WO2009125876A1 - Tôle d'acier à haute résistance pour conteneurs et procédé pour sa production - Google Patents

Tôle d'acier à haute résistance pour conteneurs et procédé pour sa production Download PDF

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Publication number
WO2009125876A1
WO2009125876A1 PCT/JP2009/057717 JP2009057717W WO2009125876A1 WO 2009125876 A1 WO2009125876 A1 WO 2009125876A1 JP 2009057717 W JP2009057717 W JP 2009057717W WO 2009125876 A1 WO2009125876 A1 WO 2009125876A1
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WIPO (PCT)
Prior art keywords
less
rolling
strength
cold rolling
steel
Prior art date
Application number
PCT/JP2009/057717
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English (en)
Japanese (ja)
Inventor
加藤寿勝
荒谷誠
河村勝人
小島克己
佐藤覚
筋田成子
青木文男
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
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 US12/936,681 priority Critical patent/US20110168303A1/en
Priority to KR1020137017399A priority patent/KR20130083487A/ko
Priority to CN2009801127859A priority patent/CN101999009B/zh
Priority to BRPI0909012A priority patent/BRPI0909012A2/pt
Publication of WO2009125876A1 publication Critical patent/WO2009125876A1/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/001—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
    • C22C38/02—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a method of manufacturing a steel plate for a high-strength container suitable as a container material for reducing or expanding the diameter shape after three-piece processing such as welding or two-piece processing such as DI. .
  • Patent Document 1 after controlling the components in the steel within a certain range, after the hot rolling is finished (at the Ar 3 transformation point—30), and then pickling and cold rolling are performed.
  • a method of secondary annealing by performing continuous annealing has been proposed.
  • Patent Document 1 P is set to 0.02 wt% or less so as not to deteriorate the flange workability, neck workability, and corrosion resistance, and the reduction ratio of the secondary cold rolling is 15 to 30%. Therefore, it is difficult to efficiently process thin products and it is difficult to produce them, and there is a problem that appearance defects are likely to occur. In addition, cracks may occur on the surface of the slab, causing problems when yields are reduced in the product. In addition, it is difficult to manufacture stably, and improvement is necessary.
  • the following method has been proposed as a typical method for producing a hard container steel plate, which is appropriately selected according to the type of annealing (for example, Non-Patent Document 1).
  • BAF Cold Rolling ⁇ Cold Rolling ⁇ Box Annealing
  • CAL Cold Rolling
  • the above method uses various rolling oils with high viscosity for the purpose of improving lubricity during rolling. There is a problem of poor appearance after rolling. Furthermore, when the rolling reduction ratio is high, the steel sheet is stretched by rolling, so the difference in resistance between the width direction of the copper sheet and the rolling direction increases.
  • Patent Document 1 Japanese Patent No. 3108615-Non-Patent Document 1 “Technology History of Surface-treated Steel Sheets for Cans in Japan” issued by the Japan Iron and Copper Association October 30, 2010 p. 188
  • the present invention has been made in view of such circumstances.
  • the tensile strength TS has a strength of 50 OMPa or more, and the difference in resistance between the sheet width direction and the rolling direction is 2 OMPa or less. Furthermore, it aims at providing the steel plate for containers excellent in workability, and its manufacturing method. DISCLOSURE OF THE INVENTION The present inventors have intensively studied to solve the above problems. As a result, the following knowledge was obtained.
  • a steel sheet for high-strength cans has been completed by managing components based on the above knowledge.
  • the present invention has been made based on the above findings, and the gist thereof is as follows.
  • the “high-strength steel plate for containers” is a steel plate for containers having a tensile strength T S (hereinafter, sometimes simply referred to as T S) of 500 MPa or more.
  • the steel plate for high-strength containers of the present invention is intended for container materials and can materials. Regardless of the presence or absence of surface treatment, tin plating, nickel tin plating, chromium plating (so-called tin-free plating), or organic coatings can be applied for a wide range of applications. .
  • the thickness of the plate is not particularly limited, but from the viewpoint of obtaining the effect by making the best use of the present invention, a thickness of 0.3 mm or less and further 0.20 mm or less are preferable. Particularly preferred is 0.170 mm or less.
