US20110108168A1 - High-strength steel sheet for can and method for manufacturing same - Google Patents
High-strength steel sheet for can and method for manufacturing same Download PDFInfo
- Publication number
- US20110108168A1 US20110108168A1 US12/933,117 US93311709A US2011108168A1 US 20110108168 A1 US20110108168 A1 US 20110108168A1 US 93311709 A US93311709 A US 93311709A US 2011108168 A1 US2011108168 A1 US 2011108168A1
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- US
- United States
- Prior art keywords
- slab
- steel sheet
- continuous casting
- annealing
- strength steel
- 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.)
- Abandoned
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 81
- 239000010959 steel Substances 0.000 title claims abstract description 81
- 238000000034 method Methods 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000009749 continuous casting Methods 0.000 claims abstract description 25
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 14
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 238000000137 annealing Methods 0.000 claims description 29
- 238000005452 bending Methods 0.000 claims description 16
- 238000005097 cold rolling Methods 0.000 claims description 12
- 230000009466 transformation Effects 0.000 claims description 10
- 239000004922 lacquer Substances 0.000 claims description 6
- 238000005336 cracking Methods 0.000 abstract description 24
- 238000005728 strengthening Methods 0.000 description 20
- 239000006104 solid solution Substances 0.000 description 17
- 238000005096 rolling process Methods 0.000 description 12
- 238000012937 correction Methods 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 230000009467 reduction Effects 0.000 description 8
- 238000009864 tensile test Methods 0.000 description 7
- 239000004615 ingredient Substances 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000004804 winding Methods 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000007747 plating Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 239000005029 tin-free steel Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 235000013361 beverage Nutrition 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
Classifications
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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
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
-
- 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
-
- 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
- C21D8/0442—Flattening; Dressing; Flexing
-
- 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
- C21D8/0473—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- 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
- 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
Definitions
- This disclosure relates to a steel sheet for a can, the steel sheet having high strength and being free from slab cracking during continuous casting, and a method for manufacturing the steel sheet.
- cost-cutting measures for the manufacturing cost of cans have been taken to expand the demand for steel cans.
- An example of the cost-cutting measures for the manufacturing cost of cans is a reduction in raw-material cost.
- a simple reduction in the thickness of a conventional steel sheet reduces the strength of a can body.
- high-strength thin steel sheet for a can is desired for these uses.
- JP 5-195073 discloses a method including subjecting a steel containing 0.07%-0.20% C, 0.50%-1.50% Mn, 0.025% or less S, 0.002%-0.100% Al, and 0.012% or less N to rolling, continuous annealing, and skin pass rolling to afford a steel sheet having a proof stress of 56 kgf/mm 2 or more.
- JP 59-50125 discloses a method including subjecting a steel containing 0.13% or less C, 0.70% or less Mn, 0.050% or less S, and 0.015% or less N to rolling and continuous annealing and that a steel sheet has a yield stress of about 65 kgf/mm 2 after lacquer baking in an Example.
- JP 62-30848 discloses a method including subjecting a steel containing 0.03%-0.10% C, 0.15%-0.50% Mn, 0.02% or less S, 0.065% Al, and 0.004%-0.010% N to rolling, continuous annealing, and skin pass rolling to afford a steel sheet having a yield stress of 500 ⁇ 50 N/mm 2 .
- JP 2000-26921 discloses a method including subjecting a steel containing 0.1% or less C and 0.001%-0.015% N to rolling, continuous annealing, overaging, and skin pass rolling to afford a steel sheet having a temper designation of up to T6 (a hardness of about 70 (HR30T)).
- a steel sheet having a yield strength of about 420 MPa is used for bodies of three-piece cans.
- the steel sheet is required to have a thickness reduced by several percent. It is necessary to have a yield strength of 450 MPa or more to meet the requirement and maintain the strength of can bodies.
- a steel corner In the case where a steel having high C and N contents is produced and formed into a slab, cracking can occur at a corner (hereinafter, referred to as a “slab corner”) of a long side and a short side of the cross section of the slab in a continuous casting process.
