WO2016067514A1 - Steel sheet for two-piece can and manufacturing method therefor - Google Patents
Steel sheet for two-piece can and manufacturing method therefor Download PDFInfo
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- WO2016067514A1 WO2016067514A1 PCT/JP2015/004784 JP2015004784W WO2016067514A1 WO 2016067514 A1 WO2016067514 A1 WO 2016067514A1 JP 2015004784 W JP2015004784 W JP 2015004784W WO 2016067514 A1 WO2016067514 A1 WO 2016067514A1
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- 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
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a steel plate for cans suitable for can container materials used in food and beverage cans and a method for producing the same.
- the present invention relates to a two-piece can high-strength steel sheet having excellent formability and a method for producing the same, and the two-piece can high-strength steel sheet according to the present invention is a two-piece machined to the can body. It can be preferably applied to a deformed can.
- the can body is often formed into a deformed can having a bead processing or a geometric shape.
- the can body is processed after forming with a relatively high degree of processing by drawing or ironing. For this reason, the steel plate used for manufacture of the two-piece can deformed can requires higher formability.
- the strength increase due to work hardening is small at the bottom of the can with a low degree of processing. For this reason, when the steel plate is thinned, the strength of the steel plate tends to be insufficient at the bottom of the can.
- the formability is generally low. If the moldability is low, it is not preferable for the can body as described above. Therefore, a technique for improving the formability of the DR steel sheet has been studied.
- Patent Document 1 in mass%, C: 0.001 to 0.10%, Mn: 0.05 to 0.50%, Al: 0.015 to 0.13%, Si: 0.05 %, P: 0.03% or less, S: 0.03% or less, the balance being Fe and inevitable impurities, crystal grain size: 6-30 ⁇ m, centerline average roughness: 0.05- 0.6 ⁇ m, plate thickness: 0.15 to 0.30 mm electrolytic chromic acid-treated steel sheet coated on both sides with 10 to 50 ⁇ m thick thermoplastic resin and dry squeezing with high temperature volatile lubricant applied to the surface A resin-coated steel sheet for a processing can is disclosed.
- Patent Document 2 in mass%, C: 0.001 to 0.06%, Mn: 0.05 to 0.50%, Al: 0.015 to 0.13%, Si: 0.05% or less , P: 0.03% or less, S: 0.03% or less, with the balance being Fe and inevitable impurities, and after pickling, cold rolling, continuous annealing, at a rolling rate of 5-25% Rolled, centerline average roughness: 0.05 to 0.6 ⁇ m, plate thickness: 0.15 to 0.30 mm, then treated with electrolytic chromic acid, and then a thermoplastic resin having a thickness of 10 to 50 ⁇ m on both sides.
- a method for producing a resin-coated steel sheet for a dry-type squeezing and ironing which is coated and coated with a high-temperature volatile lubricant on the surface thereof, is disclosed.
- Patent Document 3 in mass%, C: 0.02 to 0.07%, Si: 0.005 to 0.05%, Mn: 0.1 to 1.5%, P: 0.04% or less S: 0.02% or less, Al: 0.005 to 0.1%, N: more than 0.003 to 0.007%, B: 0.001 to 0.01%, B / N: The relationship of 0.3 to 1.5 is satisfied, the balance is made of a steel composition of Fe and inevitable impurities, and the Rankford value (r value) of at least one of the rolling direction and the sheet width direction is 0.8 or less.
- r value Rankford value
- Patent Document 3 The technology described in Patent Document 3 is for a three-piece can.
- the steel sheet described in Patent Document 3 has a large anisotropy because the r value of at least one of the rolling direction and the sheet width direction is 0.8 or less.
- This steel plate having large anisotropy does not have the formability required for forming a two-piece can including drawing.
- the present invention has been made in view of such circumstances, and solves the problems of the prior art described above, and in particular, provides a high-strength steel sheet for a two-piece can that can be preferably used for forming a two-piece deformed can and a method for manufacturing the same.
- the purpose is to do.
- the present inventors have conducted intensive research to solve the above problems. Specifically, in order to find a method for achieving both excellent strength required for the can bottom and excellent moldability required for the can body, as a result, component composition, tensile strength, elongation, The inventors have found that the above-mentioned problems can be solved by adjusting the yield elongation and the ferrite grain size to a specific range, and the present invention has been completed based on this finding.
- the present invention has been made based on the above findings, and the gist thereof is as follows.
- a high-strength steel sheet for a two-piece can characterized by having 480 MPa or more, elongation of 7% or more, yield elongation of 3% or less, and ferrite grain size of less than 6 ⁇ m.
- the high-strength steel sheet for a two-piece can according to (1), further comprising, by mass%, B: 0.0001% or more and 0.0030% or less.
- a secondary cold rolling step of performing secondary cold rolling at a high temperature for a two-piece can Method of manufacturing a degree steel plate.
- the high-strength steel sheet for a two-piece can of the present invention is adjusted to have a specific composition, has a tensile strength of 480 MPa or more, an elongation of 7% or more, a yield elongation of 3% or less, and a ferrite grain size of 6 It is adjusted to less than 0.0 ⁇ m.
- the high-strength steel sheet for a two-piece can of the present invention has excellent strength required for a can bottom and excellent formability required for a can body. Therefore, if the high-strength steel plate for a two-piece can according to the present invention is used, a two-piece modified can can be easily manufactured.
- the high-strength steel sheet for a two-piece can of the present invention is, in mass%, C: 0.020% or more and 0.080% or less, Si: 0.04% or less, Mn: 0.10% or more and 0.60% or less, P: 0.02% or less, S: 0.015% or less, Al: 0.010% or more and 0.100% or less, N: 0.0005% or more and 0.0030% or less, the balance being Fe and inevitable It has a component composition consisting of mechanical impurities.
