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WO2020203470A1 - Tôle d'acier pour canette et son procédé de fabrication - Google Patents

Tôle d'acier pour canette et son procédé de fabrication Download PDF

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Publication number
WO2020203470A1
WO2020203470A1 PCT/JP2020/013035 JP2020013035W WO2020203470A1 WO 2020203470 A1 WO2020203470 A1 WO 2020203470A1 JP 2020013035 W JP2020013035 W JP 2020013035W WO 2020203470 A1 WO2020203470 A1 WO 2020203470A1
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WO
WIPO (PCT)
Prior art keywords
less
rolling
cans
tensile strength
rolled
Prior art date
Legal status (The legal status 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 status listed.)
Ceased
Application number
PCT/JP2020/013035
Other languages
English (en)
Japanese (ja)
Inventor
勇人 齋藤
房亮 假屋
克己 小島
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 Steel Corp filed Critical JFE Steel Corp
Priority to PH1/2021/552442A priority Critical patent/PH12021552442A1/en
Priority to KR1020217030864A priority patent/KR102549938B1/ko
Priority to JP2020544692A priority patent/JP6819838B1/ja
Priority to MYPI2021005539A priority patent/MY196420A/en
Priority to CN202080025702.9A priority patent/CN113748220B/zh
Publication of WO2020203470A1 publication Critical patent/WO2020203470A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21D8/0273—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
    • 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
    • C22C38/06—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
    • C22C38/12—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a can steel plate suitable for application to a material for a can container used for food cans, beverage cans, etc. and a method for producing the same, and can be particularly preferably applied to the production of an easy open end (EOE).
  • EEE easy open end
  • the present invention relates to a steel plate for cans and a method for manufacturing the same.
  • the pressure resistance will decrease, so it is necessary to use a high-strength steel plate.
  • SR Single Redened
  • DR Double Redduced
  • the SR material is a material manufactured by temper rolling after annealing
  • the DR material is a steel sheet manufactured by cold rolling (secondary cold rolling) again after annealing. ..
  • Patent Document 1 states that as a high-strength SR steel plate, C: 0.03 to 0.13%, Si: 0.03% or less, Mn: 0.3 to 0.6%, P: 0. 02% or less, Al: 0.1% or less, N: 0.012% or less, Nb: 0.005 to 0.05%, Ti: 0.005 to 0.05%, b: 0.0005 It contains 1 or more of ⁇ 0.005%, has a composition of iron and unavoidable impurities in the balance, and has a ferrite structure with a cementite ratio of 0.5% or more, and has a ferrite average grain size of 7 ⁇ m or less.
  • steel plates for cans having a tensile strength of 450 to 550 MPa after a coating baking treatment, a total elongation of 20% or more, and a yield elongation of 5% or less.
  • Patent Document 2 describes as a DR steel plate having good workability, in terms of mass%, C: 0.010 to 0.080%, Si: 0.05% or less, Mn: 0.10% or more and 0.70% or less. P: 0.03% or less, S: 0.020% or less, N: 0.0120% or more and 0.0180% or less, Al: 0.005% or more and 0.070% or less, and the balance is an unavoidable impurity
  • the content of N as a solid solution N is 0.0100% or more, the ferrite particle size is 7.0 ⁇ m or less, and the depth is 1/4 of the plate thickness from the surface layer.
  • the displacement density at the position is 4.0 ⁇ 10 14 m- 2 or more and 2.0 ⁇ 10 15 m- 2 or less, the tensile strength in the direction perpendicular to rolling after aging treatment is 530 MPa or more, and the elongation is 7% or more.
  • a high-strength steel plate characterized by this has been proposed.
  • Patent Document 1 can be applied only to steel sheets having a tensile strength of up to 550 MPa, and cannot cope with further thinning.
  • Patent Document 2 since the N content is high, there is a problem that the yield elongation is large and a stretcher strain is generated at the time of lid processing and the appearance is deteriorated. Further, there is a problem that the can-opening force required to open the EOE increases simply by increasing the strength.
  • the present invention has been made in view of such circumstances, and an object of the present invention is to provide a steel sheet for cans having excellent processability and openability, and a method for manufacturing the same.
  • the present invention has the following gist.
  • the component composition in terms of mass%, C: 0.100% or more and less than 0.130%, Si: 0.04% or less, Mn: 0.10% or more and 0.60% or less, P: 0.020 % Or less, S: 0.020% or less, Al: 0.01% or more and 0.10% or less, N: 0.0005% or more and 0.0040% or less, Nb: 0.005% or more and 0.030% or less, B: Containing more than 0.0005% and 0.0050% or less, the balance is composed of Fe and unavoidable impurities, has a ferrite structure containing pearlite in an area fraction of 1.0% or more, and has a ferrite structure at 210 ° C.
