WO2006088223A1 - Procédé de fabrication d’une feuille en acier à teneur extrêmement faible en carbone et objet moulé à teneur extrêmement faible en carbone présentant d’excellentes propriétés de surface, d’aptitude au façonnage et d'aptitude au - Google Patents

Procédé de fabrication d’une feuille en acier à teneur extrêmement faible en carbone et objet moulé à teneur extrêmement faible en carbone présentant d’excellentes propriétés de surface, d’aptitude au façonnage et d'aptitude au Download PDF

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Publication number
WO2006088223A1
WO2006088223A1 PCT/JP2006/303201 JP2006303201W WO2006088223A1 WO 2006088223 A1 WO2006088223 A1 WO 2006088223A1 JP 2006303201 W JP2006303201 W JP 2006303201W WO 2006088223 A1 WO2006088223 A1 WO 2006088223A1
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WO
WIPO (PCT)
Prior art keywords
mass
less
steel
molten steel
low carbon
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Application number
PCT/JP2006/303201
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English (en)
Japanese (ja)
Inventor
Katsuhiro Sasai
Wataru Ohashi
Original Assignee
Nippon Steel Corporation
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Filing date
Publication date
Application filed by Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to EP06714341A priority Critical patent/EP1852514B1/fr
Priority to BRPI0607866-4B1A priority patent/BRPI0607866B1/pt
Publication of WO2006088223A1 publication Critical patent/WO2006088223A1/fr
Priority to US13/530,946 priority patent/US20120261085A1/en

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Classifications

    • 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
    • B22D11/114—Treating the molten metal by using agitating or vibrating means
    • B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
    • 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
    • C21C7/0006—Adding metallic additives
    • 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
    • C21C7/06—Deoxidising, e.g. killing
    • 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
    • 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
    • C21C7/10—Handling in a vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper

Definitions

  • the present invention relates to an ultra-low carbon steel plate excellent in surface properties, workability and formability, and a method for producing an ultra-low carbon flake.
  • the molten steel refined in the converter or vacuum processing vessel contains a large amount of dissolved oxygen, and this excess oxygen is deoxidized by A 1, a strong deoxidizing element that has a strong affinity for oxygen. It is common. However, A 1 produces alumina inclusions by deoxidation, which aggregate and coalesce into a coarse alumina cluster. '
  • ultra-low carbon molten steel which is a material for thin steel sheets with a low carbon concentration and a high dissolved oxygen concentration after refinement, has an extremely large amount of aluminum class, and the rate of surface defects is extremely high. Measures to reduce system inclusions are a major issue.
  • Mg deoxidation that does not produce any alumina inclusions as described in Japanese Patent Application Laid-Open No. 5-3020 1 1 2 has a high vapor pressure of Mg and yield to molten steel. Therefore, deoxidation of molten steel with a high dissolved oxygen concentration, such as extremely low carbon steel, with only Mg requires a large amount of Mg, and considering the production cost, what is a practical process? I can not say.
  • the present invention makes it possible to prevent surface flaws by forming finely dispersed oxides during solidification without generating inclusions in the molten steel, and also to improve workability and formability.
  • the purpose is to present an excellent ultra-low carbon steel sheet and its manufacturing method.
  • the present invention has the following configuration.
  • the dissolved oxygen concentration in the molten steel is 0.0 1 mass% or more, 0. 0
  • a method for producing an ultra-low carbon steel slab characterized by forging molten steel adjusted to 6% by mass or less.
  • the dissolved oxygen concentration in the molten steel is 0.0 1 mass% or more, 0
  • the steel contains 4 0 in terms of the number of oxides present in the steel.
  • At least 40% of the number of oxides present in the steel is at least 20% by mass of Si oxide, Mn oxide, and Fe oxide.
  • the ultra-low carbon steel sheet excellent in surface properties, workability and formability according to any one of the above (10) to (12).
  • the oxide can be finely precipitated at the time of solidification with almost no inclusions in the molten steel, so that surface flaws can be reliably prevented and C and N in the steel plate are fixed.
  • scouring is performed in a steelmaking furnace such as a converter or an electric furnace.
  • a steelmaking furnace such as a converter or an electric furnace.
  • Cu, Nb and B are added to the molten steel with a carbon concentration of 0.005 mass% or less by performing vacuum degassing, etc., and the dissolved oxygen concentration is set to 0.0 1 Adjust to 0.06 mass%.
  • This melting method is to reduce the carbon concentration to such an extent that it does not generate CO gas by reacting with oxygen during forging, and with little addition of A 1, leaving a large amount of dissolved oxygen,
  • Cu, Nb, and B, which have very little deoxidation power, are added, and C and N are fixed and the texture is controlled. It is also to ensure quality.
  • the molten steel decarburized in the converter or vacuum processing vessel contains a large amount of dissolved oxygen, and this dissolved oxygen is usually almost deoxidized by the addition of A 1 ([Equation 1] For this reason, a large amount of alumina inclusions are produced.
  • Nb and B are added as elements having extremely weak deoxidizing power so as to hardly deoxidize molten steel even if an amount sufficient to fix N and C is added.
  • Nb works mainly to improve the workability of the steel sheet by fixing C and B mainly fixing N as precipitates.
  • the Rankford value (denoted as r value) is usually extremely low in the Ti addition of A 1 deoxidation. The value is slightly lower than that of carbon steel.
  • the present inventor has examined in detail the additive elements that easily develop the texture of the plate surface orientation ⁇ 1 1 1 ⁇ suitable for improving the r value in the steel sheet. We found that u addition was most effective.
  • the dissolved oxygen concentration is less than 0.01% by mass. If deoxidized until it is lowered, alumina and titania and other inclusions will increase too much and will remain in the molten steel without being lifted off.
  • the dissolved oxygen concentration in the molten steel needs to be not less than 0.01% by mass and not more than 0.06% by mass.
  • the dissolved oxygen concentration in the molten steel can be analyzed by an oxygen sensor using a solid electrolyte, and the C concentration can be analyzed by a molten steel sampling method.
  • Nb mainly fixes C
  • B mainly fixes N as precipitates, thereby improving the workability of the steel sheet.
  • the preferred range of addition of Nb and B to the molten steel can be appropriately expressed by using the middle side of the following formula described using the chemical equivalent of each element as an index.
  • the middle side of [Equation 2] is the free Nb amount that is not carbonized by combining with C
  • the middle side of [Equation 3] is the free that is not nitrided by combining with N. Means the amount of B.
  • the oxygen concentration at equilibrium between Nb and B is 0.01% by mass or more, and dissolved oxygen is added even if Nb and B are added. 0.0 1 mass% or more can be secured.
  • the preferred concentration of Cu added to the molten steel in the molten steel will be explained.
  • Cu has the effect of developing a ⁇ 1 1 1 ⁇ orientation texture in which high r-values are easily obtained in steel sheets, and the effect is difficult to appear unless at least 0.0 1 mass% is added. Therefore, the addition amount is preferably 0.01% by mass or more.
  • the upper limit is preferably set to 3.0% by mass.
  • Ni has the effect of mitigating the deterioration of hot rolled surface properties due to Cu, and is generally added on a mass basis with more than half of Cu as a guide.
  • the steel sheet having a high oxygen concentration according to the present invention when the dissolved oxygen concentration in the molten steel is 0.01 mass% or more, the scale-base metal interface of the hot rolled sheet is smoothed, and the scale peelability is improved. We have found that Cu embrittlement is suppressed.