  • Ding 3 is 5 0 0? & Above, steel sheet for high-strength containers with a difference in resistance between the sheet width direction and the rolling direction of 2 OMPa or less.
  • the P content is adjusted, and the rolling reduction in the second cold rolling (hereinafter sometimes referred to as secondary cold rolling) is set to 20 to 50%.
  • secondary cold rolling is set to 20 to 50%.
  • a high-strength steel sheet for containers can be provided.
  • the component composition of the steel plate for containers according to the present invention will be described.
  • C is set to 0.05% or less.
  • C is 0.01% or more.
  • it is 0.02 or more and 0.04% or less, More preferably, it is 0.02 or more and 0.03% or less.
  • Si should be 0.043 ⁇ 4 or less.
  • ⁇ is an effective element to prevent hot cracking due to S. Further, the effect of preventing cracking is obtained by adding according to the amount of S. It also has the effect of refining crystal grains. In order to exert these effects, it is necessary to add at least 0.1% of Mn. On the other hand, if added in a large amount, the corrosion resistance tends to deteriorate, and the steel plate is hardened more than necessary, and the flange workability and neck workability are deteriorated. Therefore, the upper limit is set to 1.2%. It is preferable to be 35% or less.
  • P is a component that hardens the steel, and in the present invention, P contains a predetermined amount according to the required strength. If it is less than 0.000 to 0%, a TS of 500 MPa or more cannot be obtained. On the other hand, including an excessive amount of P component more than necessary degrades the corrosion resistance. It also degrades the flange workability and neck workability. Since these become prominent when they exceed 0.100%, the upper limit is set to 0.100%. It is preferable that the range is from 0.0020 to 0.020% because a higher strength can be obtained by an appropriate strength by adding P and the effect of secondary cold rolling described later.
  • S exists as an inclusion in steel and is an element that reduces the ductility of the steel sheet and further degrades the corrosion resistance. Therefore, it should be 0.10 or less. Preferably it is 0.030% or less.
  • A1 is an element necessary for steel deoxidation. If the amount is less than 0.001%, deoxidation becomes insufficient, and the flange workability deteriorates due to inclusions, leading to deterioration of neck workability. Therefore, 0.001% That's it.
  • A1 combines with the N component to reduce the solute N, but if the solid N is excessively reduced, the required strength cannot be obtained. Therefore, it is set to 0.100% or less. It is preferable that the content be 0.03 to 0.075%.
  • N is an element useful for increasing the strength without increasing the hardness of the weld.
  • the content is 0.10% or less. It is preferable that the content be 0.05% or less. Further, from the viewpoint of preventing slab cracking, it is more preferably less than 0.01%. Even more preferable is 0.005% or less. As described above, by reducing N, slab cracking can be reduced, and the yield can be improved without the need for slab maintenance.
  • the balance is Fe and inevitable impurities.
  • the balance other than the above components is Fe and inevitable impurities.
  • an inevitable impurity for example, Sn: 0.01% or less is acceptable.
  • the steel plate for containers of the present invention has the above composition, has a TS of 50 OM Pa or more, and has a resistance difference between the plate width direction and the rolling direction of 2 OM Pa or less.
  • a TS of 500 MPa or more the rigidity does not decrease even if the plate thickness is reduced.
  • the difference in resistance between the sheet width direction and the rolling direction is 2 OMPa or less, no cracking occurs during flange processing or necking processing.
  • the molten steel having the above composition is melted by a generally known melting method using a converter or the like, and then a rolled material (slab) is formed by a generally known forging method such as a continuous forging method. Next, these rolled materials are used to form hot rolled sheets by hot rolling.
  • the slab extraction temperature of the slab is 1050 ⁇ or higher, a sufficiently high hot rolling end temperature can be secured in the hot rolling of the next process.
  • the slab extraction temperature is preferably 1050 ° C or higher and 1300 ° C or lower.
  • Hot rolling end temperature (Ar 3 transformation point temperature-30) or more Hot rolling end temperature is used to improve the cold rolling property and product characteristics of the subsequent process.
  • the shape of the hot-rolled sheet deteriorates, causing problems in pickling and cold rolling operations in the next process.
