WO2017169011A1 - Ti含有フェライト系ステンレス鋼板および製造方法並びにフランジ - Google Patents
Ti含有フェライト系ステンレス鋼板および製造方法並びにフランジ Download PDFInfo
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- WO2017169011A1 WO2017169011A1 PCT/JP2017/002300 JP2017002300W WO2017169011A1 WO 2017169011 A1 WO2017169011 A1 WO 2017169011A1 JP 2017002300 W JP2017002300 W JP 2017002300W WO 2017169011 A1 WO2017169011 A1 WO 2017169011A1
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- WIPO (PCT)
- Prior art keywords
- steel sheet
- less
- ferritic stainless
- stainless steel
- mass
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 75
- 239000010959 steel Substances 0.000 claims abstract description 75
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 21
- 239000013078 crystal Substances 0.000 claims abstract description 16
- 239000000203 mixture Substances 0.000 claims abstract description 15
- 239000000126 substance Substances 0.000 claims abstract description 13
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 238000005096 rolling process Methods 0.000 claims description 22
- 229910052799 carbon Inorganic materials 0.000 claims description 18
- 238000000034 method Methods 0.000 claims description 18
- 238000000605 extraction Methods 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 238000000137 annealing Methods 0.000 claims description 8
- 238000005520 cutting process Methods 0.000 claims description 3
- 238000005498 polishing Methods 0.000 claims description 3
- 239000006104 solid solution Substances 0.000 abstract description 5
- 239000000243 solution Substances 0.000 abstract 1
- 238000005098 hot rolling Methods 0.000 description 15
- 230000000694 effects Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 11
- 238000004804 winding Methods 0.000 description 9
- 238000005097 cold rolling Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- 239000002436 steel type Substances 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 238000009863 impact test Methods 0.000 description 4
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 238000009628 steelmaking Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- YRKCREAYFQTBPV-UHFFFAOYSA-N acetylacetone Chemical compound CC(=O)CC(C)=O YRKCREAYFQTBPV-UHFFFAOYSA-N 0.000 description 2
- 230000002441 reversible effect Effects 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 244000017020 Ipomoea batatas Species 0.000 description 1
- 235000002678 Ipomoea batatas Nutrition 0.000 description 1
- OKIZCWYLBDKLSU-UHFFFAOYSA-M N,N,N-Trimethylmethanaminium chloride Chemical compound [Cl-].C[N+](C)(C)C OKIZCWYLBDKLSU-UHFFFAOYSA-M 0.000 description 1
- 230000005856 abnormality Effects 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000009841 combustion method Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000012528 membrane Substances 0.000 description 1
- 239000011255 nonaqueous electrolyte Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000001226 reprecipitation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- 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
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
- F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
- F01N13/16—Selection of particular materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
- F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
- F01N13/18—Construction facilitating manufacture, assembly, or disassembly
- F01N13/1805—Fixing exhaust manifolds, exhaust pipes or pipe sections to each other, to engine or to vehicle body
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
- F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
- F01N13/18—Construction facilitating manufacture, assembly, or disassembly
- F01N13/1872—Construction facilitating manufacture, assembly, or disassembly the assembly using stamp-formed parts or otherwise deformed sheet-metal
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
- F01N2530/00—Selection of materials for tubes, chambers or housings
- F01N2530/02—Corrosion resistive metals
- F01N2530/04—Steel alloys, e.g. stainless steel
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Definitions
- the present invention relates to a thick gauge Ti-containing ferritic stainless steel sheet having excellent toughness and a method for producing the same. Moreover, it is related with the flange using the said Ti containing ferritic stainless steel plate.
- Automotive exhaust gas flow path members are required to have characteristics such as corrosion resistance, heat resistance and strength.
- austenitic stainless steel sheets have been frequently used as materials excellent in these characteristics.
- ferritic steel type that has a low thermal expansion coefficient and a low raw material cost instead of an austenitic steel type.
- An example of such an alternative material is a Ti-containing ferritic stainless steel sheet.
- An automobile exhaust gas flow path member is generally manufactured by a process in which a cold-rolled annealed steel sheet is subjected to press processing, or various processes are performed after the cold-rolled annealed steel sheet is pipe-processed.
- automobile exhaust gas flow path members are often formed into a complicated shape, and the cold-rolled annealed steel sheet, which is the material, requires excellent workability.
- it is advantageous to increase the cold rolling rate.
- it is effective to use a hot-rolled annealed steel sheet having a thickness gauge (for example, a thickness of 5.0 mm or more).