  • the surface properties of the hot-rolled sheet are good and the characteristics of the present invention can be maximized.However, if necessary, the amount is less than half of Cu. Ni may be added. Originally heat In this steel sheet with good surface properties, the addition of Ni to the conventional Cu-added steel only increases the cost. The upper limit of Ni is 1/2 of the Cu concentration. The following is preferable.
  • the Si concentration in the molten steel is preferably 0.05 mass% or more and 0.03 mass% or less. This is because when the Si concentration is less than 0.05 mass%, the strength of the steel plate is likely to be insufficient, and when the Si concentration exceeds 0.03 mass%, the workability of the steel sheet is lowered.
  • the Si concentration is less than 0.03% by mass, the equilibrium oxygen concentration will also exceed 0.02% by mass, and the dissolved oxygen concentration will exceed 0.02% by mass simply by adjusting the Si concentration. 0.06 mass% or less is possible, and by adding an element with deoxidizing power, the dissolved oxygen concentration in the molten steel is 0.01 mass% or more 0.06 mass% The following can be ensured.
  • the Mn concentration in the molten steel is less than 0.08% by mass, cracks are likely to occur during hot rolling of the slab, and if the Mn concentration exceeds 0.3% by mass, the workability of the steel sheet is increased. descend. For this reason, the Mn concentration in the molten steel is preferably 0.08% by mass or more and 0.3% by mass or less. In addition, since Mn has a very weak deoxidizing power compared to S i, even if the Mn concentration is 0.3% by mass, the equilibrium oxygen concentration is more than 0.1% by mass. By adding elements, the dissolved oxygen concentration in the molten steel can be ensured to be not less than 0.01% by mass and not more than 0.06% by mass.
  • Mn has a very weak deoxidizing power
  • Mn concentration is 0.3% by mass or less, almost no Mn oxide is formed in the equilibrium state, but after the converter is blown or vacuum degassing treatment
  • Mn is added with large block of ferromanganese or manganese ore. Therefore, a region with a high Mn concentration may be locally generated in the molten steel, and a small amount of Mn oxide is generated in that region.
  • inclusions are added to the molten steel. Since it is more preferable not to produce it, it is more preferable to adjust the Mn concentration under operating conditions after the converter blowing or without the addition of Mn after vacuum degassing.
  • Mn is contained in the hot metal, and even without the addition of Mn, it is possible to achieve a Mn concentration of about 0.15 mass% depending on the operating conditions. Therefore, considering the inclusions in addition to the material, a more preferable range of M n concentration is that melting can be performed after converter blowing or without addition of M n after vacuum degassing treatment. 1 5% by weight.
  • a 1 is not added or hardly added in the molten steel so as not to form alumina inclusions that easily aggregate and coalesce.
  • the acid-soluble A 1 concentration of the steel sheet exceeds 0.005 mass%, the alumina inclusion in the steel sheet increases, so the upper limit is 0.05 mass%. It was. Since it is preferable not to add A 1 to the molten steel, of course, the lower limit value of the A 1 concentration includes 0% by mass.
  • the acid-soluble A 1 is the amount of A 1 dissolved in the acid, and usually corresponds to the dissolved A 1 concentration (concentration of A 1 not A 1 20 3 ).
  • T i in the molten steel is effective in improving workability because C and N are fixed as T i N and T i C, but if the amount of T i increases, for example, If the Ti concentration exceeds 0.01% by mass, the equilibrium oxygen concentration will be less than 0.01% by mass. I can't keep it. Therefore, when T i is added in order to further improve the workability, it may be added in a range of not more than 0.01% by mass.
  • a continuous forging machine is equipped with an in-mold electromagnetic stirrer or an electromagnetic coil, and by using these, it is possible to forge without trapping CO bubbles in a piece.
  • the present inventor makes the dissolved oxygen concentration about 0.06% by mass if the molten steel flow rate in the vertical meniscus is about 40 to 100 cm Z s when electromagnetic stirring is performed during solidification. However, it is known that it is more preferable because it can be fabricated with almost no CO bubbles trapped in the pieces.
  • the swirling flow velocity of molten steel by electromagnetic stirring is less than 40 cm Z s, it is difficult to obtain a sufficient C 0 bubble cleaning effect, and when the swirling flow velocity exceeds 100 cm Z s, CO bubbles are washed.
  • the mold powder on the surface of the molten steel is caught and surface defects are likely to occur.
  • the molten steel blown in a converter and decarburized to a C concentration of about 0.05% by mass is decarburized by a vacuum degassing apparatus to a C concentration of about 0.05% by mass.
  • the dissolved oxygen concentration in the molten steel is controlled so as to approach 0.01 to 0.06 mass% after the decarburization is finished in consideration of the decarburization amount.
  • Mn and Si are not added, or as much as possible, Cu, Nb, B, Ni, etc. are added, and the dissolved oxygen concentration in the molten steel is further reduced. If it is necessary to make fine adjustments to the target value, add a small amount of A 1 or Ti at the same time to adjust the ingredients.
  • the molten steel produced in this way is manufactured by continuous forging or continuous forging using electromagnetic stirring.
  • the steel plate of the present invention will be described.
  • a hot-rolled steel sheet obtained by hot rolling a slab produced by the above method, and a steel sheet obtained by processing the slab such as a cold-rolled steel sheet obtained by cold rolling is defined as a steel plate. Therefore, the steel sheet of the present invention contains Cu, Nb and B.
  • Other elements include, for example, S i and M n from the viewpoint of securing strength, a small amount of T i from the viewpoint of securing workability, and further, acid-soluble A 1 of 0.005% by mass or less. You may contain.
