WO2022009849A1 - 極低炭素鋼製品の製造方法 - Google Patents

極低炭素鋼製品の製造方法 Download PDF

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Publication number
WO2022009849A1
WO2022009849A1 PCT/JP2021/025374 JP2021025374W WO2022009849A1 WO 2022009849 A1 WO2022009849 A1 WO 2022009849A1 JP 2021025374 W JP2021025374 W JP 2021025374W WO 2022009849 A1 WO2022009849 A1 WO 2022009849A1
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Prior art keywords
slab
hot
rolling
ultra
low carbon
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PCT/JP2021/025374
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English (en)
French (fr)
Japanese (ja)
Inventor
佳祐 佐野
正敏 石割
勝 三宅
健二 鼓
Original Assignee
Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to CN202180047165.2A priority Critical patent/CN115803126A/zh
Priority to JP2022535325A priority patent/JP7452656B2/ja
Priority to EP21837995.6A priority patent/EP4151755A4/en
Priority to US18/013,326 priority patent/US20230287543A1/en
Priority to KR1020237000489A priority patent/KR20230022213A/ko
Publication of WO2022009849A1 publication Critical patent/WO2022009849A1/ja

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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
    • C21D8/0221—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
    • 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
    • B21B1/02—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 heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
    • B22D1/002—Treatment with gases
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/116—Refining the metal
    • B22D11/117—Refining the metal by treating with gases
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/128—Accessories for subsequent treating or working cast stock in situ for removing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/068—Decarburising
    • 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
    • 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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to a method for manufacturing an ultra-low carbon steel product having few blister defects.
  • the blister defect in a cold-rolled steel sheet is that hydrogen that has entered the steel sheet during pickling after hot rolling stays in bubbles in the steel sheet and is annealed after cold rolling. It is a puffy surface defect that expands in volume with heating and deforms the surface of the steel sheet softened by heating due to the increased pressure.
  • Patent Document 1 As a technique for suppressing the generation of such blister, in Patent Document 1, a molten steel discharge hole is positioned between a mold having an upper magnetic pole and a lower magnetic pole and a peak position of a magnetic field due to the upper magnetic pole and the lower magnetic pole. It is disclosed that by casting a slab while controlling the molten steel flow by using a continuous casting machine having a nozzle, it is possible to suppress the trapping of air bubbles in the solidified shell, thereby suppressing the generation of blister. ..
  • Patent Document 1 is mainly a technique for suppressing bubbles that cause blister defects from being trapped in the solidified shell at the casting stage.
  • an inert gas is introduced into the immersion nozzle to prevent non-metal inclusions such as alumina from adhering to the inner wall surface of the immersion nozzle, ensuring that air bubbles are trapped in the solidified shell. It is difficult to prevent. Therefore, even if air bubbles are trapped in the solidified shell, there is a problem that a method capable of suppressing the occurrence of blister defects in the subsequent steps after the hot rolling step is required.
  • the present invention has been made in view of such a situation of the prior art, and an object thereof is to prevent blister defects in the steps after the hot rolling step even if bubbles are trapped in the solidified shell. It is to provide a method for manufacturing an ultra-low carbon steel product that can suppress the occurrence.
  • the gist of the present invention for solving the above problems is as follows.
  • a method for producing an ultra-low carbon steel product having a carbon concentration of 0.005% by mass or less which comprises a cold-rolling step of cold-rolling the hot-rolled steel sheet to obtain a cold-rolled steel sheet.
  • the rolling step a method for producing an ultra-low carbon steel product, which is cold-rolled at a reduction rate predetermined according to the thickness of the hot-rolled steel sheet.