- Patent Document 1 discloses a technique of performing rapid cooling after hot rolling and winding at a temperature of 450 ° C. or less.
- Patent Document 2 discloses a technique in which the hot rolling finishing temperature is increased according to the composition and the water is cooled rapidly after winding.
- Patent Document 3 discloses a method in which a coil is wound up at 570 ° C.
- An object of the present invention is to provide a Ti-containing ferritic stainless steel thick gauge steel plate having excellent toughness and a flange using the same.
- the toughness of the Ti-containing ferritic stainless steel thick gauge steel sheet is improved by reducing the amount of C and N dissolved in the ferrite phase matrix. It was found that the degree of is greatly influenced by the ferrite crystal grain size.
- the present invention has been completed based on such findings.
- K value ⁇ 0.07 ⁇ Cr-6790 ⁇ Free (C + N) ⁇ 1.44 ⁇ d + 267 (1)
- Free (C + N) was obtained by subtracting the total content (mass%) of C and N present in the extraction residue recovered by the electrolytic extraction method from the total content (mass%) of C and N present in the steel. Value (mass%).
- d is an average crystal grain size ( ⁇ m) determined by a cutting method using a linear test line defined in Annex C of JIS G0551: 2013 on an observation surface obtained by polishing a cross section (L cross section) parallel to the rolling direction and the plate thickness direction. ).
- a Ti-containing ferritic stainless steel thick gauge steel plate having excellent toughness can be realized stably. Since this steel plate has particularly improved low-temperature toughness, it is possible to relax restrictions on sheet passing conditions and manufacturing conditions. Even when processing thick gauge steel plates into various parts (such as flanges in automobile exhaust gas paths), the reliability of toughness is high.
- the C content (the total amount of C and solute C present as a compound) is limited to 0.030% or less.
- the content is more preferably 0.020% or less, and may be controlled to 0.015% or less.
- An excessively low C increases the load on steel making and increases the cost.
- steel sheets with a C content of 0.003% or more are targeted.
- Si and Mn are effective as a deoxidizer and have the effect of improving high-temperature oxidation resistance. It is more effective to secure a content of 0.02% or more for Si and 0.10% or more for Mn. When these elements are contained in a large amount, they cause the embrittlement of steel.
- the Si content is limited to 2.0% or less, and more preferably 1.0% or less.
- the Mn content is also limited to 2.0% or less, and more preferably 1.0% or less.
- P and S When P and S are contained in a large amount, it causes a decrease in corrosion resistance.
- the P content is acceptable up to 0.050% and the S content is acceptable up to 0.040%.
- An excessively low P and low S increase the load on steel making and become uneconomical.
- the P content may be adjusted in the range of 0.010 to 0.050%, and the S content in the range of 0.0005 to 0.040%.
- Cr is important for ensuring corrosion resistance as stainless steel. It is also effective for improving high temperature oxidation resistance. In order to exert these effects, a Cr content of 10.0% or more is necessary. If a large amount of Cr is contained, the steel becomes hard, which may hinder the toughness improvement of the thick gauge hot-rolled annealed steel sheet. Here, steel with a Cr content of 19.0% or less is targeted.
- N is a factor that reduces the toughness of the hot-rolled annealed steel sheet.
- the N content (the total amount of solute N and N present as a compound) is limited to 0.030% or less.
- the content is more preferably 0.020% or less, and may be controlled to 0.015% or less.
- An excessively low N increases the load on steel making and increases the cost.
- the N content may be adjusted in the range of 0.003% or more.
- Ti combines with C and N to form Ti carbonitride, thereby suppressing grain boundary segregation of Cr carbonitride and extremely effective in maintaining high corrosion resistance and high temperature oxidation resistance of steel. It is.
- the Ti content needs to be 0.07% or more. 0.09% or more is more effective, and more preferably 0.15% or more.
- An excessive Ti content is not preferable because it promotes a decrease in toughness of the hot-rolled annealed steel sheet. As a result of various studies, the Ti content is limited to 0.50% or less, and it is more desirable to make it contain in the range of 0.40% or less.
- carbonitride refers to a compound in which one or more of C and N are bonded to a metal element. In the case of Ti carbonitride, TiC, TiN and Ti (C, N) correspond to this.
- Al is effective as a deoxidizer. In order to obtain the effect sufficiently, it is effective to add so that the Al content is 0.010% or more. A large amount of Al content causes a decrease in toughness. Al content is limited to 0.20% or less.