  • aluminum nitride will precipitate at the stage of hot-rolled base metal, making it impossible to secure sufficient solute N for strengthening.
  • a structure in which carbide aggregates is formed in the hot-rolled mother plate, and the effect of uniform precipitation of carbide due to overaging described later cannot be obtained.
  • this adversely affects the corrosion resistance of the steel plate.
  • the pickling performance deteriorates as the scale thickness generated on the steel sheet surface increases. In order to avoid these problems, it is necessary to set the temperature to 750 "C or less.
  • the hot-rolled sheet manufactured in this way is pickled and cold-rolled to form a cold-rolled sheet.
  • the surface scale can be removed with an acid such as hydrochloric acid or sulfuric acid.
  • the rolling reduction is less than 80%, it may not be possible to obtain a sufficiently fine structure after annealing, so 80% or more is preferable.
  • the rolling reduction is more preferably 85% or more.
  • the upper limit of the rolling reduction is not particularly required, and is set as appropriate in consideration of the capacity of equipment lines for hot rolling and cold rolling.
  • Annealing temperature Recrystallization temperature below 800 ° C (preferred conditions) If an unrecrystallized structure remains in the steel sheet, it may cause formability failure during can making, poor appearance, etc., so it is necessary to perform recrystallization treatment by continuous annealing. However, if the annealing temperature is excessively increased, defects such as heat buckles and plate breakage occur during continuous annealing. In addition, abnormal crystal grain growth increases the risk of deteriorating appearance characteristics. Therefore, the annealing temperature is 800, and it is preferable to carry out in the following recrystallization temperature range.
  • a soaking time equivalent to 5 s or more and 60 s or less is sufficient.
  • a soaking time of 5 s or longer is preferable because precipitation of carbides that can disperse stress during processing becomes sufficient. .
  • the difference in yield strength between the sheet width direction and the rolling direction is 2 OMPa or less. It becomes possible.
  • the density and ratio of carbides having a particle size of 1.5 im or less and a particle size of 1.5 to more than 111 / 3.0 or less can be set within a preferable range described later. .
  • Second cold rolling reduction 20-50% (preferably 20-30%)
  • the second cold rolling after continuous annealing (hereinafter sometimes referred to as secondary cold rolling) is necessary to ensure the pressure resistance of the welded can, that is, the yield strength of the steel sheet.
  • the reduction ratio of secondary cold rolling is required to be at least 20%.
  • the rolling reduction exceeds 50%, the material property anisotropy increases, and the difference in resistance between the sheet width direction and the rolling (rolling) direction exceeds 2 OMPa.
  • the flange formability and neck workability of the new plate removal method (a plate removal method in which the rolling direction of the steel plate is parallel to the axial direction of the can body) are significantly deteriorated.
  • the content is preferably 20% or more and 30% or less, but may be appropriately selected according to the P content and the intended steel sheet strength. Specifically, when the P content is as high as more than 0.020% and not more than 0.100%, a relatively low rolling reduction is preferable.
  • a plated layer can be formed on the surface of the cold-rolled steel sheet (at least one side) to obtain a plated steel sheet.
  • the adhesion layer formed on the surface any of those applied to steel plates for containers can be applied.
  • the plating layer include tin plating, chromium plating, nickel plating, nickel plating and chromium plating.
  • Tables 2 and 3 show the overaging treatment conditions and the secondary cold rolling reduction ratio.
  • the steel sheet obtained as described above was subjected to structure observation by the following method to determine the density and ratio of the carbide particle size. The following tests were conducted to evaluate the characteristics.
  • the cold-rolled steel sheet obtained as described above was embedded in a single-climate resin and the cross section was polished. Next, after being used as a corrosive solution, a soda picrate soda solution prepared by mixing picric acid and sodium hydroxide was used and immersed in the corrosive solution at 80 seconds for 6 seconds. Next, the carbides were observed in three fields of view (in the range of about 0.1375mm x 0.1375mm) with a 400x optical microscope.
