WO2010113333A1 - Tôle d'acier pour un conteneur à haute résistance et son procédé de fabrication - Google Patents

Tôle d'acier pour un conteneur à haute résistance et son procédé de fabrication Download PDF

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Publication number
WO2010113333A1
WO2010113333A1 PCT/JP2009/058729 JP2009058729W WO2010113333A1 WO 2010113333 A1 WO2010113333 A1 WO 2010113333A1 JP 2009058729 W JP2009058729 W JP 2009058729W WO 2010113333 A1 WO2010113333 A1 WO 2010113333A1
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WIPO (PCT)
Prior art keywords
less
rolling
strength
steel
temperature
Prior art date
Application number
PCT/JP2009/058729
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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 CN2009801586065A priority Critical patent/CN102388156A/zh
Publication of WO2010113333A1 publication Critical patent/WO2010113333A1/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
    • C22C38/04—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
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • the present invention relates to a steel plate for a high-strength container suitable as a container material for reducing or expanding a diameter shape after three-piece processing such as welding or two-piece processing such as DI, and a manufacturing method thereof.
  • Patent Document 1 after controlling the components in steel within a certain range, hot rolling is finished at (Ar3 transformation point ⁇ 30 ° C.) or higher, and then, after pickling and cold rolling, continuous annealing is performed.
  • a method of performing secondary cold rolling has been proposed.
  • P is set to 0.02 wt% or less so that the flange workability, neck workability, and corrosion resistance are not deteriorated, and the reduction ratio of the secondary cold rolling is set to 15 to 30%.
  • the rolling reduction in the second cold rolling is as high as 20 to 50%, and the operation efficiency is lowered due to the high rolling load.
  • various rolling oils with high viscosity are used for the purpose of improving lubricity during rolling, there is a problem of poor appearance after rolling due to uneven concentration of the rolling oil or partial oil adhesion.
  • the rolling reduction ratio is high, the steel sheet is stretched by rolling, so that the difference in yield strength between the width direction of the steel sheet and the rolling direction becomes large.
  • the present invention has been made in view of such circumstances, and has a tensile strength TS of 500 MPa or more, a proof stress difference between the plate width direction and the rolling direction of 40 MPa or less, and a container having excellent workability. It aims at providing a steel plate and its manufacturing method.
  • the inventors of the present invention have intensively studied to solve the above problems. As a result, the following knowledge was obtained.
  • P is secured as a component composition at a certain level and the second cold rolling is performed at a rolling reduction (10% or more and less than 20%) that is lower than the conventional rolling rolling reduction, the appearance mismatch is small, and the width direction and the rolling direction It was found that a high strength material can be secured with a small proof stress difference.
  • a steel sheet for a high-strength container has been completed by managing components based on the above findings.
  • 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 TS 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 further organic coating is applied, and it can be applied to a wide range of applications.
  • the plate thickness is not particularly limited, but from the viewpoint of obtaining the effect by making the most of the present invention, the plate thickness is preferably 0.30 mm or less, and more preferably 0.20 mm or less. Particularly preferred is 0.170 mm or less.
  • the steel plate for containers of the present invention is a steel plate for high strength containers having a TS500 MPa or more and a difference in yield strength between the plate width direction and the rolling direction of 40 MPa or less. And in this invention, in order to improve and ensure the intensity
  • the component composition of the steel plate for containers according to the present invention will be described. C: 0.001 to 0.10% When there is much C component, the steel plate after secondary cold rolling will be hardened more than necessary, and can-making property and neck workability will deteriorate.
  • the effect which prevents a crack is acquired by adding according to S amount. It also has the effect of refining crystal grains. In order to exhibit these effects, it is necessary to add at least 0.1% of Mn. On the other hand, when 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 set it to 0.35% or less.
  • P: 0.007 to 0.100% P is a component necessary for hardening steel and obtaining a required strength, and is the most important requirement in the present invention. In order to acquire this effect, 0.007% or more of P is contained.
  • S 0.10% or less S is an element which exists as an inclusion in steel and reduces the ductility of the steel sheet and further deteriorates the corrosion resistance. Therefore, it is 0.10% or less. Preferably it is 0.030% or less.
  • Al 0.001 to 0.100% Al is an element necessary for deoxidation of steel.
  • N is an element useful for increasing the strength without increasing the hardness of the weld. However, if the content is too large, the steel sheet is remarkably hardened, and the risk of generating cracking defects in the rolled material (slab) is significantly increased.
  • N is 0.10% or less. It is preferable to make it 0.05% or less. Further, from the viewpoint of preventing slab cracking, it is more preferably less than 0.01%. Even more preferably, it is 0.005% or less. Thus, by reducing N, slab cracks can be reduced, and slab maintenance is not required, and yield can be improved.
  • the balance is Fe and inevitable impurities.
  • the balance other than the above components is Fe and inevitable impurities. As an inevitable impurity, for example, Sn: 0.01% or less is acceptable.
  • the container steel plate of the present invention has the above composition, TS of 500 MPa or more, and a proof stress difference between the plate width direction and the rolling direction of 40 MPa or less.
  • TS 500 MPa or more
  • the rigidity does not decrease even if the plate thickness is reduced.
  • the difference in proof stress between the sheet width direction and the rolling direction is 40 MPa or less, no cracking occurs during flange processing or necking processing.
  • Molten steel having the above composition is melted by a generally known melting method using a converter or the like, and then rolled into a rolled material (slab) by a generally known casting method such as a continuous casting method.
  • Slab extraction temperature 1050-1300 ° C (preferred conditions)
  • the slab heating temperature is preferably 1050 ° C. or higher and 1300 ° C. or lower.