- Mo is effective in improving the corrosion resistance and can be added as necessary. In that case, it is more effective to set the Mo content to 0.01% or more. A large amount of Mo may adversely affect toughness.
- the Mo content is in the range of 0 to 1.50%.
- the B is effective in improving the secondary workability and can be added as necessary. In that case, it is more effective to secure a content of 0.0010% or more. However, if the B content exceeds 0.0003%, the formation of Cr 2 B may impair the uniformity of the metal structure, and the workability may be reduced.
- the B content is in the range of 0 to 0.0003%.
- K value The K value represented by the following formula (1) is a U-notch impact test piece (thickness direction is rolled) in a Ti gauge ferritic stainless steel thick gauge steel plate (plate thickness 5.0 to 11.0 mm) in the above chemical composition range.
- An index that accurately estimates the Charpy impact value (J / cm 2 ) at 20 ° C. using the direction perpendicular to the plate thickness direction and the plate thickness direction from the Cr content in steel, the amount of solute C + N, and the average crystal grain size. is there.
- K value ⁇ 0.07 ⁇ Cr-6790 ⁇ Free (C + N) ⁇ 1.44 ⁇ d + 267 (1)
- the value of the Cr content (% by mass) in the steel is substituted for the Cr position in the formula (1).
- Free (C + N) was obtained by subtracting the total content (mass%) of C and N present in the extraction residue recovered by the electrolytic extraction method from the total content (mass%) of C and N present in the steel. Value (mass%).
- d is an average crystal grain size ( ⁇ m) determined by a cutting method using a linear test line defined in Annex C of JIS G0551: 2013 on an observation surface obtained by polishing a cross section (L cross section) parallel to the rolling direction and the plate thickness direction. ).
- the toughness near room temperature of the thick gauge Ti-containing ferritic stainless steel sheet is greatly affected by the Cr content, the solute C + N amount, and the ferrite average crystal grain size. . If the Cr content, the solid solution C + N amount and the average crystal grain size are adjusted so that the chemical composition is satisfied and the K value is 150 or more, when processing a thick gauge steel plate into a steel pipe or various members, It was confirmed that the reliability relating to toughness when cold rolling was performed to obtain a thin gauge steel sheet was sufficiently ensured. Therefore, in this specification, it is required that the K value is 150 or more.
- the amount of solid solution C + N and the average grain size of ferrite in the hot-rolled annealed steel sheet can be controlled by hot-rolling conditions described later, and a hot-rolled annealed steel sheet having a K value of 150 or more can be created.
- Free (C + N) in the above formula (1) corresponds to a solid solution (C + N) concentration (mass%).
- Free (C + N) can be obtained by the following method. [How to find Free (C + N)] In a non-aqueous electrolyte consisting of 10% by mass acetylacetone, 1% by mass tetramethylammonium chloride and 89% by mass methyl alcohol, a sample with a known mass collected from a steel plate was used against a saturated sweet potato reference electrode (SCE). Apply a potential of -100 mV to 400 mV to dissolve all the sample matrix (metal substrate), and then filter the liquid containing undissolved material through a membrane filter with a pore size of 0.05 ⁇ m.
- SCE saturated sweet potato reference electrode
- C and N in the extraction residue are analyzed by infrared absorption method-high frequency combustion method for C, and by impulse heating melting-thermal conductivity method for N, respectively, and the total of C and N present in the extraction residue Content Insol (C + N) (mass% in steel) is calculated.
- Free (C + N) (mass%) is obtained by the following equation (2).
- Free (C + N) Total (C + N) -Insol (C + N) (2)
- Total (C + N) is the total amount (mass%) of C and N present in the steel
- Insol (C + N) is the total content (mass%) of C and N present in the extraction residue.
- Ti-containing ferritic stainless steel is one of the steel types useful for automotive exhaust gas passage member applications in terms of material characteristics such as corrosion resistance and heat resistance. An excellent workability is required for a material steel plate for processing into an automobile exhaust gas flow path member. In order to improve the Rankford value (r value), which is an index of workability, it is effective to increase the cold rolling rate. In order to obtain a high cold rolling rate, it is advantageous to employ a hot-rolled steel plate with a thick gauge.
- Ti-containing ferritic stainless steel is a steel type that tends to cause a reduction in toughness of the steel sheet from around normal temperature to low temperature. Thick gauge steel plates are more likely to have the effect of reduced toughness.
- toughness improvement is intended for hot rolled steel sheets having a thickness of 5.0 mm or more. It is more effective to target a hot-rolled steel sheet having a thickness of 5.5 mm or more. If the plate thickness becomes too thick, the load may be excessive in a general sheet passing line in the cold rolling process.