- the slab corner In the case of a vertical-bending type or bow type continuous casting machine, the slab undergoes bending deformation or unbending deformation (only in the vertical-bending type continuous casting machine) at high temperatures.
- Such a steel with high C and N contents has poor high temperature ductility, thus causing cracking during deformation.
- the slab corner When the slab corner is cracked, it is necessary to perform, for example, surface grinding. This disadvantageously causes a reduction in yield and an increase in cost.
- the high-strength steel sheets described in the related art have high proportions of C and N, which function as solid-solution strengthening elements, and thus are highly likely to be cracked at slab corners in a continuous casting process.
- the ductility of the steel described above is reduced in the range above 800° C. and below 900° C.
- the operation is performed in such a manner that the temperatures of a slab corner in a region (hereinafter, referred to as a “correction zone”) where a slab undergoes bending deformation or unbending deformation in continuous casting are not within the temperature range, thereby more assuredly preventing the cracking at the slab corner.
- % indicates the units of the content of each ingredient in the steel and means % by mass.
- high-strength steel sheet for a can is used to indicate a steel sheet for a can, the steel sheet having a yield strength of 450 MPa or more.
- a steel sheet for a can is a high-strength steel sheet for a can, the steel sheet having a yield strength of 450 MPa or more.
- Solid-solution strengthening using C and N and solid-solution strengthening and grain refinement strengthening using P and Mn result in a steel sheet having a higher strength than a conventional steel sheet for a can, the conventional steel sheet having a yield strength of 420 MPa.
- a steel sheet for a can it is essential to achieve predetermined strength or more (a yield strength of 450 MPa or more) after continuous annealing, skin pass rolling, and lacquer baking.
- the amount of C added is important, C functioning as a solid-solution strengthening element.
- the lower limit of the C content is set to 0.03%. Meanwhile, at a C content exceeding 0.10%, cracking at a slab corner is not prevented even when S and Al contents are regulated in a range described below.
- the upper limit of the C content is set to 0.10%.
- the C content is in the range of 0.04% to 0.07%.
- Si is an element that increases the strength of steel by solid-solution strengthening. A large amount of Si added causes a significant reduction in corrosion resistance. Thus, the Si content is in the range of 0.01% to 0.5%.
- P is an element that has a great ability for solid-solution strengthening. A large amount of P added causes a significant reduction in corrosion resistance. Thus, the upper limit is set to 0.100%. Meanwhile, a P content of less than 0.001% causes an excessively large dephosphorization cost. Thus, the lower limit of the P content is set to 0.001%.
- S is an impurity derived from a blast furnace feed material. S combines with Mn in steel to form MnS. The precipitation of MnS at grain boundaries at high temperatures leads to embrittlement. Meanwhile, the addition of Mn is needed to ensure strength. It is necessary to reduce the S content to inhibit the precipitation of MnS, thereby preventing cracking at a slab corner.
- the upper limit of the S content is set to 0.020% and preferably 0.005% or less. Furthermore, a S content of less than 0.001% causes an excessively large desulfurization cost. Thus, the lower limit is set to 0.001%.
- Al functions as a deoxidant and is an element needed to increase the cleanness of steel.
- Al combines with N in steel to form AlN. Like MnS, this segregates at grain boundaries to cause high-temperature embrittlement. A large amount of N is contained to ensure strength. Thus, to prevent embrittlement, it is necessary to reduce the Al content.
- the upper limit of the Al content is set to 0.10% and preferably 0.04% or less. Meanwhile, an Al content of a steel of less than 0.01% can cause insufficient deoxidation. The lower limit of the Al content is therefore set to 0.01%.
- N is an element that contributes to solid-solution strengthening.
- N is preferably added in an amount of 0.005% or more. Meanwhile, a large amount of N added causes a deterioration in hot ductility, so that cracking at a slab corner is inevitable even when the S content is regulated within the range described above.
- the upper limit of the N content is set to 0.012%.
- the balance is set to Fe and incidental impurities.
- the steel has microstructures that do not contain a pearlite microstructure.