  • Finishing temperature (hot rolling end temperature): (Ar3 transformation point temperature ⁇ 30) ° C.
  • the hot rolling end temperature is (Ar3 transformation point ⁇ ) in order to improve the cold rolling property and product characteristics of the subsequent process. 30) It is necessary to set the temperature to be equal to or higher than ° C. When the temperature is lower than (Ar3 transformation point ⁇ 30) ° C., the metal structure of the final product is coarsened, and rough skin is likely to occur during canning. In addition, when the hot rolling finish temperature becomes low, a ridging phenomenon occurs, and an appearance defect after the forming process tends to occur. Therefore, the hot rolling end temperature is set to (Ar3 transformation point ⁇ 30) ° C. or higher.
  • Winding temperature 400 ⁇ 750 °C If the coiling temperature is too low, the shape of the hot-rolled sheet deteriorates, and the pickling and cold rolling operations in the next process are hindered. On the other hand, if it becomes too high, aluminum nitride precipitates at the stage of the hot-rolled mother plate, and it becomes impossible to ensure sufficient solute N for strengthening. In addition, a structure in which carbide aggregates is formed in the hot-rolled mother plate, which adversely affects the corrosion resistance of the steel plate. Furthermore, 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 lower.
  • the hot-rolled sheet thus manufactured is pickled and cold-rolled to obtain a cold-rolled sheet.
  • the surface scale may be removed with an acid such as hydrochloric acid or sulfuric acid according to a conventional method.
  • 85% or more of a rolling reduction is more preferable.
  • the upper limit of the rolling reduction is not particularly required, and is appropriately set in consideration of the capability of the equipment row for hot rolling and cold rolling.
  • Annealing temperature Recrystallization temperature of 800 ° C or less (preferred condition) If the non-recrystallized structure remains in the steel sheet, it causes a formability defect and a poor appearance at the time of can making, and therefore it is necessary to perform a recrystallization process by continuous annealing. However, if the annealing temperature is excessively increased, defects such as heat buckles and plate breakage occur during continuous annealing. And the risk of deteriorating appearance characteristics due to abnormal crystal grain growth increases. Therefore, the annealing temperature is preferably performed in a recrystallization temperature range of 800 ° C.
  • Secondary cold rolling reduction 10% or more and less than 20% (preferably 10% or more and less than 15%) Secondary cold rolling after continuous annealing is necessary to secure the pressure resistance of the weld can, that is, the yield strength of the steel sheet.
  • the rolling reduction of secondary cold rolling needs to be at least 10%.
  • the rolling reduction is 20% or more, the material property anisotropy increases, and the difference in yield strength between the sheet width direction and the rolling direction exceeds 40 MPa.
  • the flange workability and neck workability in the new plate cutting method are significantly deteriorated.
  • the welding at the time of can making increases the amount of strain release, and the softening in the heat affected zone becomes significant, so that flange cracking is likely to occur. Therefore, less than 20%.
  • it is preferably 10% or more and less than 15%.
  • 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.
  • Any plating layer applied to the steel plate for containers can be applied to the plating layer formed on the surface.
  • the plating layer include tin plating, chromium plating, nickel plating, and nickel / chromium plating.
  • the coating, an organic resin film, etc. after these plating treatments there is no problem in applying a coating, an organic resin film, etc. after these plating treatments.
  • a steel containing the components shown in Table 1 and the balance being Fe and inevitable impurities was melted in a converter and made into a slab by a continuous casting method. Subsequently, these slabs were hot rolled at a slab extraction temperature of 1200 ° C., a hot rolling finishing temperature of 900 ° C., and a winding temperature of 650 ° C. to obtain hot rolled sheets having a finished thickness of 2.0 mm. Thereafter, the hot-rolled sheets are descaled by pickling, and further cold-rolled with a reduction rate of 90% to obtain cold-rolled sheets having a finished thickness of 0.20 mm. Continuous annealing at ⁇ 30 s and secondary cold rolling at the rolling reduction shown in Tables 2 and 3 were performed to obtain cold-rolled steel sheets.
  • the steel plate obtained as described above was subjected to the following tests to evaluate the characteristics.
  • (I) Tensile test JIS No. 13-B tensile test specimens were collected from the center in the width direction of these cold-rolled steel sheets in the rolling (L) direction and subjected to a tensile test at a strain rate crosshead speed of 10 mm / s. The tensile strength TS and the yield strength YS were measured. The tensile test was carried out within one day after commercialization. The reason why the tensile test piece is a JIS No. 13-B test piece is to reduce as much as possible the phenomenon of breaking outside the gauge.
  • no. No. 3 has a P content of less than 0.007%, so that the strength is insufficient even when the rolling reduction of the secondary cold rolling is 10%.
  • Table 3, No. 15-17, no. Examples 22 to 24 are examples in which the N content is 0.0070% and 0.0025%, and the preferred 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. Moreover, it turns out that a flange crack and an external appearance defect are completely suppressed by making the rolling reduction rate of secondary cold rolling 10% or more and less than 15% which is a suitable range, and it has become a more favorable result.
  • a steel plate for a high-strength container having a TS of 500 MPa or more, a difference in yield strength between the sheet width direction and the rolling direction of 40 MPa or less, and excellent workability that does not cause cracking during flange processing or necking processing Is obtained.
  • the reduction ratio in the second cold rolling can be lowered by hardening using the P component, the operational efficiency is increased and the productivity is excellent, and the appearance problems and width after rolling are reduced.
  • the problem of the difference in yield strength between the direction and the rolling direction is solved.
  • N component into less than 0.01% which is a suitable range, a slab crack can be prevented and the yield fall in a product can be suppressed.
  • the steel plate for containers of the present invention can provide excellent strength without cracking in necking and flange processing.
  • food containers such as cans, non-food containers such as oil filters, and electronic parts such as batteries are mainly used. It can be suitably used as a container material.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)