- a steel plate having a thickness of 11.0 mm or less is targeted. More preferably, the plate thickness is 9.0 mm or less.
- the above-described thick gauge Ti-containing ferritic stainless steel hot-rolled steel sheet having excellent toughness can be produced by a conventional stainless-steel hot-rolled steel sheet production facility. Below, a manufacturing method is illustrated.
- a cast slab is manufactured by a continuous casting method.
- An ingot may be made by the ingot-making method, and the slab may be produced by forging or split rolling.
- the slab thickness is preferably 200 to 250 mm.
- the slab is placed in a heating furnace and heated to a temperature of 950 ° C. or higher.
- the heating time time during which the material temperature is maintained at 950 ° C. or higher
- the heating time can be set, for example, in the range of 50 to 120 minutes.
- coarse TiC generated at the time of casting decomposes into Ti + C, and a structural state in which TiC has almost disappeared can be realized.
- TiN is not completely decomposed even at 1150 ° C., it is not necessary to pay particular attention to complete solid solution of N.
- the maximum material temperature can be set within a range of 1120 ° C. or less, the material temperature (extraction temperature) when taking out from the furnace needs to be adjusted to a temperature range described later.
- Rough rolling The heated slab is taken out of the furnace at an extraction temperature of 950 to 1120 ° C. and rolled by a roughing mill. If the extraction temperature is higher than this, the average crystal grain size of the recrystallized ferrite phase tends to be coarse, and it becomes difficult to obtain a hot-rolled steel sheet having the above-mentioned K value of 150 or less.
- Rough rolling is performed by rolling in one pass or a plurality of passes to produce an intermediate slab having a thickness of 20 to 50 mm. At that time, it is important to control the surface temperature of the intermediate slab obtained by rough rolling so as to be 700 to 850 ° C.
- the extraction temperature and the rough rolling pass schedule are set so that at least the final pass temperature of rough rolling is in the range of 700 to 850 ° C.
- This temperature range overlaps the temperature range where TiC reprecipitation occurs.
- TiC is reprecipitated during rough rolling from a state in which almost no undissolved TiC remains, fine TiC is generated from many sites.
- Ti carbonitride generated with these many TiCs or TiN already deposited as nuclei is finely dispersed.
- the finely dispersed Ti carbonitride exhibits the effect of suppressing the coarsening of ferrite recrystallized grains by the pinning effect.
- the total rolling rate of rough rolling is preferably 80 to 90%.
- finish hot rolling A series of hot rolling applied to the intermediate slab before winding is herein referred to as “finish hot rolling”.
- the finish hot rolling may be performed using a reverse rolling mill or a tandem continuous rolling mill.
- the pass schedule is set so that the plate thickness after the final pass becomes 5.0 to 11.0 mm and the winding temperature described later can be realized.
- the growth of recrystallized grains is suppressed by the pinning effect even during finish hot rolling.
- the total rolling rate of finish hot rolling can be set to 65 to 85%, for example.
- Winding The steel sheet that has been subjected to finish hot rolling is wound into a coil with a surface temperature of 650 to 800 ° C. to obtain a hot-rolled steel sheet.
- the coil When the coil is wound at a temperature lower than 650 ° C., the high-temperature strength is increased, so that a state where the coil cannot be wound in a normal shape is likely to occur.
- it is necessary to pass a rewinding process, leading to an increase in production cost.
- it is wound at a temperature higher than 800 ° C. dynamic secondary recrystallization is promoted, and crystal grain coarsening tends to proceed. In this case, there is a possibility that the K value is lowered (that is, the toughness is lowered).
- annealing By subjecting the hot-rolled steel sheet obtained as described above to annealing at 800 to 1100 ° C. (hot-rolled sheet annealing), a thick gauge Ti-containing ferritic stainless steel sheet having excellent toughness can be obtained.
- the annealing time can be, for example, soaking 0 to 5 minutes.
- the soaking of 0 minutes refers to the case of cooling immediately after the material temperature reaches a predetermined temperature.
- the steel shown in Table 1 was melted to obtain a continuous cast slab having a thickness of about 200 mm. All the chemical compositions of the steel satisfy the provisions of the present invention.
- Each continuous cast slab was placed in a heating furnace, held at the slab heating temperature shown in Table 2 for about 50 to 100 minutes according to the steel type, then taken out of the furnace, and immediately subjected to rough rolling by a roughing mill.