- the tensile strength is 480 MPa or more
- the elongation is 7% or more
- the yield elongation is 3% or less.
- the structure of the high-strength steel plate for a two-piece can of the present invention is a structure having a ferrite particle size of less than 6 ⁇ m.
- the high-strength steel sheet for a two-piece can of the present invention will be described in the order of component composition, physical properties, and structure.
- the high-strength steel sheet for a two-piece can according to the present invention is, in mass%, C: 0.020% or more and 0.080% or less, Si: 0.04% or less, Mn: 0.10% or more and 0.0. 60% or less, P: 0.02% or less, S: 0.015% or less, Al: 0.010% or more and 0.100% or less, N: 0.0005% or more and 0.0030% or less, and the balance Consists of Fe and inevitable impurities.
- the reason for adopting this component composition is as follows. In the following description, “%” representing the content of each component means “mass%”.
- C 0.020% or more and 0.080% or less C is an element important for strength improvement.
- the tensile strength can be set to 480 MPa or more.
- the upper limit of the C content needs to be 0.080%.
- the larger the C content the finer the ferrite grain size and the higher the strength.
- the C content is preferably 0.030% or more.
- the C content is preferably 0.060% or less.
- Si 0.04% or less
- Si content 0.04% or less.
- Si content 0.03% or less.
- Mn 0.10% or more and 0.60% or less Mn has an effect of improving the hardness of the steel sheet by solid solution strengthening. Moreover, since Mn forms MnS, it is possible to prevent a decrease in hot ductility due to S contained in the steel. In order to acquire these effects, it is necessary to make Mn content 0.10% or more.
- the Mn content is preferably set to 0.30% or more so that tensile strength can be secured even if the rolling rate in DR rolling is reduced by solid solution strengthening with Mn. If the Mn content exceeds 0.60%, the elongation is remarkably lowered and the can-making ability is lowered. Therefore, the Mn content needs to be 0.60% or less.
- S 0.015% or less S forms sulfides in steel and reduces hot ductility. Therefore, the upper limit of the S content is 0.015% or less.
- Al 0.010% or more and 0.100% or less Al forms N and AlN, thereby reducing solid solution N in the steel, lowering the yield elongation and suppressing stretcher strain. For this reason, it is necessary to make Al content 0.010% or more.
- the Al content is preferably 0.050% or more, and more preferably 0.060% or more. Further, when the Al content is excessive, a large amount of alumina is generated, and alumina remains in the steel sheet, resulting in a decrease in canability. Therefore, the Al content needs to be 0.100% or less. Preferably it is 0.080% or less.
- N 0.0005% or more and 0.0030% or less
- yield elongation increases, stretcher strain occurs, the surface appearance becomes poor, and the can-making ability decreases.
- N content needs to be 0.0030% or less.
- it is 0.0025% or less.
- it is difficult to stably make the N content less than 0.0005%, and if the N content is made less than 0.0005%, the manufacturing cost also increases. For this reason, the lower limit of the N content is 0.0005%.
- the high-strength steel sheet for a two-piece can of the present invention preferably contains B as an optional component in the range of 0.0030% or less in addition to the above essential components.
- B 0.0001 to 0.0030%
- B forms N and BN, reduces the solute N, and lowers the yield elongation.
- the B content is preferably 0.0001% or more, and more preferably 0.0003% or more.
- the upper limit of the B content is preferably 0.0030%.
- the balance other than the above essential components and optional components is Fe and inevitable impurities.
- Inevitable impurities include Cr: 0.08% or less, Cu: 0.02% or less, Ni: 0.02% or less, O: 0.006% or less.
- the high-strength steel sheet for 2-piece cans of the present invention has a tensile strength of 480 MPa or more, an elongation of 7% or more, and a yield elongation of 3% or less.
- the technical significance of each physical property is as follows, but in the present invention, the combination of these physical properties, the above component composition, and the structure described later, the strength required for the can bottom, and the can body are required.
- One of the important technical significances is that both excellent moldability and compatibility can be achieved.
- the tensile strength of the steel plate needs to be 480 MPa or more. Preferably it is 490 MPa or more.
- the value obtained by measuring with the method as described in an Example is employ
- Elongation 7% or more
- it is 9% or more.
- the elongation can be increased to 7% or more while being high strength of 480 MPa or more. It becomes possible to ensure canability.
- the value obtained by measuring with the method as described in an Example is employ
- the elongation is usually 25% or less.
- Yield elongation 3% or less Yield elongation needs to be 3% or less in order to prevent stretcher strain during canning. Preferably it is 2% or less.
- the value obtained by measuring with the method as described in an Example is employ
- the ferrite grain size in the structure of the high-strength steel sheet for a two-piece can of the present invention is less than 6 ⁇ m.
- Ferrite particle size less than 6 ⁇ m
- the balance between increasing strength and elongation is improved by reducing the ferrite particle size. For this reason, it is necessary to make a ferrite particle size less than 6.0 micrometers. Further, by reducing the ferrite grain size to less than 6.0 ⁇ m and reducing the yield elongation to 3% or less, there is an effect of improving the adhesion between the resin coated on the steel sheet and the steel sheet surface. From this point of view, the ferrite grain size is preferably 5.5 ⁇ m or less.
- the particle size means an average crystal particle size.
- the content of the ferrite phase in the structure is 95 vol% or more for the reason of improvement in elongation. More preferably, it is 98 vol% or more.
- phases other than the ferrite phase include cementite, pearlite, martensite, and bainite.
- ⁇ Method for producing high-strength steel plate for 2-piece can> As an example of a method for producing a high-strength steel sheet for a two-piece can of the present invention, a heating step, a hot rolling step, a winding step, a pickling step, a primary cold rolling step, a continuous annealing step, The manufacturing method which has a secondary cold rolling process is mentioned. Hereinafter, each step will be described.