- the pearlite microstructure is a lamellar microstructure of ferrite phases and cementite phases.
- the presence of a coarse pearlite microstructure causes voids and cracks due to stress concentration, reducing the ductility in a temperature region below the A 1 transformation point.
- a three-piece beverage can may be subjected to necking in which both ends of the can body are reduced in diameter. Furthermore, to roll the top and the bottom into flanges, flanging is performed in addition to necking Insufficient ductility at room temperature causes cracking in a steel sheet during the severe processing. Thus, to avoid a reduction in ductility at room temperature, the microstructures do not contain the pearlite microstructure.
- a method for manufacturing a steel sheet for a can will be described below.
- the hot rolling may be performed according to a common method.
- the thickness after the hot rolling is not particularly specified.
- the thickness is preferably 2 mm or less.
- the finishing temperature and the winding temperature are not particularly specified.
- the finishing temperature is preferably set to 850° C. to 930° C.
- the winding temperature is preferably set to 550° C. to 650° C.
- cold rolling is performed.
- the cold rolling is preferably performed at a draft of 80% or more. This is performed to crush pearlite microstructures formed after the hot rolling. A draft of less than 80% in the cold rolling allows the pearlite microstructures to be left. Thus, the draft in the cold rolling is set to 80% or more.
- the upper limit of the draft is not particularly specified. An excessively large draft causes an excessively large load imposed on a rolling mill, leading to faulty rolling. Hence, the draft is preferably 95% or less.
- the annealing temperature is set to a temperature below the A 1 transformation point.
- An annealing temperature of the A 1 transformation point or higher causes the formation of an austenite phase during the annealing.
- the austenite phase is transformed into pearlite microstructures in a cooling process after the annealing.
- the annealing temperature is set to a temperature below the A 1 transformation point.
- a known method for example, continuous annealing or batch annealing, may be employed.
- the resulting steel slabs were reheated to 1250° C., hot-rolled at a roll finishing temperature ranging from 880° C. to 900° C., cooled at an average cooling rate of 20 to 40 ° C./s until winding, and wound at a winding temperature ranging from 580° C. to 620° C.
- cold rolling was performed at a draft of 90% or more, affording steel sheets for a can, each of the steel sheets having a thickness of 0.17 to 0.2 mm.
- the resulting steel sheets for a can were heated at 15 ° C./sec and subjected to continuous annealing at annealing temperatures shown in Table 1 for 20 seconds. After cooling, skin pass rolling was performed at a draft of 3% or less. Common chromium plating was continuously performed, affording tin-free steel.
- a tensile test was performed. Specifically, each of the steel sheets was processed into tensile test pieces of JIS-5 type. The tensile test was performed with an Instron tester at 10 mm/min to measure the yield strength.
- a notched tensile test was also performed.
- Each of the steel sheets was processed into a tensile test piece having a width of the parallel portion of 12.5 mm, a length of the parallel portion of 60 mm, and a gauge length of 25 mm.
- a V-notch with a depth of 2 mm was made on each side of the middle of the parallel portion.
- the resulting test pieces were used for the tensile test.
- Test pieces each having an elongation at break of 5% or more were evaluated as pass (P).
- a test piece having an elongation at break of less than 5% was evaluated as fail (F).
- Table 1 shows the results together with the conditions.
- Table 1 shows that each of Samples 1 to 8, which are Examples, has excellent strength and a yield strength of 450 MPa or more required for a reduction in the thickness of the can body of a three-piece can by several percent. Furthermore, the results demonstrate that no cracking occurs at a slab corner during the continuous casting.
- Samples 9 and 10 which are Comparative Examples, are small in Mnf and N, respectively, thus leading to insufficient strength.
- Samples 11 and 12 have a high S content and a high Al content, respectively.
- Samples 13 and 14 have the surface temperatures of the slab corners within the region above 800° C. and below 900° C. in the upper correction zone and the lower correction zone, respectively, the region being outside our range. Hence, cracking occurred at the slab corners.
- the annealing temperature is the A 1 transformation point or higher.
- the microstructure contains pearlite at room temperature, leading to insufficient ductility at room temperature.