  • the number of carbide particles having a particle size of 1.5 / m or less, a particle size of 1.5 ⁇ or more, 3.0 ⁇ or less, and a particle size of more than 3.0 // m was determined, and the average value of the density and ratio of the three fields was determined.
  • the particle diameter of the carbide is set to the minimum diameter.
  • the minimum diameter is set as the particle diameter in the present invention.
  • Nos. 8 to 10 as examples of the present invention 10 and 13 to 1; 18 and 26 to 28 and 31 to 36 have sufficient strength, and the width direction of the plate
  • the difference in resistance in the rolling direction is 2 OMPa or less, and, for example, the performance required for 3-piece processing has been sufficiently achieved.
  • it has an excellent appearance and no neck wrinkles or flange cracks are observed.
  • the workability is further improved in Nos. 8 to 10, Nos. 13 to 15, 26 to 28, and 31 to 3 in which the density and ratio of the carbides are in a suitable range.
  • Nos. 1, 2, 19, and 20 in the comparative examples in which overaging treatment is not performed have a low rolling reduction in secondary cold rolling and cannot provide strength.
  • Nos. 3-5 and 2 1-23 have a secondary cold rolling reduction ratio of 20% or more and high strength, but the difference in resistance between the L and C directions exceeds 2 OMPa, resulting in neck wrinkles. And the occurrence of flange cracks is remarkable. In addition, appearance defects have occurred.
  • No. 6, 7, 11 1, 12, 24, 25, 29, 30 with a rolling reduction of secondary cold rolling of less than 20% cannot obtain strength.
  • the steel sheet for high-strength containers according to the present invention has a density of carbides with a particle size of 1.5 m or less of 102 ⁇ m 2 and a particle size of 1.5 / zm or more and a carbide of 3.0 / im or less. it is preferred density of 63 ZlOOOO / zm 2 greater. Furthermore, the ratio of the number of carbides with a particle size of 1.5 / xm or less to the total number of carbides is more than 52%, and the ratio of the number of carbides with a particle size of 3.0 / zm or less to the total number of carbides is more than 85%. Is more preferable.
  • the density of carbides with a particle size of 1.5 / zm or less is 102 10000; more than zm 2 and the density of carbides with a particle size of more than 1.5 and 3.0 m or less is 63 / 10,000 m 2.
  • a sufficient amount of carbides functioning as a dispersion site can be secured, and workability will be further improved.
  • the density of carbides with a particle size of 1.5 ⁇ or less is 130/10000 ⁇ 2 or more, and the density of carbides with a particle size of more than 1.5 ⁇ of 3.0 ⁇ m or less is 80 or more and 10000 ⁇ m 2 .
  • the ratio of the number of carbides with a particle size of 1.5 / zm or less to the total number of carbides is more than 52%, and the ratio of the number of carbides with a particle size of 3.0 xm or less to the total number of carbides is If it exceeds 85%, the effect of the carbide functioning as a stress dispersion site is further enhanced, and the workability is further improved. More preferably, the ratio of the number of carbides having a particle size of 1.5 m or less to the total number of carbides is 55% or more, and the ratio of the number of carbides having a particle size of 3.0 ⁇ m or less to the total number of carbides is 90%. That's it.
  • the density and ratio of the carbides can be controlled by annealing the copper sheet after cold rolling under predetermined conditions. Specifically, in the continuous annealing process after cold rolling, an overaging treatment is performed by adjusting the thermal history of the steel sheet within a predetermined range.
  • Table 3 is an example in which the N content is 0.0055% and 0.0039% and the preferable range is less than 0.01%. From Table 3, it can be seen that when the N content is less than 0.01%, no slab cracking is confirmed and slab cracking is prevented.
  • the workability has a TS of 50 OMPa or more, the difference in resistance between the sheet width direction and the rolling direction is 2 OMPa or less, and no cracking occurs during flange processing or necking processing. A high strength steel plate for containers is obtained.
  • the P content is adjusted, and the reduction ratio in the second cold rolling is increased to 20 to 50% to increase the strength, and the appearance problems after rolling, the width direction and the rolling direction are increased. The problem of resistance to resistance is eliminated.
  • the steel plate for containers of the present invention can provide excellent strength without cracking in necking and flange processing.
  • it can be used for food containers such as cans, non-food containers such as oil filters, and electronic parts such as batteries. It can be suitably used as a container material in the center.