- the heating step is a step of heating the slab to a heating temperature of 1130 ° C or higher.
- the heating temperature in the heating process is set to 1130 ° C. or higher.
- it is 1150 degreeC or more.
- the upper limit of the heating temperature is not particularly defined, but if the heating temperature is too high, excessive scale is generated, resulting in defects on the product surface. Therefore, the upper limit of the heating temperature is preferably 1260 ° C.
- the component composition of the slab becomes the component composition of the high-strength steel plate for a two-piece can
- the component composition of the slab needs to be adjusted so as to satisfy the component composition of the two-piece high-strength steel plate of the present invention.
- the hot rolling process is a process in which the slab after the heating process is hot rolled under the condition of a hot rolling finishing temperature of 820 to 930 ° C.
- a hot rolling finishing temperature 820 to 930 ° C.
- the hot rolling finish rolling temperature is higher than 930 ° C.
- the ferrite grain size in the hot rolled sheet becomes coarse
- the ferrite grain size in the annealed sheet becomes coarse
- the tensile strength decreases
- the tensile strength and elongation The balance will also worsen.
- the upper limit of the hot rolling finishing temperature is set to 930 ° C.
- the lower limit of the hot rolling finishing temperature is 820 ° C.
- a preferred lower limit is 860 ° C.
- the winding process is a process in which the hot-rolled sheet obtained in the hot rolling process is wound at a winding temperature of 640 ° C or lower.
- the coiling temperature exceeds 640 ° C.
- the ferrite grain size in the hot rolled sheet becomes coarse
- the ferrite grain size in the annealed sheet becomes coarse
- the tensile strength decreases
- the balance between tensile strength and elongation is poor.
- the upper limit of coiling temperature shall be 640 degreeC.
- the lower limit of the coiling temperature is not particularly defined, it is preferable to set the coiling temperature to 570 ° C. or higher from the viewpoint of generating AlN during winding, reducing the amount of dissolved N, and reducing yield elongation.
- the pickling process is a process of pickling the hot-rolled sheet after the winding process.
- the pickling conditions are not particularly limited as long as the surface scale can be removed. Pickling can be performed by a conventional method.
- the primary cold rolling process is a process in which the hot-rolled sheet after the pickling is subjected to primary cold rolling under conditions of a rolling rate of 85% or more.
- the rolling ratio of primary cold rolling needs to be 85% or more in order to refine the ferrite grain size after annealing and improve the balance between tensile strength and formability. If the rolling ratio in the primary cold rolling becomes too large, the anisotropy of tensile properties becomes large, and the can-making ability may be lowered. For this reason, it is preferable that the rolling rate of primary cold rolling shall be 90% or less.
- the continuous annealing step is a step of continuously annealing the cold-rolled sheet obtained in the primary cold rolling step under conditions of an annealing temperature of 620 ° C or higher and 690 ° C or lower.
- an annealing temperature of 620 ° C or higher and 690 ° C or lower.
- the annealing temperature needs to be 620 ° C. or higher.
- the annealing temperature is too high, the ferrite grain size becomes coarse, so the annealing temperature needs to be 690 ° C. or less.
- the annealing method is not limited, the continuous annealing method is preferable from the viewpoint of material uniformity.
- the secondary cold rolling process is a process in which the annealed sheet obtained in the continuous annealing process is subjected to secondary cold rolling under the condition of a rolling rate of 6 to 20%.
- the annealed plate is strengthened and thinned by secondary cold rolling.
- the rolling rate needs to be 6% or more.
- yield elongation reduces by secondary cold rolling.
- the rolling rate needs to be 20% or less.
- the rolling rate is preferably 15% or less.
- the high-strength steel plate for a two-piece can of the present invention is obtained.
- Sn plating, Ni plating, Cr plating or the like may be applied, and further an organic film such as chemical conversion treatment or lamination may be applied.
- a steel slab was obtained by melting steel containing components of steel symbols A to K shown in Table 1, with the balance being Fe and inevitable impurities.
- the obtained steel slab was heated under the conditions shown in Table 2 and then hot-rolled, wound, removed the scale by pickling, then primary cold-rolled, and each annealing temperature was adjusted in a continuous annealing furnace.
- the steel sheet was annealed for 15 s and subjected to DR rolling (secondary cold rolling) at the secondary rolling rate shown in Table 2 to obtain steel plates (steel plate symbols No. 1 to 18) having a thickness of 0.17 to 0.19 mm.
- the steel plate was subjected to chromium plating (tin-free) treatment as a surface treatment, and then a laminated steel plate coated with an organic film was produced.
- Ferrite grain size After embedding in the cross section in the rolling direction, polishing, and corroding with nital to reveal grain boundaries, the average grain size was measured by a cutting method in accordance with JIS G 0551 to evaluate the ferrite grain size.
- the results are shown in Table 3.
- the tensile strength is 480 MPa or more
- the elongation is 7% or more
- the yield elongation is 3% or less
- the ferrite particle size is less than 6.0 ⁇ m, and has excellent moldability and strength.
- any one or more of the above characteristics are inferior.
- steel plate symbols No. 9, 11, 13, and 17 have a can evaluation of “ ⁇ ”, but the tensile strength of the steel plate is low, and it is not sufficient for the bottom of the can.
