) 0.01 내지 0.30%, 나이오븀(Nb) 0.30 내지 0.70%로 포함하고, 나머지 철(Fe) 및 기타 불가피한 불순물을 포함하는 스테인리스강을 1,100 내지 1,300℃로 재가열하는 단계;상기 스테인리스강을 복수 회의 조압연하는 단계; 및상기 스테인리스강을 사상압연하는 단계를 포함하는 페라이트계 스테인리스강의 제조 방법에 있어서,상기 조압연하는 단계에서, 최종 2회의 조압연은 총압하율 50% 이상으로 수행하며,상기 조압연 후 상기 사상압연 전, 하기 식(1)의 시간 동안 유지되는 페라이트계 스테인리스강의 제조 방법.8,000/(재가열 온도-1,000)<시간(초)<120 --------------- 식(1)
- 제9항에 있어서, 나이오븀(Nb)/타이타늄(Ti)의 중량비는 2 내지 10인 것을 특징으로 하는 페라이트계 스테인리스강의 제조 방법.
- 제9항에 있어서, 상기 사상압연하는 단계 이후, 권취하는 단계를 더 포함하며, 권취 온도는 500 내지 700℃인 것을 특징으로 하는 페라이트계 스테인리스강의 제조 방법.
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JP4518834B2 (ja) * | 2004-05-12 | 2010-08-04 | 新日鐵住金ステンレス株式会社 | 加工性に優れた耐熱フェライト系ステンレス鋼板の製造方法 |
JP2007211313A (ja) * | 2006-02-10 | 2007-08-23 | Nippon Metal Ind Co Ltd | 耐リジング性に優れたフェライト系ステンレス鋼とその製造方法 |
EP2460899A4 (en) * | 2009-07-27 | 2014-07-09 | Nisshin Steel Co Ltd | FERRITIC STAINLESS STEEL FOR EGR COOLER AND EGR COOLER |
CN104073738B (zh) * | 2014-07-16 | 2016-09-28 | 苏州大学 | 奥氏体耐热钢及其制备方法 |
-
2015
- 2015-09-22 KR KR1020150133572A patent/KR101697093B1/ko active IP Right Grant
-
2016
- 2016-02-18 CN CN201680017870.7A patent/CN107429366A/zh active Pending
- 2016-02-18 JP JP2017542037A patent/JP6461363B2/ja active Active
- 2016-02-18 WO PCT/KR2016/001638 patent/WO2017052005A1/ko active Application Filing
- 2016-02-18 US US15/579,789 patent/US20180179607A1/en not_active Abandoned
Patent Citations (5)
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JPH09194937A (ja) * | 1996-01-19 | 1997-07-29 | Nippon Steel Corp | 加工性に優れた高純フェライト系ステンレス熱延鋼帯の製造方法 |
JPH1017999A (ja) * | 1996-06-27 | 1998-01-20 | Kawasaki Steel Corp | 耐食性、成形性および材質均一性に優れるフェライト系ステンレス熱延鋼板およびその製造方法 |
JPH1017937A (ja) * | 1996-06-28 | 1998-01-20 | Kawasaki Steel Corp | 加工性に優れるフェライト系ステンレス鋼板の製造方法 |
JP2006233278A (ja) * | 2005-02-25 | 2006-09-07 | Nippon Steel & Sumikin Stainless Steel Corp | 加工性に優れた排気部品用フェライト系ステンレス鋼板およびその製造方法 |
JP2008291303A (ja) * | 2007-05-24 | 2008-12-04 | Jfe Steel Kk | 打ち抜き加工性に優れる温水器用フェライト系ステンレス鋼板およびその製造方法 |
Also Published As
Publication number | Publication date |
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KR101697093B1 (ko) | 2017-01-18 |
CN107429366A (zh) | 2017-12-01 |
JP6461363B2 (ja) | 2019-01-30 |
US20180179607A1 (en) | 2018-06-28 |
JP2018508656A (ja) | 2018-03-29 |
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