  • FIG. 1 is a graph showing the relationship between the amount of width reduction and the occurrence rate of blister defects.
  • FIG. 2 is a graph showing the relationship between the rolling reduction rate of cold rolling and the occurrence rate of blister defects.
  • the blister defect is caused by the hydrogen that has entered the steel sheet during pickling after hot rolling, staying in a part such as air bubbles in the steel sheet, and expanding in volume with heating during annealing after cold rolling. It is generated by deforming the surface of the steel sheet softened by heating due to the increased pressure.
  • the present inventors include the slab subjected to hot rolling by rolling down the slab by a predetermined rolling amount according to the size (dimension) of the slab width in the direction orthogonal to the rolling direction of the slab. The present invention was completed by finding that the generation of blister defects can be suppressed by deforming the bubbles.
  • the present invention will be described through embodiments of the present invention.
  • the method for manufacturing an ultra-low carbon steel product according to the present embodiment is at least a refining step of adjusting the carbon concentration of molten iron to make molten steel, a casting step of casting molten steel into a slab, and rolling down the slab. It has a width reduction step and a hot rolling step of hot rolling the width reduced slab. Further, after the hot rolling step, there may be a cold rolling step of cold rolling the hot rolled steel sheet.
  • the molten steel of ultra-low carbon steel is melted by degassing and decarburizing the molten steel that has been subjected to the primary refining treatment in advance in a refining device such as a converter, using a degassing device such as the RH method. Will be done.
  • the process including these treatments is an example of a refining process in which the carbon concentration of molten iron is adjusted to form molten steel.
  • molten steel of ultra-low carbon steel having a carbon concentration of 0.005% by mass or less is melted.
  • the molten steel of ultra-low carbon steel is continuously cast into a slab using a continuous casting machine equipped with a tundish, a mold, a foot roll, a guide roll, a pinch roll, a secondary cooling device, and the like.
  • the process of continuously casting from molten steel to a slab using this continuous casting machine is an example of a casting process of casting molten steel into a slab.
  • the slab is hot-rolled to form a hot-rolled steel sheet, and the hot-rolled steel sheet is pickled to manufacture a hot-rolled steel sheet.
  • the hot-rolled steel sheet may be further cold-rolled, tempered, or the like to be a cold-rolled steel sheet, and further, the cold-rolled steel sheet may be subjected to an alloyed hot-dip galvanized steel sheet to be an alloyed hot-dip galvanized steel sheet. good.
  • the process of hot-rolling a slab including this pickling treatment to make a hot-rolled steel plate is an example of a hot-rolling process of hot-rolling a slab, and the hot-rolled steel plate is cold-rolled, annealed, or the like to be cold-rolled.
  • the process of forming rolled steel sheets is an example of a cold rolling process in which hot-rolled slabs are cold-rolled.
  • the molten steel in the tundish is poured into the mold through the dipping nozzle.
  • the ultra-low carbon steel having a carbon concentration of 0.005% by mass or less contains alumina generated in the process of decarburization / deoxidation treatment by the RH degassing device.
  • the molten steel is injected from the tundish into the mold from the inner wall surface of the immersion nozzle to the inside of the nozzle.
  • An inert gas such as Ar gas is blown into the gas. The bubbles of the inert gas are discharged into the mold together with the molten steel from the molten steel discharge hole of the immersion nozzle.
  • the slab containing the bubbles is cast.
  • the slab containing the bubbles is regarded as a hot-rolled steel sheet, and when the hot-rolled steel sheet is pickled, hydrogen stays in the bubbles and the volume expands with heating during annealing after cold rolling, thereby increasing the volume. Blister defects occur by deforming the surface of the steel sheet softened by heating due to pressure.