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Abstract
Description
本発明の2ピース缶用高強度鋼板は、質量%で、C:0.020%以上0.080%以下、Si:0.04%以下、Mn:0.10%以上0.60%以下、P:0.02%以下、S:0.015%以下、Al:0.010%以上0.100%以下、N:0.0005%以上0.0030%以下を含有し、残部はFeおよび不可避的不純物からなる成分組成を有する。 <High-strength steel sheet for 2-piece cans>
The high-strength steel sheet for a two-piece can of the present invention is, in mass%, C: 0.020% or more and 0.080% or less, Si: 0.04% or less, Mn: 0.10% or more and 0.60% or less, P: 0.02% or less, S: 0.015% or less, Al: 0.010% or more and 0.100% or less, N: 0.0005% or more and 0.0030% or less, the balance being Fe and inevitable It has a component composition consisting of mechanical impurities.
Cは、強度向上に重要な元素である。C含有量を0.020%以上とすることで、引張強さを480MPa以上とすることができる。また、C含有量が0.080%を超えると、伸びが7%未満に低下し、製缶性が低下する。そこで、C含有量の上限を0.080%とする必要がある。また、C含有量が多いほど、フェライト粒径が微細化し、高強度化する。このため、C含有量は0.030%以上にすることが好ましい。また、製缶性の確保の観点からは、C含有量を0.060%以下とすることが好ましい。 C: 0.020% or more and 0.080% or less C is an element important for strength improvement. By setting the C content to 0.020% or more, the tensile strength can be set to 480 MPa or more. Moreover, when C content exceeds 0.080%, elongation will fall to less than 7% and can manufacturing property will fall. Therefore, the upper limit of the C content needs to be 0.080%. Moreover, the larger the C content, the finer the ferrite grain size and the higher the strength. For this reason, the C content is preferably 0.030% or more. Further, from the viewpoint of securing canability, the C content is preferably 0.060% or less.
Siを多量に含有すると、表面濃化により表面処理性が劣化し、耐食性が低下する。このため、Si含有量を0.04%以下とする必要がある。好ましくは0.03%以下である。 Si: 0.04% or less When a large amount of Si is contained, the surface treatment property deteriorates due to surface concentration, and the corrosion resistance decreases. For this reason, it is necessary to make Si content 0.04% or less. Preferably it is 0.03% or less.
Mnは、固溶強化により鋼板の硬度を向上させる効果を有する。また、MnがMnSを形成することで、鋼中に含まれるSに起因する熱間延性の低下を防止できる。これらの効果を得るためにはMn含有量を0.10%以上にすることが必要である。特に、Mnによる固溶強化によりDR圧延での圧延率を低減しても引張強さが確保できるようにするために、Mn含有量を0.30%以上にすることが好ましい。Mn含有量が0.60%を超えると、伸びが著しく低下し、製缶性が低下するため、Mn含有量を0.60%以下とする必要がある。 Mn: 0.10% or more and 0.60% or less Mn has an effect of improving the hardness of the steel sheet by solid solution strengthening. Moreover, since Mn forms MnS, it is possible to prevent a decrease in hot ductility due to S contained in the steel. In order to acquire these effects, it is necessary to make Mn content 0.10% or more. In particular, the Mn content is preferably set to 0.30% or more so that tensile strength can be secured even if the rolling rate in DR rolling is reduced by solid solution strengthening with Mn. If the Mn content exceeds 0.60%, the elongation is remarkably lowered and the can-making ability is lowered. Therefore, the Mn content needs to be 0.60% or less.
Pを多量に含有すると過剰な硬質化や中央偏析より成形性が低下する。また、Pを多量に含有すると耐食性が低下する。そこで、P含有量の上限は0.02%とする。 P: 0.02% or less When a large amount of P is contained, formability is deteriorated due to excessive hardening or central segregation. Further, when P is contained in a large amount, the corrosion resistance is lowered. Therefore, the upper limit of the P content is 0.02%.
Sは、鋼中で硫化物を形成して、熱間延性を低下させる。よって、S含有量の上限は0.015%以下とする。 S: 0.015% or less S forms sulfides in steel and reduces hot ductility. Therefore, the upper limit of the S content is 0.015% or less.
Alは、NとAlNを形成することにより、鋼中の固溶Nを減少させて、降伏伸びを低下させ、ストレッチャーストレインを抑制する。このため、Al含有量を0.010%以上にする必要がある。降伏伸びを低減して製缶性を向上させる観点から、Al含有量は0.050%以上であることが好ましく、0.060%以上であることがさらに好ましい。また、Al含有量が過剰になるとアルミナが多量に発生して、アルミナが鋼板内に残存して製缶性が低下する。そこで、Al含有量を0.100%以下とする必要がある。好ましくは0.080%以下である。 Al: 0.010% or more and 0.100% or less Al forms N and AlN, thereby reducing solid solution N in the steel, lowering the yield elongation and suppressing stretcher strain. For this reason, it is necessary to make Al content 0.010% or more. From the viewpoint of reducing yield elongation and improving canability, the Al content is preferably 0.050% or more, and more preferably 0.060% or more. Further, when the Al content is excessive, a large amount of alumina is generated, and alumina remains in the steel sheet, resulting in a decrease in canability. Therefore, the Al content needs to be 0.100% or less. Preferably it is 0.080% or less.
Nは固溶Nとして存在すると、降伏伸びが増加し、ストレッチャーストレインが発生して、表面外観が不良となり、製缶性が低下する。このため、N含有量を0.0030%以下とする必要がある。好ましくは0.0025%以下である。一方、N含有量を安定して0.0005%未満とするのは難しく、N含有量を0.0005%未満にしようとすると製造コストも上昇する。このため、N含有量の下限は0.0005%とする。 N: 0.0005% or more and 0.0030% or less When N is present as a solid solution N, yield elongation increases, stretcher strain occurs, the surface appearance becomes poor, and the can-making ability decreases. For this reason, N content needs to be 0.0030% or less. Preferably it is 0.0025% or less. On the other hand, it is difficult to stably make the N content less than 0.0005%, and if the N content is made less than 0.0005%, the manufacturing cost also increases. For this reason, the lower limit of the N content is 0.0005%.