Abstract

L'invention concerne une tôle d'acier pour conteneurs dont la dureté est de 500 MPa ou plus et qui présente une excellente aptitude au façonnage, ainsi qu'un procédé de production de la tôle. On peut obtenir une tôle d'acier à haute résistance pour conteneurs, qui présente une résistance en traction de 500 MPa ou plus et dans laquelle la différence de contrainte d'essai entre la direction de la largeur de la tôle et la direction de laminage est de 20 MPa ou moins en faisant subir à un acier qui contient en masse C: 0,01 à 0,05 %, Si: 0,04 % ou moins, Mn: 0,1 à 1,2 %, S: 0,10 % ou moins, Al: 0,001 à 0,100 %, N: 0,10 % ou moins, P: 0,0020 à 0,100 %, le solde étant Fe et les impuretés inévitables, un laminage à chaud à une température de finition non inférieure à la température de transformation Ar3 moins 30°C, et à une température de bobinage de 400 à 750°C, en faisant subir à l'acier laminé un décapage, un laminage à froid et ensuite un recuit continu, notamment de sur-vieillissement, et en faisant subir ensuite à la tôle ainsi obtenue un deuxième laminage à froid à un taux d'étirage de 20 à 50 %.
PCT/JP2009/057717 2008-04-11 2009-04-10 Tôle d'acier à haute résistance pour conteneurs et procédé pour sa production WO2009125876A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US12/936,681 US20110168303A1 (en) 2008-04-11 2009-04-10 High tensile strength steel for container and producing method of the same
KR1020137017399A KR20130083487A (ko) 2008-04-11 2009-04-10 고강도 용기용 강판 및 그 제조 방법
CN2009801127859A CN101999009B (zh) 2008-04-11 2009-04-10 高强度容器用钢板及其制造方法
BRPI0909012A BRPI0909012A2 (pt) 2008-04-11 2009-04-10 aço de resistência à tração alta para recipiente e método de produção do mesmo

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2008103303 2008-04-11
JP2008-103303 2008-04-11
JP2008185660 2008-07-17
JP2008-185660 2008-07-17

Publications (1)

Publication Number Publication Date
WO2009125876A1 true WO2009125876A1 (fr) 2009-10-15

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US (1) US20110168303A1 (fr)
JP (1) JP5434212B2 (fr)
KR (2) KR20130083487A (fr)
CN (2) CN103409706B (fr)
BR (1) BRPI0909012A2 (fr)
MY (1) MY168642A (fr)
TW (1) TWI390053B (fr)
WO (1) WO2009125876A1 (fr)

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WO2011048274A1 (fr) * 2009-10-23 2011-04-28 Rautaruukki Oyj Procédé de production de produit en acier à haute résistance et produit en acier
CN102286688A (zh) * 2010-06-21 2011-12-21 宝山钢铁股份有限公司 一种高硬度镀锡原板用钢及其制造方法
JP2013133483A (ja) * 2011-12-26 2013-07-08 Jfe Steel Corp 高強度高加工性缶用鋼板およびその製造方法
KR20210141612A (ko) 2019-03-29 2021-11-23 제이에프이 스틸 가부시키가이샤 캔용 강판 및 그의 제조 방법

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BRPI0911139B1 (pt) * 2008-04-03 2018-03-13 Jfe Steel Corporation Chapa de aço de alta resistência para latas e método para produção da mesma
WO2012077628A1 (fr) 2010-12-06 2012-06-14 新日本製鐵株式会社 Tôle en acier destinée aux revêtements inférieurs de bombes aérosol et son procédé de fabrication
EP2770079B1 (fr) * 2012-04-19 2017-11-15 Nippon Steel & Sumitomo Metal Corporation Feuille d'acier et son procédé de production
CN103290312B (zh) * 2013-06-05 2015-01-21 首钢总公司 提高440MPa级碳素结构钢加工硬化值的生产方法
CN103757534B (zh) * 2013-12-27 2016-01-20 首钢总公司 一种具有良好凸缘焊接性能的冷轧钢板及其生产方法
CA2944403C (fr) * 2014-04-30 2019-02-26 Jfe Steel Corporation Tole d'acier a haute resistance pour contenant, et son procede de production
WO2019026739A1 (fr) * 2017-07-31 2019-02-07 Ｊｆｅスチール株式会社 Tôle d'acier pour capsule-couronne, capsule-couronne et procédé de fabrication de tôle d'acier pour capsule-couronne
CN109423577B (zh) 2017-08-30 2021-01-12 宝山钢铁股份有限公司 一种高强多相钢镀锡原板及其制造方法
CN110541123B (zh) * 2019-09-05 2021-06-15 首钢集团有限公司 一种电池壳用冷轧带钢及其制备方法
EP4108796A4 (fr) * 2020-02-17 2023-02-15 Nippon Steel Corporation Tôle d'acier de canette et son procédé de production
CN115341155B (zh) * 2022-10-17 2023-02-24 江苏省沙钢钢铁研究院有限公司 一种镀锡板及其制造方法

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CN103409706B (zh) 2015-12-02
TWI390053B (zh) 2013-03-21
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