  • Ti 0.005% or more and 0.030% or less
  • Mo 0.01% or more and 0.05% or less
  • Cr 0.05% or more and 0.20% or less.
  • the steel sheet for cans according to (1) which contains one or more of them.
  • the cold-rolled sheet obtained in the primary cold rolling step is annealed at an annealing temperature of 720 ° C. or higher and 780 ° C. or lower.
  • a method for producing a steel plate for cans in which the annealed plate obtained in the annealing step is cold rolled at a rolling ratio of 6.0% or more and 30.0% or less.
  • the steel sheet for cans of the present invention has excellent workability and openability. According to the present invention, the steel plate used for food cans, beverage cans and the like can be further thinned, and resource saving and cost reduction can be achieved.
  • the processability means the lid-making property
  • the excellent lid-making property means that there is no stretcher strain and there is no rivet cracking.
  • the component composition, the steel sheet structure, the steel sheet characteristics, and the manufacturing method of the steel sheet for cans of the present invention will be described in order.
  • the present invention is not limited to the following embodiments.
  • the following "opening of a can” means opening an EOE to which the steel plate for a can of the present invention is applied.
  • the component composition of the steel sheet for cans of the present invention will be described.
  • % indicating the content of each component means mass%.
  • C 0.100% or more and less than 0.130% C is an important element that contributes to the reduction of yield elongation and the reduction of can opening force by forming pearlite in addition to the improvement of tensile strength.
  • the pearlite can be set to 1.0% or more and the tensile strength can be set to 630 MPa or more. It is preferably 0.105% or more. More preferably, it is 0.110% or more.
  • the C content needs to be less than 0.130%. It is preferably 0.125% or less.
  • Si 0.04% or less
  • the Si content is preferably 0.03% or less.
  • Si contributes to the improvement of tensile strength, it is preferable to add 0.01% or more.
  • Mn 0.10% or more and 0.60% or less Mn not only contributes to the improvement of tensile strength by solid solution strengthening, but also promotes the formation of pearlite.
  • the Mn content needs to be 0.10% or more. It is preferably 0.20% or more. More preferably, it is 0.40% or more.
  • the Mn content needs to be 0.60% or less. Preferably, it is 0.50% or less.
  • the P content is set to 0.020% or less. Preferably, it is 0.018% or less.
  • P contributes to the improvement of tensile strength, it is preferable to add 0.005% or more. More preferably, it is 0.008% or more.
  • S 0.020% or less S forms sulfide in steel and lowers hot rollability. Therefore, the S content is set to 0.020% or less. It is preferably 0.015% or less. More preferably, it is 0.012% or less. When the S content is 0.005% or more, pitting corrosion can be prevented regardless of the contents of the can, so it is preferable to add 0.005% or more of S. More preferably, it is 0.008% or more.
  • Al 0.01% or more and 0.10% or less
  • Al is useful as a deoxidizing element and contributes to reduction of yield elongation by forming a nitride. Therefore, it is necessary to contain 0.01% or more. It is preferably 0.03% or more. If it is excessively contained, a large amount of alumina is generated and remains in the steel sheet to reduce workability. Therefore, the Al content needs to be 0.10% or less. It is preferably 0.09% or less. More preferably, it is 0.08% or less.
  • N 0.0005% or more and 0.0040% or less
  • the N content needs to be 0.0040% or less. It is preferably 0.0030% or less. More preferably, it is 0.0025% or less.
  • the N content is set to 0.0005% or more.
  • Nb 0.005% or more and 0.030% or less
  • Nb is an important element for improving tensile strength by refining ferrite crystal grains and forming carbides, and Nb is contained in order to obtain such an effect.
  • the amount should be 0.005% or more. It is preferably 0.010% or more. More preferably, it is 0.012% or more.
  • the Nb content needs to be 0.030% or less. It is preferably 0.023% or less.
  • B Exceeding 0.0005% and 0.0050% or less B has the effect of forming N and BN to reduce the solid solution N and reduce the yield elongation.
  • the B content needs to exceed 0.0005%. It is preferably over 0.0020%. More preferably, it is 0.0025% or more. Even if B is excessively contained, not only the above effect is saturated, but also C precipitated as granular cementite increases, pearlite decreases, and the can openability deteriorates. Therefore, the B content is 0.0050. Must be less than or equal to%. It is preferably 0.0035% or less. More preferably, it is 0.0030% or less.
  • the steel sheet for cans of the present invention has Ti: 0.005% or more and 0.030% or less, Mo: 0.01% or more and 0.05% or less, Cr: 0.05% or more and 0.20% or less. Of these, it is preferable to contain one or more of them.