- the extraction temperature was the same as the slab heating temperature.
- Rough rolling was performed in 7 to 9 passes according to the finish target plate thickness, and an intermediate slab having a thickness of 20 to 50 mm was produced. The surface temperature of the intermediate slab was measured on the final pass exit side of the roughing mill. The temperature is displayed as “intermediate slab temperature” in Table 2.
- the obtained intermediate slab was immediately subjected to finish hot rolling by a continuous hot rolling mill equipped with a 6-stand mill or a reversible hot rolling mill having a coiler furnace, and then wound up to obtain the plate thickness shown in Table 2.
- a hot rolled steel sheet was obtained.
- the winding temperature was determined by measuring the plate surface temperature immediately before the winder.
- the obtained hot-rolled steel sheet was subjected to hot-rolled sheet annealing at a temperature shown in Table 2 for soaking 0 minutes.
- Nos. 21, 22, 23, 24, 25, 26, 27, and 28, which are comparative examples, are slab heating temperatures, intermediate slab temperatures, and coiling temperatures that are significantly higher than those of the present invention.
- the stopping effect was not obtained, the average crystal grain size was increased, and as a result, the toughness was reduced.
- the slab heating temperature and the intermediate slab temperature satisfy the conditions of the present invention, but the coiled shape was poor because the coiling temperature was low.
- Ti addition amount is small although C and N content in steel is high, Free (C + N) became high and toughness fell.
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Abstract
Description
[1]質量%で、C:0.003~0.030%、Si:2.0%以下、Mn:2.0%以下、P:0.050%以下、S:0.040%以下、Cr:10.0~19.0%、N:0.030%以下、Ti:0.07~0.50%、Al:0.010~0.20%、残部Feおよび不可避的不純物からなる化学組成を有し、下記(1)式により定義されるK値が150以上であり、板厚が5.0~11.0mmであるTi含有フェライト系ステンレス鋼板。
K値=-0.07×Cr-6790×Free(C+N)-1.44×d+267 ……(1)
ここで、(1)式のCrの箇所には鋼中Cr含有量(質量%)の値が代入される。Free(C+N)は、鋼中に存在するCとNの合計含有量(質量%)から電解抽出法で回収される抽出残渣中に存在するCとNの合計含有量(質量%)を差し引いた値(質量%)である。dは、圧延方向および板厚方向に平行な断面(L断面)を研磨した観察面について、JIS G0551:2013の附属書Cに規定される直線試験線による切断法により求まる平均結晶粒径(μm)である。
[2]質量%で、さらにMo:1.50%以下を含有する化学組成を有する上記[1]に記載のTi含有フェライト系ステンレス鋼板。
[3]質量%で、さらにB:0.0030%以下を含有する化学組成を有する上記[1]または[2]に記載のTi含有フェライト系ステンレス鋼板。
[4]前記化学組成を有する鋼のスラブを加熱炉で加熱したのち950~1120℃の温度で炉から出し、粗圧延機により圧延して板厚20~50mm、表面温度700~850℃の中間スラブとし、次いで前記中間スラブに熱間圧延を施して板厚5.0~11.0mmとしたのち表面温度650~800℃にて巻き取ることにより熱延鋼板を得る工程、