  • the slab to be subjected to hot rolling is preliminarily prepared according to the slab width in the direction orthogonal to the rolling direction of the slab. It further has a width rolling step of rolling down by a predetermined rolling amount. Specifically, a sizing press is used to reduce the width of the slab to be subjected to hot rolling. This makes it possible to suppress the occurrence of blister defects that occur during annealing after cold rolling.
  • the swelling amount ( ⁇ ) of the bubbles is expressed by the following formula (1) using the beam calculation formula in which both ends are supported.
  • ⁇ WL 2 /384EI ... (1)
  • ⁇ is the amount of swelling (m)
  • W is the stress (N)
  • L is the bubble width (m)
  • E is Young's modulus (MPa)
  • I is the moment of inertia of area. The next moment (m 4 ).
  • L in the above equation (1) becomes smaller.
  • the amount of swelling ( ⁇ ) at the center of the beam also becomes smaller, and it is considered that this effect suppresses the swelling of bubbles, thereby suppressing the generation of blister defects.
  • Slabs having a width dimension of 1100 to 2100 mm were reduced in width by 500 tons or more by changing the amount of reduction by a sizing press. These width-rolled slabs are hot-rolled to form hot-rolled steel sheets (plate thickness 2.6-4.0 mm), pickled with hydrochloric acid, and then with a constant rolling ratio (0.72-0.76). ) To cold-roll to make a cold-rolled steel sheet. The obtained cold-rolled steel sheet was subjected to alloying hot-dip galvanizing treatment, and the surface defects of this alloyed hot-dip galvanized steel sheet were continuously measured by an online surface defect meter.
  • This surface defect is visually confirmed by visual inspection, SEM analysis, ICP analysis, etc. to see if the surface defect is a blister defect, and 100 is added to the value obtained by dividing the coil mass in which the blister defect occurs by the total coil mass. Multiply to calculate the incidence of blister defects.
  • the rolling reduction of cold rolling was calculated by the following equation (2).
  • Reduction rate (steel plate thickness at cold pressure inlet-steel plate thickness at cold pressure outlet) / steel plate thickness at cold pressure inlet ...
  • the standard values of the component concentration are C concentration: 0.0000 to 0.0020, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.10 to 0.25.
  • Ultra-low carbon steel 1 having a mass%, P concentration: 0.010 to 0.020 mass%, S concentration: 0.003 to 0.010 mass%, N concentration: 0.0000 to 0.0035 mass%, and The standard values of the component concentration are C concentration: 0.0000 to 0.0015, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.05 to 0.18% by mass, P concentration: 0.000.
  • FIG. 1 is a graph showing the relationship between the amount of width reduction by the sizing press and the occurrence rate of blister defects.
  • the horizontal axis is the width reduction amount (mm) of the slab
  • the vertical axis is the occurrence rate (%) of blister defects.
  • the occurrence rate of blister defects increased slightly, but by increasing the width reduction amount of the slab as a whole, the occurrence rate of blister defects increased. It can be seen that it tends to be lower. From this result, it can be seen that the occurrence of blister defects can be suppressed by rolling down the slab to be subjected to hot rolling with a predetermined rolling reduction amount according to the slab width in the direction orthogonal to the rolling direction of the slab.
  • the width reduction amount according to the slab width is determined in advance by grasping the relationship between the width reduction amount shown in FIG. 1 and the occurrence rate of blister defects by experiments or the like. That is, in the example shown in FIG. 1, for a slab having a width dimension of 1100 to 2100 mm, the width reduction may be performed by a sizing press with a reduction amount of 200 to 250 mm or more, whereby the occurrence rate of blister defects may be performed. It can be seen that can be greatly reduced.
  • cold rolling may be performed at a reduction ratio predetermined according to the plate thickness of the hot-rolled steel sheet.
  • a reduction ratio predetermined according to the plate thickness of the hot-rolled steel sheet.