  • the C concentration in the molten steel is made very low, dissolved oxygen precipitates as Fe oxide inclusions during forging.
  • the Fe oxide inclusions do not form in the molten steel, but precipitate during solidification, so they are finely dispersed in the flakes without agglomeration.
  • the Fe oxide inclusions include not only pure Fe oxide but also oxide compounded with Si oxide or Mn oxide.
  • the ultra-low carbon steel sheet as in the present invention contains S i, M n, and Fe as oxides.
  • S i, M n, and Fe as oxides.
  • one or more oxides of S i, M n and Fe are included.
  • various oxides such as Mg, Ca, and A1 oxides may be included.
  • fine oxides having a diameter of 0.5 m to 30 m were found to be 10 000 Zcm 2 or more 1 0 0 0 0 0 0 in the steel sheet. Zc m 2 or less are dispersed.In this way, the inclusions are finely dispersed, so that surface defects can be prevented.
  • the diameter of the fine oxide is 0.5 m to 30 m. This is because the size of inclusions in the steel sheet of the present invention is almost within the range of 0.5 m to 30 m, and inclusions with a size of about 30 m can be used. Thus, surface defects can be sufficiently prevented.
  • the inclusion dispersion state is set to 1 0 00 0 cm 2 or more and 1 0 0 0 0 0 0 or less Zcm 2 when the inclusions in the steel sheet in the present invention are within this number density range. Because surface defects do not occur.
  • the polished surface of the steel sheet was observed with an optical microscope at 100 and 100 times, and the inclusion particle size distribution within the unit area was evaluated.
  • the particle size of this inclusion ie, the diameter is measured by measuring the major axis and minor axis,
  • the number of oxides present in the steel sheet is 40% or more, but contains at least S i, M n, and F e, most of the inclusions are formed during solidification, and aggregate coalescence This is preferable because it can be finely dispersed and surface defects are less likely to occur.
  • including at least S i, M n, and F e means one or more of S i, M n, and F e, and is used in the same meaning thereafter.
  • the C concentration should be 0.01% by mass or less, preferably 0.05% by mass or less from the viewpoint of workability. However, since the condition for preventing the generation of C 0 bubbles at the time of solidification is 0.05% by mass or less, the present invention sufficiently satisfies the C concentration determined from the workability conditions.
  • the lower limit of C concentration is not specified.
  • This molten steel was forged into a slab having a thickness of 2500 mm and a width of 180 mm by a continuous forging method.
  • the forged piece was cut into 8500 mm length to make one coil unit.
  • the slab thus obtained was hot-rolled and cold-rolled by a conventional method, and finally formed a cold-rolled steel sheet having a thickness of 0.7 mm and a width of 180 mm coil.
  • visual inspection was performed on the inspection line after cold rolling to evaluate the number of surface defects generated per coil.
  • the workability of the obtained cold-rolled steel sheet was evaluated, and it was a high workability steel sheet with a total elongation of 5 7% and an r value of 2.6.
  • 300 t of molten steel with a C concentration of 0.03 mass% was produced by refinement in a converter and treatment in a reflux vacuum degassing apparatus.
  • this molten steel is slabs with a thickness of 250 mm and a width of 180 mm while electromagnetically stirring the molten steel at the meniscus at an average flow rate of 50 cm / s. Forged.
  • the forged piece was cut into 8500 mm length and made into one coil unit.
  • the slab thus obtained was hot-rolled and cold-rolled by a conventional method, and finally formed a cold-rolled steel plate having a thickness of 0.7 mm and a width of 180 mm.
  • visual inspection was performed on the inspection line after cold rolling to evaluate the number of surface defects generated per coil.
  • the slab thus obtained was hot-rolled and cold-rolled by a conventional method, and finally formed a cold-rolled steel plate having a thickness of 0.7 mm and a width of 180 mm.
  • visual inspection was performed on the inspection line after cold rolling to evaluate the number of surface defects generated per coil.
  • the present invention it is possible to provide an ultra-low carbon thin steel sheet having excellent surface properties, workability, and formability. Therefore, the present invention expands the applications of the thin steel sheet. Industrial applicability is great.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne un procédé de production d’une pièce moulée en acier à teneur extrêmement faible en carbone, caractérisé en qu’il comprend la suppression du carbone dans un acier fondu à une teneur de 0,005 % en masse ou moins, l’ajout de Cu, de Nb et de B à l’acier fondu résultant, et le réglage de la concentration d’oxygène dissous dans l’acier fondu à 0,01 à 0,06 % en masse ; et d’une feuille d’acier à teneur extrêmement faible en carbone, caractérisée en ce qu’elle comprend 0,005 % en masse de C ou moins et 0,005 % en masse ou moins d'Al soluble dans un acide, et qui comprend du Cu, du Nb et du B, et qui comprend en outre de fines particules d'oxyde ayant un diamètre de 0,5 à 30 µm dispersées dans celle-ci, dans une quantité de 1000 à 1 000 000 particules/cm2.
PCT/JP2006/303201 2005-02-18 2006-02-16 Procédé de fabrication d’une feuille en acier à teneur extrêmement faible en carbone et objet moulé à teneur extrêmement faible en carbone présentant d’excellentes propriétés de surface, d’aptitude au façonnage et d'aptitude au WO2006088223A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP06714341A EP1852514B1 (fr) 2005-02-18 2006-02-16 Procédé de fabrication d une feuille en acier à teneur extrêmement faible en carbone et objet moulé à teneur extrêmement faible en carbone présentant d'excellentes propriétés de surface, d'aptitude au façonnage et d'aptitude a la mise en forme
BRPI0607866-4B1A BRPI0607866B1 (pt) 2005-02-18 2006-02-16 Método de produção de uma placa lingotada de aço, bem como chapa de aço
US13/530,946 US20120261085A1 (en) 2005-02-18 2012-06-22 Extremely low carbon steel plate excellent in surface characteristics, workability, and formability and a method of producing extremely low carbon cast slab