前記熱延鋼板を800~1100℃で焼鈍する工程、
を有する上記[1]~[3]のいずれかに記載のTi含有フェライト系ステンレス鋼板の製造方法。
[5]上記[1]~[3]のいずれかに記載のTi含有フェライト系ステンレス鋼板を用いたフランジ。
[6]前記フランジが排ガス経路用フランジである上記[5]に記載のフランジ。
[7]前記フランジが自動車排ガス経路用フランジである上記[5]に記載のフランジ。
本発明では、以下に示す成分元素を含有するフェライト系ステンレス鋼を対象とする。鋼板の化学組成に関する「%」は、特に断らない限り質量%を意味する。
下記(1)式で表されるK値は、上記化学組成範囲のTi含有フェライト系ステンレス鋼の厚ゲージ鋼板(板厚5.0~11.0mm)におけるUノッチ衝撃試験片(衝撃方向が圧延方向と板厚方向に垂直な方向)を用いた20℃でのシャルピー衝撃値(J/cm2)を、鋼中Cr含有量、固溶C+N量、平均結晶粒径から精度良く推定する指標である。
K値=-0.07×Cr-6790×Free(C+N)-1.44×d+267 ……(1)
ここで、(1)式のCrの箇所には鋼中Cr含有量(質量%)の値が代入される。Free(C+N)は、鋼中に存在するCとNの合計含有量(質量%)から電解抽出法で回収される抽出残渣中に存在するCとNの合計含有量(質量%)を差し引いた値(質量%)である。dは、圧延方向および板厚方向に平行な断面(L断面)を研磨した観察面について、JIS G0551:2013の附属書Cに規定される直線試験線による切断法により求まる平均結晶粒径(μm)である。
〔Free(C+N)の求め方〕
10質量%のアセチルアセトン、1質量%のテトラメチルアンモニウムクロライド、89質量%のメチルアルコールからなる非水系電解液中で、鋼板から採取した質量既知のサンプルに、飽和甘汞基準電極(SCE)に対して-100mV~400mVの電位を付与し、サンプルのマトリックス(金属素地)を全部溶解させたのち、未溶解物を含む液を孔径0.05μmのメンブレンフィルターにてろ過し、フィルターに残った固形分を抽出残渣として回収する。抽出残渣中のCおよびNを、Cについては赤外線吸収式-高周波燃焼法にて、Nについてはインパルス加熱融解-熱伝導度法にてそれぞれ分析し、抽出残渣中に存在するCとNの合計含有量Insol(C+N)(鋼中に占める質量%)を算出する。Free(C+N)(質量%)は下記(2)式によって求まる。
Free(C+N)=Total(C+N)-Insol(C+N) ……(2)
ここで、Total(C+N)は鋼中に存在するCとNの合計量(質量%)、Insol(C+N)は抽出残渣中に存在するCとNの合計含有量(質量%)である。
Ti含有フェライト系ステンレス鋼は、耐食性、耐熱性等の材料特性面において、自動車排ガス流路部材用途に有用な鋼種の一つである。自動車排ガス流路部材に加工するための素材鋼板には優れた加工性が要求される。その加工性の指標となるランクフォード値(r値)を向上させるためには、冷間圧延率を増大させることが効果的である。高い冷間圧延率を稼ぐためには、厚ゲージの熱延鋼板を採用することが有利となる。一方、Ti含有フェライト系ステンレス鋼は常温付近から低温側で鋼板の靭性低下を生じやすい鋼種である。厚ゲージの鋼板では靭性低下の影響がより顕在化しやすい。
靭性に優れる上記の厚ゲージTi含有フェライト系ステンレス熱延鋼板は、従来一般的なステンレス熱延鋼板製造設備にて製造することができる。以下に、製造方法を例示する。
連続鋳造法によって鋳造スラブを製造する。造塊法によって鋳塊を作り、鍛造あるいは分塊圧延にてスラブを製造してもよい。スラブ厚さは200~250mmとすることが好ましい。
上記スラブを加熱炉に入れ、950℃以上の温度に加熱する。加熱時間(材料温度が950℃以上に保持される時間)は例えば50~120分の範囲で設定することができる。950℃以上の温度に加熱することにより、鋳造時に生成した粗大なTiCがTi+Cに分解し、TiCがほぼ消失した組織状態を実現できる。TiNについては1150℃でもまだ完全には分解しないが、Nの完全固溶化には特にこだわる必要はない。材料の最高到達温度は1120℃以下の範囲で設定できるが、炉から出す際の材料温度(抽出温度)は後述の温度範囲に調整する必要がある。
加熱後のスラブを抽出温度950~1120℃にて炉から出し、粗圧延機により圧延する。抽出温度がこれより高いと、再結晶フェライト相の平均結晶粒径が粗大化しやすく、上述のK値が150以下である熱延鋼板を得ることが難しくなる。粗圧延は1パスまたは複数パスの圧延にて行い、板厚20~50mmの中間スラブを製造する。その際、粗圧延によって得られる中間スラブの表面温度が700~850℃となるようにコントロールすることが重要である。すなわち、少なくとも粗圧延の最終パス温度が700~850℃の範囲となるように抽出温度および粗圧延パススケジュールを設定する。この温度範囲はTiCの再析出が生じる温度域に重なる。未固溶のTiCがほとんど残存していない状態から、粗圧延中にTiCを再析出させると、多くのサイトから微細なTiCが発生する。中間スラブ中には、これら数多くのTiCあるいは既に析出しているTiNを核として生成したTi炭窒化物が微細分散した状態となる。微細分散したTi炭窒化物は、ピン止め効果によってフェライト再結晶粒の粗大化を抑制する作用を発揮する。中間スラブの表面温度が850℃を超えるような高温で粗圧延を行うと、TiCが活発に再析出する温度より高温での粗圧延となるので、前記ピン止め効果が十分に発揮されず、粗大結晶粒が生成し、結晶粒微細化効果が不十分となる。一方、中間スラブの表面温度が700℃を下回ると、後述の仕上熱間圧延での変形抵抗が増大したり、巻取温度が低くなりすぎたりする要因となる。粗圧延の合計圧延率は80~90%とすることが好ましい。