  • a slab that has been sizing-pressed with a constant width reduction amount (0 to 100 mm) is hot-rolled to form a hot-rolled steel sheet (plate thickness 2.6 to 4.0 mm), pickled with hydrochloric acid, and then reduced.
  • Cold-rolled steel sheets with different rolling ratios were produced by cold rolling at different rates to produce 200 tons or more of cold-rolled steel sheets having different rolling ratios.
  • Each of the obtained cold-rolled steel sheets was subjected to an alloyed hot-dip galvanized treatment, and the surface defects of the alloyed hot-dip galvanized steel sheets were continuously measured by an online surface defect meter. It was confirmed whether or not the surface defect was a blister defect by using visual inspection, SEM analysis, ICP analysis, etc., and the occurrence rate of the blister defect was calculated.
  • FIG. 2 is a graph showing the relationship between the rolling reduction rate of cold rolling and the occurrence rate of blister defects.
  • the horizontal axis is the cold reduction rate ( ⁇ )
  • the vertical axis is the blister defect occurrence rate (%).
  • the rolling reduction rate of cold rolling also correlates with the occurrence rate of blister defects, and that the occurrence rate of blister defects tends to decrease by increasing the rolling reduction rate of cold rolling.
  • cold rolling may be performed at a reduction rate predetermined according to the plate thickness of the hot-rolled steel sheet, thereby causing blister defects. It turns out that it can be suppressed.
  • the reduction rate according to the thickness of the hot-rolled steel sheet is determined in advance by grasping the relationship between the reduction rate of cold rolling shown in FIG. 2 and the occurrence rate of blister defects by experiments or the like. That is, in the example shown in FIG. 2, a hot-rolled steel sheet having a thickness of 2.6 to 4.0 mm may be cold-rolled at a reduction rate of 0.76 or more, whereby blister is generated. It can be seen that the rate can be greatly reduced.
  • the mechanism for suppressing the generation of blister defects due to the width reduction of the slab is different from the mechanism for suppressing the generation of blister defects due to cold rolling. ..
  • the slabs that have been subjected to the width reduction with a plurality of different reduction amounts are prepared, and the cold reduction ratio of the hot-rolled steel sheet manufactured from the slab is prepared.
  • the amount of reduction in width reduction according to the size of the slab width and the reduction rate of cold rolling according to the thickness of the hot-rolled steel sheet. can be predetermined.
  • the ultra-low carbon steel product manufactured by the method for producing an ultra-low carbon steel product according to the present embodiment has an extremely low carbon content of 0.005% by mass or less when the occurrence of blister defects is suppressed by reducing the width.
  • the ultra-low carbon steel slab may be a cold-rolled steel sheet that has been hot-rolled, pickled, and cold-rolled. It may be.
  • the method for producing ultra-low carbon steel according to the present embodiment is not limited to the ultra-low carbon steels 1 and 2 described above, and the standard value of the component concentration is C concentration: 0.0000 to 0.0030, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.10 to 0.25% by mass, P concentration: 0.015 to 0.030% by mass, S concentration: 0.005 to 0.012% by mass, N Ultra-low carbon steel 3 having a concentration of 0.0000 to 0.0035% by mass, standard values of component concentration of C concentration: 0.0000 to 0.0020, Si concentration: 0.00 to 0.04% by mass, Mn concentration: 0.10 to 0.25% by mass, P concentration: 0.000 to 0.010% by mass, S concentration: 0.004 to 0.012% by mass, N concentration: 0.0000 to 0.0030% by mass It can also be applied to the ultra-low carbon steel 4 which is%.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)
PCT/JP2021/025374 2020-07-08 2021-07-05 極低炭素鋼製品の製造方法 WO2022009849A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CN202180047165.2A CN115803126A (zh) 2020-07-08 2021-07-05 极低碳钢制品的制造方法
JP2022535325A JP7452656B2 (ja) 2020-07-08 2021-07-05 極低炭素鋼製品の製造方法
EP21837995.6A EP4151755A4 (en) 2020-07-08 2021-07-05 METHOD FOR PRODUCING AN EXTREMELY LOW CARBON STEEL PRODUCT
US18/013,326 US20230287543A1 (en) 2020-07-08 2021-07-05 Method for producing ultra-low carbon steel product
KR1020237000489A KR20230022213A (ko) 2020-07-08 2021-07-05 극저탄소강 제품의 제조 방법