  • Ti 0.005% or more and 0.030% or less Ti has the effect of fixing N as TiN and reducing the yield elongation. Further, by preferentially generating TiN, the formation of BN is suppressed, and by securing the solid solution B, the ferrite crystal grains are refined, which contributes to the improvement of yield stress and tensile strength. Furthermore, it also contributes to the improvement of tensile strength by forming fine carbides. Therefore, it is preferable to contain Ti at 0.005% or more. The Ti content is more preferably 0.010% or more. If Ti is contained in an amount of more than 0.030%, the recrystallization temperature becomes excessively high, unrecrystallized grains remain, and the tensile strength becomes excessive. Therefore, the Ti content is preferably 0.030% or less. More preferably, it is 0.025% or less.
  • Mo 0.01% or more and 0.05% or less
  • Mo is preferably contained in an amount of 0.01% or more because it contributes to the improvement of tensile strength and the increase in the amount of pearlite by refining ferrite crystal grains and forming carbides. .. More preferably, it is 0.02% or more. If Mo is contained in an amount of more than 0.05%, such an effect is saturated. Therefore, the Mo content is preferably 0.05% or less.
  • Cr 0.05% or more and 0.20% or less Cr is preferably contained in an amount of 0.05% or more because it contributes to an increase in the amount of pearlite. More preferably, it is 0.08% or more. If Cr is contained in an amount of more than 0.20%, such an effect is saturated. Therefore, the Cr content is preferably 0.20% or less. More preferably, it is 0.16% or less.
  • the rest of the above component composition in the steel sheet for cans according to the present invention is Fe and unavoidable impurities.
  • the surface integral of pearlite is preferably 1.5% or more. More preferably, it is 1.8% or more.
  • the surface integral ratio of the pearlite is preferably 10% or less. More preferably, it is 5.0% or less.
  • the rest is a ferrite phase and may contain granular cementite. It is not necessary to include a hard phase such as martensite, bainite, and retained austenite, but the steel sheet structure may contain 1% or less of the total surface integral.
  • a sample is cut out, embedded in a resin, polished, corroded with nital to reveal a structure, and then a scanning electron microscope (SEM) is used so that a vertical cross section parallel to the rolling direction of the steel sheet can be observed.
  • SEM scanning electron microscope
  • the steel plate structure is photographed at.
  • the surface integral of pearlite is measured by image processing using the captured image.
  • Tensile strength 630 MPa or more, 750 MPa or less, yield elongation: 3.0% or less, elongation: 3.0% or more and less than 10.0%
  • a can The tensile strength of the steel plate used for the lid needs to be 630 MPa or more. Preferably, it is 650 MPa or more. If the tensile strength becomes excessive, the can opening force increases, so the tensile strength needs to be 750 MPa or less. It is preferably 710 MPa or less. In order to suppress the occurrence of cracks during rivet processing, the elongation needs to be 3.0% or more. It is preferably 4.0% or more.
  • the elongation needs to be less than 10.0%. It is preferably less than 7.0%. In order to prevent stretcher strain during lid processing, the yield elongation must be 3.0% or less. Preferably, it is 2.0% or less. More preferably, it is 1.2% or less.
  • tensile strength, yield elongation and elongation are evaluated according to JIS Z 2241 after collecting a JIS No. 5 tensile test piece from the rolling direction and subjecting it to aging heat treatment at 210 ° C. for 20 minutes.
  • the thickness of the steel plate for cans of the present invention is not particularly limited, but is preferably 0.30 mm or less. Since the steel plate for cans of the present invention can be gauged down to an ultra-thin size, it is more preferable to set the plate thickness to 0.10 to 0.25 mm from the viewpoint of resource saving and cost reduction.
  • a steel sheet for cans can be manufactured under the conditions described below. It should be noted that steps such as a plating step of applying Sn plating, Ni plating, Cr plating and the like, a chemical conversion treatment step, a resin film coating step of laminating and the like may be appropriately performed.
  • the slab heating temperature is preferably 1100 ° C. or higher. More preferably, it is 1150 ° C. or higher. When Ti is contained, 1200 ° C. or higher is even more preferable. If the slab heating temperature is 1280 ° C. or lower, surface defects due to scale can be easily avoided, and therefore it is preferably 1280 ° C. or lower.
  • the slab heating temperature is more preferably 1250 ° C. or lower.
  • Finishing temperature 830 ° C or higher and 960 ° C or lower (suitable range) If the finishing temperature of hot rolling is 960 ° C or lower, finer ferrite crystal grains can be obtained, and the tensile strength after cold rolling, annealing, and secondary cold rolling becomes good, so the finishing temperature is set to 960.
  • the temperature is preferably below ° C.
  • the finishing temperature of hot rolling is 830 ° C. or higher, the Nb carbides formed during hot rolling become finer and better tensile strength can be obtained. Therefore, it is preferable to set the finishing temperature to 830 ° C. or higher. ..
  • the finishing temperature is more preferably 850 ° C. or higher.