上記中間スラブに対して巻取までの間に施す一連の熱間圧延を、ここでは「仕上熱間圧延」と呼ぶ。仕上熱間圧延は、リバース式圧延機を用いて行ってもよいし、タンデム式の連続圧延機を用いて行ってもよい。最終パス後の板厚が5.0~11.0mmとなり、かつ後述の巻取温度が実現できるようにパススケジュールを設定する。仕上熱間圧延中にもピン止め効果によって再結晶粒の成長が抑制される。仕上熱間圧延の合計圧延率は例えば65~85%とすることができる。
仕上熱間圧延を終えた鋼板は、表面温度が650~800℃である状態でコイル状に巻き取り、熱延鋼板とする。650℃より低温で巻き取ると、高温強度が上昇するため、正常な形でコイル状に巻き取れない状態が生じやすい。このような巻取異常が発生すると、巻きなおし工程を通板する必要があるため生産コスト上昇につながる。800℃より高温で巻き取ると動的な2次再結晶化が促進され、結晶粒粗大化が進行しやすい。この場合、K値の低下(すなわち靭性低下)につながる恐れがある。巻取後は、そのまま大気中で放冷すればよい。水冷等の冷却処理を行わなくても、上記のピン止め効果によってもたらされる効果は維持される。低温靭性改善は結晶粒微細化によるところが大きい。また、固溶C、Nの低減によるマトリックスの軟質化も低温靭性改善に寄与していると考えられる。
上記のようにして得られた熱延鋼板に、800~1100℃での焼鈍(熱延板焼鈍)を施すことによって、靭性に優れた厚ゲージのTi含有フェライト系ステンレス鋼板を得ることができる。焼鈍時間は例えば均熱0~5分とすることができる。ここで、均熱0分とは材料温度が所定の温度に到達したのち直ちに冷却する場合をいう。
Claims (7)
- 質量%で、C:0.003~0.030%、Si:2.0%以下、Mn:2.0%以下、P:0.050%以下、S:0.040%以下、Cr:10.0~19.0%、N:0.030%以下、Ti:0.07~0.50%、Al:0.010~0.20%、残部Feおよび不可避的不純物からなる化学組成を有し、下記(1)式により定義されるK値が150以上であり、板厚が5.0~11.0mmであるTi含有フェライト系ステンレス鋼板。
K値=-0.07×Cr-6790×Free(C+N)-1.44×d+267 ……(1)
ここで、(1)式のCrの箇所には鋼中Cr含有量(質量%)の値が代入される。Free(C+N)は、鋼中に存在するCとNの合計含有量(質量%)から電解抽出法で回収される抽出残渣中に存在するCとNの合計含有量(質量%)を差し引いた値(質量%)である。dは、圧延方向および板厚方向に平行な断面(L断面)を研磨した観察面について、JIS G0551:2013の附属書Cに規定される直線試験線による切断法により求まる平均結晶粒径(μm)である。 - 質量%で、さらにMo:1.50%以下を含有する化学組成を有する請求項1に記載のTi含有フェライト系ステンレス鋼板。
- 質量%で、さらにB:0.0030%以下を含有する化学組成を有する請求項1に記載のTi含有フェライト系ステンレス鋼板。
- 前記化学組成を有する鋼のスラブを加熱炉で加熱したのち950~1120℃の温度で炉から出し、粗圧延機により圧延して板厚20~50mm、表面温度700~850℃の中間スラブとし、次いで前記中間スラブに熱間圧延を施して板厚5.0~11.0mmとしたのち表面温度650~800℃にて巻き取ることにより熱延鋼板を得る工程、
前記熱延鋼板を800~1100℃で焼鈍する工程、
を有する請求項1~3のいずれか1項に記載のTi含有フェライト系ステンレス鋼板の製造方法。 - 請求項1~3のいずれか1項に記載のTi含有フェライト系ステンレス鋼板を用いたフランジ。
- 前記フランジが排ガス経路用フランジである請求項5に記載のフランジ。
- 前記フランジが自動車排ガス経路用フランジである請求項5に記載のフランジ。
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MX2018010953A MX2018010953A (es) | 2016-03-30 | 2017-01-24 | Lamina de acero inoxidable ferritico que contiene ti, metodo de fabricacion, y brida. |
MYPI2018703519A MY189619A (en) | 2016-03-30 | 2017-01-24 | Ti-containing ferritic stainless steel sheet, manufacturing method, and flange |
US16/082,315 US20190093192A1 (en) | 2016-03-30 | 2017-01-24 | Ti-CONTAINING FERRITIC STAINLESS STEEL SHEET, MANUFACTURING METHOD, AND FLANGE |
CA3015441A CA3015441C (en) | 2016-03-30 | 2017-01-24 | Ti-containing ferritic stainless steel sheet, manufacturing method, and flange |