Bは、NとBNを形成して、固溶Nを減少させて、降伏伸びを低下させる。このため、Bを含有することが好ましく、B添加の効果を得るためには、B含有量は0.0001%以上であることが好ましく、0.0003%以上であることがさらに好ましい。また、Bを過剰に含有しても、上記の効果が飽和するだけではなく、伸びが低下したり、異方性が劣化して製缶性が低下したりする。そこで、B含有量の上限を0.0030%とすることが好ましい。 B: 0.0001 to 0.0030%
B forms N and BN, reduces the solute N, and lowers the yield elongation. For this reason, it is preferable to contain B, and in order to obtain the effect of addition of B, the B content is preferably 0.0001% or more, and more preferably 0.0003% or more. Moreover, even if it contains B excessively, not only said effect will be saturated, but elongation will fall or anisotropy will deteriorate and can-making property will fall. Therefore, the upper limit of the B content is preferably 0.0030%.
缶底部の強度を確保するためには、鋼板の引張強さを480MPa以上とする必要がある。好ましくは490MPa以上である。なお、鋼板の引張強さは、実施例に記載の方法で測定して得られる値を採用する。また、本発明では、通常、引張強さは580MPa以下である。 Tensile strength: 480 MPa or more In order to ensure the strength of the bottom of the can, the tensile strength of the steel plate needs to be 480 MPa or more. Preferably it is 490 MPa or more. In addition, the value obtained by measuring with the method as described in an Example is employ | adopted for the tensile strength of a steel plate. In the present invention, the tensile strength is usually 580 MPa or less.
絞り・しごき加工に加えて、ビードなどの缶胴加工性を確保するためには伸びを7%以上にすることが必要である。好ましくは9%以上である。鋼成分を所定の範囲に含有させ、かつ、後述する製造条件にて、フェライト粒径を微細にすることで、480MPa以上の高強度でありながら、伸びを7%以上にすることが出来、製缶性を確保することが可能となる。なお、鋼板の伸びは、実施例に記載の方法で測定して得られる値を採用する。また、本発明では、通常、伸びは25%以下である。 Elongation: 7% or more In addition to drawing and ironing processing, it is necessary to increase the elongation to 7% or more in order to ensure the processability of can bodies such as beads. Preferably it is 9% or more. By containing the steel components in a predetermined range and making the ferrite grain size finer under the manufacturing conditions described later, the elongation can be increased to 7% or more while being high strength of 480 MPa or more. It becomes possible to ensure canability. In addition, the value obtained by measuring with the method as described in an Example is employ | adopted for the elongation of a steel plate. In the present invention, the elongation is usually 25% or less.
製缶時のストレッチャーストレインを防止するため、降伏伸びを3%以下とする必要がある。好ましくは2%以下である。なお、鋼板の降伏伸びは、実施例に記載の方法で測定して得られる値を採用する。 Yield elongation: 3% or less Yield elongation needs to be 3% or less in order to prevent stretcher strain during canning. Preferably it is 2% or less. In addition, the value obtained by measuring with the method as described in an Example is employ | adopted for the yield elongation of a steel plate.
鋼板の成分組成を上記のように調整することに加えて、フェライト粒径を微細化することにより、高強度化と伸びのバランスが向上する。このため、フェライト粒径を6.0μm未満とする必要がある。また、フェライト粒径を6.0μm未満に微細化し、降伏伸びを3%以下に低減することで、鋼板に被覆される樹脂と鋼板表面との密着性を向上させる効果もある。この観点からフェライト粒径は5.5μm以下とすることが好ましい。なお、実施例に記載の通り、粒径は平均結晶粒径を意味する。 Ferrite particle size: less than 6 μm In addition to adjusting the component composition of the steel sheet as described above, the balance between increasing strength and elongation is improved by reducing the ferrite particle size. For this reason, it is necessary to make a ferrite particle size less than 6.0 micrometers. Further, by reducing the ferrite grain size to less than 6.0 μm and reducing the yield elongation to 3% or less, there is an effect of improving the adhesion between the resin coated on the steel sheet and the steel sheet surface. From this point of view, the ferrite grain size is preferably 5.5 μm or less. In addition, as described in the Examples, the particle size means an average crystal particle size.
本発明の2ピース缶用高強度鋼板の製造方法の一例としては、加熱工程と、熱間圧延工程と、巻取り工程と、酸洗工程と、一次冷間圧延工程と、連続焼鈍工程と、二次冷間圧延工程とを有する製造方法が挙げられる。以下、各工程について説明する。 <Method for producing high-strength steel plate for 2-piece can>
As an example of a method for producing a high-strength steel sheet for a two-piece can of the present invention, a heating step, a hot rolling step, a winding step, a pickling step, a primary cold rolling step, a continuous annealing step, The manufacturing method which has a secondary cold rolling process is mentioned. Hereinafter, each step will be described.
加熱工程とは、スラブを加熱温度1130℃以上に加熱する工程である。熱間圧延前の加熱温度が低すぎると、AlNの一部が未溶解となる。この未溶解は、製缶性を低下させる粗大AlN発生の要因となる。そこで、加熱工程における加熱温度は、1130℃以上とする。好ましくは1150℃以上である。加熱温度の上限は特に規定しないが、加熱温度が高すぎるとスケールが過剰に発生して製品表面の欠陥になる。そこで、加熱温度の上限は1260℃とすることが好ましい。 Heating step The heating step is a step of heating the slab to a heating temperature of 1130 ° C or higher. When the heating temperature before hot rolling is too low, a part of AlN becomes undissolved. This undissolved becomes a cause of generation of coarse AlN that lowers the canability. Therefore, the heating temperature in the heating process is set to 1130 ° C. or higher. Preferably it is 1150 degreeC or more. The upper limit of the heating temperature is not particularly defined, but if the heating temperature is too high, excessive scale is generated, resulting in defects on the product surface. Therefore, the upper limit of the heating temperature is preferably 1260 ° C.