  • Winding temperature 450 ° C or more and less than 670 ° C (suitable range) If the winding temperature is less than 670 ° C., the cementite in the hot-rolled plate becomes fine and sufficiently melts during annealing to promote the formation of pearlite.
  • alloy carbides such as Nb carbides are also made finer, and better tensile strength can be obtained. Therefore, the winding temperature is preferably less than 670 ° C. More preferably, it is 620 ° C. or lower.
  • the winding temperature is 450 ° C. or higher, the effect of precipitating alloy carbides such as Nb can be surely obtained and the tensile strength becomes good. Therefore, the winding temperature is preferably 450 ° C. or higher.
  • the winding temperature is more preferably 550 ° C. or higher.
  • the hot-rolled plate after winding is pickled to remove the surface scale.
  • the pickling conditions are not specified as long as the surface scale can be removed. It can be pickled by a conventional method.
  • the rolling ratio of the primary cold rolling 85.0% or more (suitable range)
  • the rolling ratio of the primary cold rolling is more preferably 87% or more.
  • the rolling ratio of the primary cold rolling is preferably 93% or less.
  • the rolling ratio of the primary cold rolling is more preferably 90.4% or less.
  • Annealing temperature 720 ° C. or higher and 780 ° C. or lower It is important to generate pearlite in the annealing step in order to obtain high tensile strength and small yield elongation. Therefore, it is necessary to set the annealing temperature to 720 ° C. or higher.
  • the annealing temperature is preferably 730 ° C. or higher.
  • the annealing temperature exceeds 780 ° C., alloy carbides such as Nb carbides become coarse, and ferrite crystal grains also become coarse and the tensile strength decreases. Therefore, the annealing temperature must be 780 ° C. or lower. ..
  • the annealing temperature is more preferably 770 ° C. or lower. As the annealing method, continuous annealing is preferable from the viewpoint of material uniformity.
  • the annealing time is not particularly limited, but is preferably 15 s or more.
  • the annealing time is preferably 60 s or less from the viewpoint of fine graining of ferrite crystal grains. More preferably, it is 40 s or less.
  • the rolling ratio (secondary rolling ratio) in the secondary cold rolling step is set to 6.0% or more. It is preferably 10.0% or more. If the secondary rolling ratio exceeds 30.0%, strain is excessively introduced, the tensile strength becomes excessive, and the can openability deteriorates. Therefore, the secondary rolling ratio is set to 30.0% or less.
  • the secondary rolling ratio is preferably 20.0% or less.
  • the secondary rolling ratio is more preferably 15.0% or less.
  • the tensile strength is 630 MPa or more and 750 MPa or less
  • the yield elongation is 3.0% or less
  • the area fraction of pearlite is 1.0% or more
  • the elongation is 3.0% or more and less than 10.0%.
  • the workability and can openability were good.
  • one or more of tensile strength, yield elongation, surface integral of pearlite, processability, and can openability were inferior.

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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)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne une tôle d'acier pour une canette comprenant, en % en poids, en tant que composition de composant, 0,100 % ou plus et moins de 0,130 % de C, 0,04 % ou moins de Si, 0,10 % ou plus et 0,60 % ou moins de Mn, 0,020 % ou moins de P, 0,020 % ou moins de S, 0,01 % ou plus et 0,10 % ou moins d'Al, 0,0005 % ou plus et 0,0040 % ou moins de N, 0,005 % ou plus et 0,030 % ou moins de Nb et plus de 0,0005 % et 0,0050 % ou moins de B, le reste étant du Fe et des impuretés inévitables. La tôle d'acier a une structure de ferrite comprenant 1,0 % ou plus de perlite comme fraction de surface, a une résistance à la traction de 630 MPa ou plus et de 750 MPa ou moins après un traitement thermique pendant 20 minutes à 210 °C, a un allongement à la limite d'élasticité de 3,0 % ou moins et a un allongement de 3,0 % ou plus et de moins de 10,0 %.
PCT/JP2020/013035 2019-03-29 2020-03-24 Tôle d'acier pour canette et son procédé de fabrication Ceased WO2020203470A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
PH1/2021/552442A PH12021552442A1 (en) 2019-03-29 2020-03-24 Steel sheet for cans and method for manufacturing the same
KR1020217030864A KR102549938B1 (ko) 2019-03-29 2020-03-24 캔용 강판 및 그의 제조 방법
JP2020544692A JP6819838B1 (ja) 2019-03-29 2020-03-24 缶用鋼板およびその製造方法
MYPI2021005539A MY196420A (en) 2019-03-29 2020-03-24 Steel Sheet for Cans and Method for Manufacturing the same
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CN113748220A (zh) 2021-12-03
MY196420A (en) 2023-03-30
KR20210131407A (ko) 2021-11-02
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CN113748220B (zh) 2023-03-31
TW202104616A (zh) 2021-02-01

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