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2005-041893 2005-02-18
JP2005041893 2005-02-18
JP2005-300096 2005-10-14
JP2005300096A JP4873921B2 (ja) 2005-02-18 2005-10-14 表面性状、加工性および成形性に優れた極低炭素鋼板および極低炭素鋳片の製造方法

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WO2006088223A1 true WO2006088223A1 (fr) 2006-08-24

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BR (1) BRPI0607866B1 (fr)
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CN102575308A (zh) * 2009-07-30 2012-07-11 塔塔钢铁艾默伊登有限责任公司 生产超低碳钢板坯、带材或片材的过程
JP5458779B2 (ja) * 2009-09-29 2014-04-02 Ｊｆｅスチール株式会社 鋼鋳片の連続鋳造方法
EP2546008B1 (fr) * 2010-03-10 2016-03-09 JFE Steel Corporation Procédé de coulée continue d'acier et procédé de fabrication d'une plaque d'acier
WO2012104306A1 (fr) * 2011-01-31 2012-08-09 Tata Steel Ijmuiden Bv Procédé de fabrication d'acier à résistance élevée et acier fabriqué au moyen dudit procédé
CN104294150B (zh) * 2014-10-30 2016-05-18 武汉钢铁(集团)公司 屏蔽线用钢及其生产方法

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KR20070094859A (ko) 2007-09-21
EP1852514B1 (fr) 2012-08-08
JP4873921B2 (ja) 2012-02-08
KR100886046B1 (ko) 2009-02-26
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US20120261085A1 (en) 2012-10-18
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