- a steel sheet for a can has a yield strength of 450 MPa or more without cracking at a slab corner in a continuous casting process and can be suitably used for can bodies, can lids, can bottoms, tabs, and so forth of three-piece cans.
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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)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2008070517A JP5526483B2 (ja) | 2008-03-19 | 2008-03-19 | 高強度缶用鋼板およびその製造方法 |
JP2008-070517 | 2008-03-19 | ||
PCT/JP2009/056015 WO2009116680A1 (ja) | 2008-03-19 | 2009-03-18 | 高強度缶用鋼板およびその製造方法 |
Related Parent Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2009/056015 A-371-Of-International WO2009116680A1 (ja) | 2008-03-19 | 2009-03-18 | 高強度缶用鋼板およびその製造方法 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US14/487,140 Division US9879332B2 (en) | 2008-03-19 | 2014-09-16 | Method of manufacturing high-strength steel sheet for a can |
Publications (1)
Publication Number | Publication Date |
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US20110108168A1 true US20110108168A1 (en) | 2011-05-12 |
Family
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Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
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US12/933,117 Abandoned US20110108168A1 (en) | 2008-03-19 | 2009-03-18 | High-strength steel sheet for can and method for manufacturing same |
US14/487,140 Active 2031-03-21 US9879332B2 (en) | 2008-03-19 | 2014-09-16 | Method of manufacturing high-strength steel sheet for a can |
Family Applications After (1)
Application Number | Title | Priority Date | Filing Date |
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US14/487,140 Active 2031-03-21 US9879332B2 (en) | 2008-03-19 | 2014-09-16 | Method of manufacturing high-strength steel sheet for a can |
Country Status (6)
Country | Link |
---|---|
US (2) | US20110108168A1 (ja) |
EP (1) | EP2253729B2 (ja) |
JP (1) | JP5526483B2 (ja) |
KR (2) | KR20100113641A (ja) |
CN (1) | CN101978084A (ja) |
WO (1) | WO2009116680A1 (ja) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5526483B2 (ja) | 2008-03-19 | 2014-06-18 | Jfeスチール株式会社 | 高強度缶用鋼板およびその製造方法 |
EP2508641B1 (en) * | 2009-12-02 | 2015-11-04 | JFE Steel Corporation | Steel sheet for cans and method for producing same |
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 |
JP6060603B2 (ja) * | 2011-10-20 | 2017-01-18 | Jfeスチール株式会社 | フランジ加工性に優れた高強度缶用鋼板およびその製造方法 |
CN107429347B (zh) * | 2015-03-31 | 2019-06-07 | 杰富意钢铁株式会社 | 罐盖用钢板及其制造方法 |
JP6028884B1 (ja) * | 2015-03-31 | 2016-11-24 | Jfeスチール株式会社 | 缶用鋼板及び缶用鋼板の製造方法 |
EP3476964B1 (en) * | 2016-09-29 | 2021-01-27 | JFE Steel Corporation | Steel sheet for crown caps, production method therefor, and crown cap |
CN107598108A (zh) * | 2017-09-28 | 2018-01-19 | 江西理工大学 | 一种判定连铸坯发生角部横裂纹所在工序的方法 |
CN114480946B (zh) * | 2020-11-12 | 2023-06-09 | 上海梅山钢铁股份有限公司 | 一种低铝包晶钢钢水的生产方法 |
Citations (3)
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US4838955A (en) * | 1985-07-29 | 1989-06-13 | Hoogovens Groep B.V. | Method for the manufacture of hard steel sheet from Al-killed continuous-cast carbon-manganese steel |
JPH08325670A (ja) * | 1995-03-29 | 1996-12-10 | Kawasaki Steel Corp | 製缶時の深絞り性及びフランジ加工性と、製缶後の表面性状とに優れ、十分な缶強度を有する製缶用鋼板及びその製造方法 |