熱間圧延工程とは、加熱工程後のスラブを、熱延仕上げ温度820~930℃の条件で熱間圧延する工程である。熱延仕上げ圧延温度が、930℃よりも高くなると、熱延板におけるフェライトの粒径が粗大になって、焼鈍板のフェライト粒径が粗大になり、引張強さが低下し、引張強さと伸びのバランスも悪くなる。このため、熱延仕上げ温度の上限を930℃とする。また、熱延仕上げ温度が820℃未満となると、引張特性の異方性が大きくなり、製缶性が低下する。そこで、熱延仕上げ温度の下限は820℃とする。好ましい下限は860℃である。 Hot rolling process The hot rolling process is a process in which the slab after the heating process is hot rolled under the condition of a hot rolling finishing temperature of 820 to 930 ° C. When the hot rolling finish rolling temperature is higher than 930 ° C., the ferrite grain size in the hot rolled sheet becomes coarse, the ferrite grain size in the annealed sheet becomes coarse, the tensile strength decreases, and the tensile strength and elongation. The balance will also worsen. For this reason, the upper limit of the hot rolling finishing temperature is set to 930 ° C. On the other hand, when the hot rolling finishing temperature is less than 820 ° C., the anisotropy of the tensile properties increases, and the can-making property is lowered. Therefore, the lower limit of the hot rolling finishing temperature is 820 ° C. A preferred lower limit is 860 ° C.
巻取り工程とは、熱間圧延工程で得られた熱延板を巻取り温度640℃以下にて巻取る工程である。巻取温度が640℃を超えると、熱延板におけるフェライトの粒径が粗大になって、焼鈍板のフェライト粒径が粗大になり、引張強さが低下し、引張強さと伸びのバランスも悪くなる。このため、巻取り温度の上限を640℃とする。巻取り温度の下限は特に定めないが、巻取り中にAlNを生成させて、固溶N量を減少させ、降伏伸びを低減させる観点から、巻取り温度を570℃以上とすることが好ましい。 Winding process The winding process is a process in which the hot-rolled sheet obtained in the hot rolling process is wound at a winding temperature of 640 ° C or lower. When the coiling temperature exceeds 640 ° C., the ferrite grain size in the hot rolled sheet becomes coarse, the ferrite grain size in the annealed sheet becomes coarse, the tensile strength decreases, and the balance between tensile strength and elongation is poor. Become. For this reason, the upper limit of coiling temperature shall be 640 degreeC. Although the lower limit of the coiling temperature is not particularly defined, it is preferable to set the coiling temperature to 570 ° C. or higher from the viewpoint of generating AlN during winding, reducing the amount of dissolved N, and reducing yield elongation.
酸洗工程とは、巻取り工程後の熱延板を酸洗する工程である。酸洗条件は表層スケールが除去できればよく、特に条件は規定しない。常法により、酸洗することができる。 Pickling process The pickling process is a process of pickling the hot-rolled sheet after the winding process. The pickling conditions are not particularly limited as long as the surface scale can be removed. Pickling can be performed by a conventional method.
一次冷間圧延工程とは、上記酸洗後の熱延板を圧延率85%以上の条件で一次冷間圧延する工程である。一次冷間圧延の圧延率は、焼鈍後のフェライト粒径を微細化させ、引張強さと成形性のバランスを向上させるために85%以上とする必要がある。一次冷間圧延における圧延率が大きくなりすぎると、引張特性の異方性が大となり、製缶性が低下する場合がある。このため、一次冷間圧延の圧延率は90%以下とすることが好ましい。 Primary cold rolling process The primary cold rolling process is a process in which the hot-rolled sheet after the pickling is subjected to primary cold rolling under conditions of a rolling rate of 85% or more. The rolling ratio of primary cold rolling needs to be 85% or more in order to refine the ferrite grain size after annealing and improve the balance between tensile strength and formability. If the rolling ratio in the primary cold rolling becomes too large, the anisotropy of tensile properties becomes large, and the can-making ability may be lowered. For this reason, it is preferable that the rolling rate of primary cold rolling shall be 90% or less.
連続焼鈍工程とは、一次冷間圧延工程で得られた冷延板を、焼鈍温度620℃以上690℃以下の条件で連続焼鈍する工程である。成形性の確保のため、焼鈍中に十分に再結晶させる必要があるため、焼鈍温度を620℃以上とする必要がある。また、焼鈍温度が高すぎると、フェライト粒径が粗大化するため、焼鈍温度は690℃以下とする必要がある。焼鈍方法は限定するものではないが、材質の均一性の観点から連続焼鈍法が好ましい。 Continuous annealing step The continuous annealing step is a step of continuously annealing the cold-rolled sheet obtained in the primary cold rolling step under conditions of an annealing temperature of 620 ° C or higher and 690 ° C or lower. In order to ensure formability, it is necessary to sufficiently recrystallize during annealing, so the annealing temperature needs to be 620 ° C. or higher. Further, if the annealing temperature is too high, the ferrite grain size becomes coarse, so the annealing temperature needs to be 690 ° C. or less. Although the annealing method is not limited, the continuous annealing method is preferable from the viewpoint of material uniformity.