EP17773561.0A EP3438308A4 (en) | 2016-03-30 | 2017-01-24 | FERRITIC STAINLESS STEEL SHEET COMPRISING TITANIUM, MANUFACTURING METHOD AND FLANGE |
CN201780020309.9A CN109415783B (zh) | 2016-03-30 | 2017-01-24 | 含Ti铁素体系不锈钢板及制造方法以及法兰 |
KR1020187031373A KR102672884B1 (ko) | 2016-03-30 | 2017-01-24 | Ti 함유 페라이트계 스테인리스 강판 및 제조 방법 및 플랜지 |
RU2018138007A RU2719968C1 (ru) | 2016-03-30 | 2017-01-24 | ЛИСТ ИЗ Ti-СОДЕРЖАЩЕЙ ФЕРРИТНОЙ НЕРЖАВЕЮЩЕЙ СТАЛИ, СПОСОБ ПРОИЗВОДСТВА И ФЛАНЕЦ |
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CN111479944A (zh) * | 2017-12-14 | 2020-07-31 | 株式会社Posco | 具有优异的冲击韧性的基于铁素体的不锈钢及其生产方法 |
EP3839087A4 (en) * | 2018-09-19 | 2021-08-11 | Posco | HOT-ROLLED AND NOT ANNEALED FERRITIC STAINLESS STEEL SHEET WITH EXCELLENT IMPACT RESISTANCE AND PROCESS FOR ITS MANUFACTURING |
EP3859044A4 (en) * | 2018-11-06 | 2021-12-22 | Posco | HOT-ROLLED STEEL SHEET WITH EXCELLENT LOW TEMPERATURE IMPACT RESISTANCE AND PROCESS FOR ITS MANUFACTURING |
EP3896178A4 (en) * | 2018-12-11 | 2022-03-16 | JFE Steel Corporation | FERRITIC STAINLESS STEEL SHEET AND METHOD OF PRODUCTION THEREOF |
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JP6261648B2 (ja) * | 2016-05-16 | 2018-01-17 | 日新製鋼株式会社 | 排気管フランジ部品用Ti含有フェライト系ステンレス鋼板および製造方法 |
KR102443897B1 (ko) * | 2018-03-30 | 2022-09-19 | 닛테츠 스테인레스 가부시키가이샤 | 페라이트계 스테인리스 강판 및 그 제조 방법 |
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CN111479944A (zh) * | 2017-12-14 | 2020-07-31 | 株式会社Posco | 具有优异的冲击韧性的基于铁素体的不锈钢及其生产方法 |
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EP3859044A4 (en) * | 2018-11-06 | 2021-12-22 | Posco | HOT-ROLLED STEEL SHEET WITH EXCELLENT LOW TEMPERATURE IMPACT RESISTANCE AND PROCESS FOR ITS MANUFACTURING |
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Also Published As
Publication number | Publication date |
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TWI715713B (zh) | 2021-01-11 |
MX2018010953A (es) | 2019-01-21 |
JP6022097B1 (ja) | 2016-11-09 |
TW201734228A (zh) | 2017-10-01 |
KR102672884B1 (ko) | 2024-06-10 |
CN109415783A (zh) | 2019-03-01 |
CN109415783B (zh) | 2021-02-12 |
JP2017179436A (ja) | 2017-10-05 |
EP3438308A1 (en) | 2019-02-06 |
MY189619A (en) | 2022-02-21 |
CA3015441A1 (en) | 2017-10-05 |
EP3438308A4 (en) | 2019-09-25 |
KR20180125584A (ko) | 2018-11-23 |
RU2719968C1 (ru) | 2020-04-23 |
US20190093192A1 (en) | 2019-03-28 |
CA3015441C (en) | 2023-10-03 |
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