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2020-117921 2020-07-08
JP2020117921 2020-07-08

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WO2022009849A1 true WO2022009849A1 (ja) 2022-01-13

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US (1) US20230287543A1 (enrdf_load_stackoverflow)
EP (1) EP4151755A4 (enrdf_load_stackoverflow)
JP (1) JP7452656B2 (enrdf_load_stackoverflow)
KR (1) KR20230022213A (enrdf_load_stackoverflow)
CN (1) CN115803126A (enrdf_load_stackoverflow)
TW (1) TWI778702B (enrdf_load_stackoverflow)
WO (1) WO2022009849A1 (enrdf_load_stackoverflow)

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS563413B2 (enrdf_load_stackoverflow) * 1974-10-26 1981-01-24
JPS632504A (ja) * 1986-06-20 1988-01-07 Furukawa Alum Co Ltd アルムニウム合金板の圧延方法
JP2001137905A (ja) * 1999-11-15 2001-05-22 Nippon Steel Corp 清浄性の優れた鋼の製造方法
JP2011206846A (ja) 2010-03-10 2011-10-20 Jfe Steel Corp 鋼板の製造方法

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6082616A (ja) * 1983-10-13 1985-05-10 Kawasaki Steel Corp 極低炭素深絞り用冷延鋼板の製造方法
JP2602699B2 (ja) * 1988-09-07 1997-04-23 日新製鋼株式会社 極低炭素Ｔｉキルド冷延鋼板のフクレ疵の防止方法
JPH0826412B2 (ja) * 1991-01-23 1996-03-13 日本鋼管株式会社 プレス成形性に優れた高強度冷延鋼板の製造方法
JP3377825B2 (ja) * 1992-04-06 2003-02-17 川崎製鉄株式会社 缶用鋼板およびその製造方法
JP2689845B2 (ja) * 1993-03-09 1997-12-10 住友金属工業株式会社 熱延鋼材の脱スケーリング方法
KR960006036B1 (ko) * 1993-12-24 1996-05-08 포항종합제철주식회사 기포결함 발생이 없는 고성형용 법랑용 강판의 제조방법
JP3422612B2 (ja) * 1996-01-19 2003-06-30 Ｊｆｅスチール株式会社 極低炭素冷延鋼板の製造方法
JPH1046241A (ja) * 1996-07-26 1998-02-17 Kawasaki Steel Corp 極低炭素冷延鋼板の製造方法
JP3546605B2 (ja) * 1996-07-29 2004-07-28 Ｊｆｅスチール株式会社 缶用鋼板の製造方法
JP3353688B2 (ja) * 1998-02-24 2002-12-03 住友金属工業株式会社 ほうろう用冷延鋼板とその製造方法
JP2001279331A (ja) * 2000-03-30 2001-10-10 Kawasaki Steel Corp 耐フクレ欠陥特性に優れたほうろう用冷延鋼板の製造方法
CN101120104A (zh) * 2005-02-18 2008-02-06 新日本制铁株式会社 表面性状、加工性和成形性优良的极低碳钢板以及极低碳铸片的制造方法
WO2008108363A1 (ja) * 2007-03-05 2008-09-12 Sumitomo Metal Industries, Ltd. 冷間圧延鋼板および合金化溶融亜鉛めっき鋼板ならびにそれらの製造方法
WO2014057519A1 (ja) * 2012-10-11 2014-04-17 Ｊｆｅスチール株式会社 形状凍結性に優れた冷延鋼板およびその製造方法
TWI504760B (zh) * 2012-11-07 2015-10-21 Jfe Steel Corp 三件式罐用鋼板及其製造方法
KR102267129B1 (ko) * 2016-02-02 2021-06-18 닛테츠 스테인레스 가부시키가이샤 Nb함유 페라이트계 스테인리스 열연 강판 및 그 제조 방법과, Nb함유 페라이트계 스테인리스 냉연 강판 및 그 제조 방법

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS563413B2 (enrdf_load_stackoverflow) * 1974-10-26 1981-01-24
JPS632504A (ja) * 1986-06-20 1988-01-07 Furukawa Alum Co Ltd アルムニウム合金板の圧延方法
JP2001137905A (ja) * 1999-11-15 2001-05-22 Nippon Steel Corp 清浄性の優れた鋼の製造方法
JP2011206846A (ja) 2010-03-10 2011-10-20 Jfe Steel Corp 鋼板の製造方法

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
MASAMICHI KOWAKA: "Metal Corrosion Damage and Corrosion Protection Technology", 1983, AGUNE INC., pages: 207
See also references of EP4151755A4

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