二次冷間圧延工程とは、連続焼鈍工程で得られた焼鈍板を、圧延率6~20%の条件で二次冷間圧延する工程である。焼鈍板は、二次冷間圧延により高強度化され、かつ薄肉化される。高強度化を十分に図るためには、圧延率を6%以上とする必要がある。また、二次冷間圧延によって、降伏伸びが低減する。また、二次冷間圧延における圧延率が高すぎると、成形性が劣化する。そこで、圧延率は20%以下とする必要がある。特に成形性が要求される場合には、圧延率を15%以下とすることが好ましい。 Secondary cold rolling process The secondary cold rolling process is a process in which the annealed sheet obtained in the continuous annealing process is subjected to secondary cold rolling under the condition of a rolling rate of 6 to 20%. The annealed plate is strengthened and thinned by secondary cold rolling. In order to sufficiently increase the strength, the rolling rate needs to be 6% or more. Moreover, yield elongation reduces by secondary cold rolling. Moreover, if the rolling rate in the secondary cold rolling is too high, the formability deteriorates. Therefore, the rolling rate needs to be 20% or less. In particular, when formability is required, the rolling rate is preferably 15% or less.
上記ラミネート鋼板から、濃硫酸にて有機被覆を除去した後、圧延向からJIS5号引張試験片を採取しJIS Z 2241に従い、引張強さ、伸び(全伸び)、降伏伸びを評価した。 Tensile Strength, Elongation, Yield Elongation After removing the organic coating with concentrated sulfuric acid from the laminated steel sheet, a JIS No. 5 tensile test piece was taken from the rolling direction, and in accordance with JIS Z 2241, tensile strength, elongation (total elongation), Yield elongation was evaluated.
圧延方向断面に埋め込み、研磨後、ナイタールにて腐食して粒界を現出したのち、JIS G 0551に従い、切断法にて平均結晶粒径を測定し、フェライト粒径を評価した。 Ferrite grain size After embedding in the cross section in the rolling direction, polishing, and corroding with nital to reveal grain boundaries, the average grain size was measured by a cutting method in accordance with JIS G 0551 to evaluate the ferrite grain size.
製缶性を評価するため、上記のラミネート鋼板を円形に打抜いた後、深絞り加工、しごき加工等を施して、円筒形に製缶した後、缶胴部の高さ中央および上下15mmの計3箇所に缶周方向にビード加工を行い、飲料缶で適用されている2ピース缶と同様の缶体を成形した。製缶時に破胴が無く、ストレッチャーストレインがほとんど見えないものを「◎」、破胴は無いが軽微なストレインストレッチャーが認められるものを「○」、破胴ないしストレインストレッチャーの顕著なものを「×」とした。 Evaluation of can manufacturing In order to evaluate the can manufacturing performance, after punching the above laminated steel sheet into a circular shape, deep drawing, ironing, etc. were performed to make a cylindrical shape. Bead processing was performed in the can circumferential direction at a total of three places of 15 mm in the vertical direction, and a can body similar to a two-piece can applied in a beverage can was formed. "◎" if there is no destructuring and almost no visible stretcher strain when making cans, "○" if there is no destructuring but a slight strain stretcher is recognized Was marked “x”.
Claims (3)
- 質量%で、C:0.020%以上0.080%以下、Si:0.04%以下、Mn:0.10%以上0.60%以下、P:0.02%以下、S:0.015%以下、Al:0.010%以上0.100%以下、N:0.0005%以上0.0030%以下を含有し、残部はFeおよび不可避的不純物からなり、
引張強さが480MPa以上であり、
伸びが7%以上であり、
降伏伸びが3%以下であり、
フェライト粒径が6μm未満であることを特徴とする2ピース缶用鋼板。 In mass%, C: 0.020% to 0.080%, Si: 0.04% or less, Mn: 0.10% to 0.60%, P: 0.02% or less, S: 0.00. 015% or less, Al: 0.010% or more and 0.100% or less, N: 0.0005% or more and 0.0030% or less, with the balance being Fe and inevitable impurities,
The tensile strength is 480 MPa or more,
Elongation is 7% or more,
Yield elongation is 3% or less,
A steel plate for a two-piece can having a ferrite grain size of less than 6 μm. - さらに、質量%で、B:0.0001%以上0.0030%以下を含有することを特徴とする請求項1に記載の2ピース缶用鋼板。 The steel sheet for a two-piece can according to claim 1, further comprising B: 0.0001% to 0.0030% in mass%.
- 請求項1又は2に記載の2ピース缶用鋼板の製造方法であって、
スラブを加熱温度1130℃以上にて加熱する加熱工程と、
前記加熱工程後のスラブを、熱延仕上げ温度820~930℃の条件で熱間圧延する熱間圧延工程と、
前記熱間圧延工程で得られた熱延板を巻取り温度640℃以下にて巻取る巻取り工程と、
前記巻取り工程後の熱延板を酸洗する酸洗工程と、
前記酸洗後の熱延板を圧延率85%以上の条件で一次冷間圧延する一次冷間圧延工程と、
前記一次冷間圧延工程で得られた冷延板を、焼鈍温度620℃以上690℃以下の条件で連続焼鈍する連続焼鈍工程と、
前記連続焼鈍工程で得られた焼鈍板を、圧延率6~20%の条件で二次冷間圧延する二次冷間圧延工程とを有することを特徴とする2ピース缶用鋼板の製造方法。
It is a manufacturing method of the steel plate for 2 piece cans according to claim 1 or 2,
A heating step of heating the slab at a heating temperature of 1130 ° C. or higher;
A hot rolling process in which the slab after the heating process is hot-rolled at a hot rolling finishing temperature of 820 to 930 ° C .;
A winding step of winding the hot-rolled sheet obtained in the hot rolling step at a winding temperature of 640 ° C. or less;
Pickling process of pickling hot-rolled sheet after the winding process;
A primary cold rolling step of primary cold rolling the hot-rolled sheet after pickling under a condition of a rolling rate of 85% or more;
A continuous annealing step of continuously annealing the cold-rolled sheet obtained in the primary cold rolling step under conditions of an annealing temperature of 620 ° C. or more and 690 ° C. or less;
A method for producing a steel plate for a two-piece can, comprising a secondary cold rolling step of subjecting the annealed plate obtained in the continuous annealing step to secondary cold rolling under conditions of a rolling rate of 6 to 20%.