Abstract

L'invention concerne une tôle d'acier pour conteneurs, laquelle présente une dureté de 500 MPa ou plus et une excellente aptitude au traitement, et sur un procédé de fabrication de cette tôle d'acier. Un acier qui contient C : 0,001 à 0,10 %, 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, et P : 0,007 à 0,100 %, en % en masse, le reste étant constitué par les impuretés inévitables, est laminé à chaud à une température de finition (température de fin de laminage à chaud) : (température de transformation d'Ar3 – 30)°C ou plus et à une température de bobinage : 400 à 750°C, est décapé et laminé à froid, et est ensuite soumis à un recuit en continu. Ensuite, la tôle est laminée à froid pour la seconde fois à une réduction de laminage : 10 % ou plus mais moins de 20 %, et une tôle d'acier pour des conteneurs à haute résistance est obtenue, laquelle présente une résistance à la traction de 500 MPa ou plus et une variation de la limite d'élasticité de 40 MPa ou moins dans la direction de la largeur de la feuille et la direction de laminage.
PCT/JP2009/058729 2009-04-02 2009-04-28 Tôle d'acier pour un conteneur à haute résistance et son procédé de fabrication WO2010113333A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN2009801586065A CN102388156A (zh) 2009-04-02 2009-04-28 高强度容器用钢板及其制造方法