US20090250147A1 (en) * | 2006-08-11 | 2009-10-08 | Hiroshi Nishida | Dr Steel Sheet and Manufacturing Method Thereof |
Family Cites Families (19)
Publication number | Priority date | Publication date | Assignee | Title |
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JPS5171812A (en) | 1974-12-20 | 1976-06-22 | Toyo Kohan Co Ltd | Renzokushodon nyoru nanshitsusukohanno seizohoho |
JPS5950125A (ja) | 1982-09-17 | 1984-03-23 | Nippon Steel Corp | 製缶用高硬質高加工性薄鋼板の製造法 |
JPH075990B2 (ja) * | 1986-01-10 | 1995-01-25 | 川崎製鉄株式会社 | 硬質かつ絞り加工性に優れる異方性の小さい缶用薄鋼板の製造方法 |
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JPH08120348A (ja) * | 1994-10-21 | 1996-05-14 | Nkk Corp | 面内異方性の小さい硬質缶用鋼板の製造方法 |
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FR2769251B1 (fr) | 1997-10-03 | 1999-12-24 | Lorraine Laminage | Procede de fabrication d'une bande de tole d'acier pour la realisation d'emballages metalliques par emboutissage et tole d'acier obtenue |
JP3663918B2 (ja) * | 1998-07-02 | 2005-06-22 | Jfeスチール株式会社 | 形状維持性に優れる缶用鋼板およびその製造方法 |
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JP3931455B2 (ja) * | 1998-11-25 | 2007-06-13 | Jfeスチール株式会社 | 缶用鋼板およびその製造方法 |
FR2795743B1 (fr) | 1999-07-01 | 2001-08-03 | Lorraine Laminage | Tole d'acier a basse teneur en aluminium pour emballage |
EP1741800A1 (en) * | 2004-04-27 | 2007-01-10 | JFE Steel Corporation | Steel sheet for can and method for production thereof |
JP4525450B2 (ja) * | 2004-04-27 | 2010-08-18 | Jfeスチール株式会社 | 高強度高延性な缶用鋼板およびその製造方法 |
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2008
- 2008-03-19 JP JP2008070517A patent/JP5526483B2/ja active Active
-
2009
- 2009-03-18 US US12/933,117 patent/US20110108168A1/en not_active Abandoned
- 2009-03-18 CN CN2009801096494A patent/CN101978084A/zh active Pending
- 2009-03-18 EP EP09722774.8A patent/EP2253729B2/en active Active
- 2009-03-18 WO PCT/JP2009/056015 patent/WO2009116680A1/ja active Application Filing
- 2009-03-18 KR KR1020107020730A patent/KR20100113641A/ko active Search and Examination
- 2009-03-18 KR KR1020137004808A patent/KR20130035273A/ko not_active Application Discontinuation
-
2014
- 2014-09-16 US US14/487,140 patent/US9879332B2/en active Active
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US4838955A (en) * | 1985-07-29 | 1989-06-13 | Hoogovens Groep B.V. | Method for the manufacture of hard steel sheet from Al-killed continuous-cast carbon-manganese steel |
JPH08325670A (ja) * | 1995-03-29 | 1996-12-10 | Kawasaki Steel Corp | 製缶時の深絞り性及びフランジ加工性と、製缶後の表面性状とに優れ、十分な缶強度を有する製缶用鋼板及びその製造方法 |
US20090250147A1 (en) * | 2006-08-11 | 2009-10-08 | Hiroshi Nishida | Dr Steel Sheet and Manufacturing Method Thereof |
Also Published As
Publication number | Publication date |
---|---|
WO2009116680A1 (ja) | 2009-09-24 |
EP2253729A1 (en) | 2010-11-24 |
KR20130035273A (ko) | 2013-04-08 |
EP2253729A4 (en) | 2014-01-01 |
EP2253729B1 (en) | 2015-07-29 |
EP2253729B2 (en) | 2024-04-03 |
CN101978084A (zh) | 2011-02-16 |
JP2009221584A (ja) | 2009-10-01 |
KR20100113641A (ko) | 2010-10-21 |
US9879332B2 (en) | 2018-01-30 |
JP5526483B2 (ja) | 2014-06-18 |
US20150000798A1 (en) | 2015-01-01 |
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