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
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US15/520,476 US20170306436A1 (en) | 2014-10-28 | 2015-09-18 | Steel sheet for two-piece can and manufacturing method therefor |
JP2016504242A JP6274302B2 (en) | 2014-10-28 | 2015-09-18 | Steel plate for 2-piece can and manufacturing method thereof |
KR1020177010597A KR101989712B1 (en) | 2014-10-28 | 2015-09-18 | Steel sheet for two-piece can and manufacturing method therefor |
CN201580059933.0A CN107002190B (en) | 2014-10-28 | 2015-09-18 | Two panels steel plate for tanks and its manufacturing method |
PH12017500433A PH12017500433B1 (en) | 2014-10-28 | 2017-03-08 | Steel sheet for two-piece can and manufacturing method therefor |
Applications Claiming Priority (2)
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JP2014-218967 | 2014-10-28 | ||
JP2014218967 | 2014-10-28 |
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WO2016067514A1 true WO2016067514A1 (en) | 2016-05-06 |
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PCT/JP2015/004784 WO2016067514A1 (en) | 2014-10-28 | 2015-09-18 | Steel sheet for two-piece can and manufacturing method therefor |
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US (1) | US20170306436A1 (en) |
JP (1) | JP6274302B2 (en) |
KR (1) | KR101989712B1 (en) |
CN (1) | CN107002190B (en) |
MY (1) | MY178159A (en) |
PH (1) | PH12017500433B1 (en) |
TW (1) | TWI604067B (en) |
WO (1) | WO2016067514A1 (en) |
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WO2018180404A1 (en) * | 2017-03-27 | 2018-10-04 | Jfeスチール株式会社 | Steel sheet for two-piece can and production method therefor |
KR20190132451A (en) * | 2017-03-27 | 2019-11-27 | 제이에프이 스틸 가부시키가이샤 | Steel plate for two-piece can and its manufacturing method |
CN113748220A (en) * | 2019-03-29 | 2021-12-03 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
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JP6028884B1 (en) * | 2015-03-31 | 2016-11-24 | Jfeスチール株式会社 | Steel plate for cans and method for producing steel plate for cans |
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- 2015-09-18 WO PCT/JP2015/004784 patent/WO2016067514A1/en active Application Filing
- 2015-09-18 US US15/520,476 patent/US20170306436A1/en not_active Abandoned
- 2015-09-18 CN CN201580059933.0A patent/CN107002190B/en active Active
- 2015-09-18 KR KR1020177010597A patent/KR101989712B1/en active IP Right Grant
- 2015-09-18 MY MYPI2017701392A patent/MY178159A/en unknown
- 2015-09-18 JP JP2016504242A patent/JP6274302B2/en active Active
- 2015-10-05 TW TW104132699A patent/TWI604067B/en active
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2017
- 2017-03-08 PH PH12017500433A patent/PH12017500433B1/en unknown
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JPH07258795A (en) * | 1994-03-23 | 1995-10-09 | Nippon Steel Corp | Fine grain hot rolled steel sheet and its production |
JPH09249919A (en) * | 1996-03-14 | 1997-09-22 | Nkk Corp | Production of extremely thin steel sheet for two piece can small in plane anisotropy |
JPH11124654A (en) * | 1997-08-18 | 1999-05-11 | Kawasaki Steel Corp | Steel sheet for can, and its production |
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WO2018180404A1 (en) * | 2017-03-27 | 2018-10-04 | Jfeスチール株式会社 | Steel sheet for two-piece can and production method therefor |
JP6455640B1 (en) * | 2017-03-27 | 2019-01-23 | Jfeスチール株式会社 | Steel plate for 2-piece can and manufacturing method thereof |
KR20190121810A (en) * | 2017-03-27 | 2019-10-28 | 제이에프이 스틸 가부시키가이샤 | Steel plate for two-piece can and its manufacturing method |
CN110462086A (en) * | 2017-03-27 | 2019-11-15 | 杰富意钢铁株式会社 | Two panels steel plate for tanks and its manufacturing method |
KR20190132451A (en) * | 2017-03-27 | 2019-11-27 | 제이에프이 스틸 가부시키가이샤 | Steel plate for two-piece can and its manufacturing method |
KR102262364B1 (en) * | 2017-03-27 | 2021-06-07 | 제이에프이 스틸 가부시키가이샤 | Steel plate for two-piece can and manufacturing method thereof |
KR102268800B1 (en) * | 2017-03-27 | 2021-06-23 | 제이에프이 스틸 가부시키가이샤 | Steel plate for two-piece can and manufacturing method thereof |
CN110462086B (en) * | 2017-03-27 | 2021-08-17 | 杰富意钢铁株式会社 | Two-piece steel sheet for can and method for producing same |
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CN113748220A (en) * | 2019-03-29 | 2021-12-03 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
Also Published As
Publication number | Publication date |
---|---|
PH12017500433A1 (en) | 2017-07-31 |
TWI604067B (en) | 2017-11-01 |
CN107002190A (en) | 2017-08-01 |
US20170306436A1 (en) | 2017-10-26 |
PH12017500433B1 (en) | 2017-07-31 |
MY178159A (en) | 2020-10-06 |
JP6274302B2 (en) | 2018-02-07 |
JPWO2016067514A1 (en) | 2017-04-27 |
KR20170063744A (en) | 2017-06-08 |
CN107002190B (en) | 2019-03-05 |
TW201632636A (en) | 2016-09-16 |
KR101989712B1 (en) | 2019-06-14 |
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