Applications Claiming Priority (2)

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JP2009-089937 2009-04-02
JP2009089937A JP5453884B2 (ja) 2008-04-03 2009-04-02 高強度容器用鋼板およびその製造方法

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WO2010113333A1 true WO2010113333A1 (fr) 2010-10-07

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JP (1) JP5453884B2 (fr)
KR (1) KR20110130478A (fr)
CN (1) CN102388156A (fr)
MY (1) MY158249A (fr)
TW (1) TWI390054B (fr)
WO (1) WO2010113333A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
EP3205739A4 (fr) * 2014-10-10 2017-09-13 JFE Steel Corporation Tôle d'acier pour couvercle et son procédé de production
CN110541123A (zh) * 2019-09-05 2019-12-06 首钢集团有限公司 一种电池壳用冷轧带钢及其制备方法

Families Citing this family (13)

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Publication number Priority date Publication date Assignee Title
EP2508641B1 (fr) * 2009-12-02 2015-11-04 JFE Steel Corporation Feuille d'acier pour canettes et procédé de fabrication associé
CA2818911C (fr) 2010-12-06 2014-07-15 Nippon Steel & Sumitomo Metal Corporation Tole en acier destinee aux revetements inferieurs de bombes aerosol et son procede de fabrication
JP5924044B2 (ja) * 2011-03-17 2016-05-25 Ｊｆｅスチール株式会社 耐圧強度が高く加工性に優れたエアゾール缶ボトム用鋼板およびその製造方法
JP5919812B2 (ja) * 2011-12-27 2016-05-18 Ｊｆｅスチール株式会社 成形性に優れた高強度薄鋼板およびその製造方法
WO2013151085A1 (fr) * 2012-04-06 2013-10-10 Ｊｆｅスチール株式会社 Tôle d'acier facilement façonnable, de résistance élevée, et son procédé de fabrication
CN103045937A (zh) * 2012-12-14 2013-04-17 宝山钢铁股份有限公司 一种二次冷轧钢及其制造方法
CN106460125B (zh) * 2014-04-30 2019-11-08 杰富意钢铁株式会社 高强度钢板及其制造方法
AU2015254790B2 (en) * 2014-04-30 2017-08-31 Jfe Steel Corporation High strength steel sheet for container, and method for producing same
TWI582243B (zh) 2014-07-22 2017-05-11 新日鐵住金股份有限公司 蓄電裝置容器用鋼箔、蓄電裝置用容器及蓄電裝置、以及蓄電裝置容器用鋼箔之製造方法
WO2016056239A1 (fr) * 2014-10-10 2016-04-14 Ｊｆｅスチール株式会社 Tôle d'acier pour couvercle et son procédé de production
CN106086643B (zh) 2016-06-23 2018-03-30 宝山钢铁股份有限公司 一种高强高延伸率的镀锡原板及其二次冷轧方法
CN111218617B (zh) * 2020-02-24 2021-09-17 包头钢铁（集团）有限责任公司 一种低屈服强度，无屈服平台的冷轧低碳钢带spcc及其生产方法
CN111549281A (zh) * 2020-05-23 2020-08-18 山东泰山轧钢有限公司 一种高硬度五金件用冷轧钢带及其生产方法

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JP2007177315A (ja) * 2005-12-28 2007-07-12 Nippon Steel Corp フランジ加工性に優れた溶接缶用連続焼鈍ｄｒ鋼板およびその製造方法
JP2007247012A (ja) * 2006-03-17 2007-09-27 Jfe Steel Kk 極薄缶用鋼板の製造方法および極薄缶用鋼板

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
EP3205739A4 (fr) * 2014-10-10 2017-09-13 JFE Steel Corporation Tôle d'acier pour couvercle et son procédé de production
CN110541123A (zh) * 2019-09-05 2019-12-06 首钢集团有限公司 一种电池壳用冷轧带钢及其制备方法
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

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KR20110130478A (ko) 2011-12-05
MY158249A (en) 2016-09-30
JP5453884B2 (ja) 2014-03-26
TW201037091A (en) 2010-10-16
CN102388156A (zh) 2012-03-21
JP2009263789A (ja) 2009-11-12
TWI390054B (zh) 2013-03-21

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