WO2013008457A1 - 缶用鋼板およびその製造方法 - Google Patents
缶用鋼板およびその製造方法 Download PDFInfo
- Publication number
- WO2013008457A1 WO2013008457A1 PCT/JP2012/004467 JP2012004467W WO2013008457A1 WO 2013008457 A1 WO2013008457 A1 WO 2013008457A1 JP 2012004467 W JP2012004467 W JP 2012004467W WO 2013008457 A1 WO2013008457 A1 WO 2013008457A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel plate
- cans
- rolling
- steel
- Prior art date
Links
Images
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
- 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
- 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
- C21D8/0426—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
- C21D8/04—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
- C21D8/0468—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
-
- 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
- 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
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Definitions
- the present invention relates to a steel plate for cans used as a container material for beverages and foods and a method for producing the same, and more particularly to a steel plate for cans having excellent flange workability and high strength and a method for producing the same. .
- steel plates used for beverage cans and food cans steel plates called DR (Double Reduced) materials may be used for lids, bottoms, 3-piece can bodies, drawn cans, and the like.
- the DR material is a steel sheet that is cold-rolled again after annealing, and it is easier to reduce the plate thickness than an SR (Single-Reduced) material that performs only temper rolling with a small rolling rate. And can manufacturing cost can be reduced by using a thin steel plate.
- the DR material manufactured by the DR method has poor ductility, so that the workability is inferior to that of the SR material.
- the body of food cans and beverage cans composed of 3 pieces is molded into a cylinder and then flanged at both ends to wind the lid and bottom. Therefore, good workability (flange workability) is required at the end of the can body.
- the steel plate as a can-making material is required to have a strength (tensile strength) corresponding to the plate thickness.
- tensile strength higher than that of SR material is required to ensure the economic effect of thinning. Is done.
- Patent Document 1 contains C: 0.04 to 0.08%, where X is the total elongation value in the rolling direction, and Y is the average rankford value.
- X is the total elongation value in the rolling direction
- Y is the average rankford value.
- a steel sheet excellent in flange workability that satisfies the relationship of X ⁇ 10% and Y ⁇ ⁇ 0.05X + 1.4 is disclosed.
- Patent Document 2 contains C: more than 0.04% and 0.08% or less, and 50 ppm ⁇ solid solution C + solid solution N ⁇ 200 ppm is satisfied between C and N dissolved in the steel sheet, and the solid solution C is 50 ppm.
- a steel sheet excellent in flange formability having a solid solution N of 50 ppm or more is disclosed.
- Patent Document 3 discloses a steel sheet having excellent flange formability, containing N: 0.01% or less, and the total of C and N dissolved in the steel sheet is in the range of 40 ppm ⁇ solid solution C + solid solution N ⁇ 150 ppm. It is disclosed.
- Patent Document 4 contains N: 0.012% or less, and has a relationship of 50 ppm ⁇ solid solution C + solid solution N between C and N dissolved in the steel sheet, and is excellent in neck-in formability and flange formability.
- a steel sheet is disclosed.
- Patent Document 1 and Patent Document 2 since the amount of C is too large, local necking occurs during flange processing, and flange cracking cannot be sufficiently suppressed.
- the steels described in Patent Document 3 and Patent Document 4 have good workability because the N content is too small, but the strength is insufficient even when secondary cold rolling is performed.
- the present invention has been made in view of such circumstances, and an object of the present invention is to provide a steel plate for cans having excellent flange workability and high strength, which is suitable as a material for a three-piece can body and the like, and a method for producing the same. .
- the C content is kept low to prevent excessive hardening of the welded part, and the plastic strain ratio (hereinafter referred to as r value) is increased to increase the flange processing. It is effective to suppress the reduction in sheet thickness. Further, by adding a large amount of N, it is possible to ensure the strength, and at the same time, it is possible to prevent softening of the heat affected zone (HAZ) by AlN that is finely precipitated.
- r value plastic strain ratio
- the component composition of the steel sheet is mass%, C: 0.001% or more and less than 0.040%, Si: 0.003% or more and 0.100% or less, Mn: 0.10% to 0.60%, P: 0.001% to 0.100%, S: 0.001% or more and 0.020% or less, Al: 0.005% or more and 0.100% or less, N: Contains more than 0.0130% and less than 0.0170%, The balance contains Fe and inevitable impurities, N total- (N as AlN) is 0.0100% or more and 0.0160% or less, where N total is the total amount of N, N as AlN is the amount of N present as AlN, Steel plate for cans with an average r value exceeding 1.0.
- the component composition of the steel sheet is further mass%, Cr: 0.10% or less, Cu: 0.20% or less, Ni: 0.15% or less, Mo: 0.05% or less, Ti: 0.3% or less, Nb: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less 2.
- all% which shows the component of steel is the mass%.
- the high strength steel plate for cans is a steel plate for cans having a tensile strength in the direction perpendicular to the rolling direction of 520 MPa or more.
- a high-strength steel plate for cans which has a tensile strength in the direction perpendicular to the rolling direction of 520 MPa or more and an elongation at break of 7% or more and is excellent in flange workability.
- the present inventors produced steel sheets (DR materials) having various average r values by using steels containing various C amounts and adjusting manufacturing conditions, and flanges having C amounts and average r values.
- the effect on workability was investigated. Since the present invention is a DR material, it is difficult to measure the r value by a tensile test specified in JIS Z 2254. Therefore, the average r-value was measured using the natural vibration method described in Annex JA of JIS Z2254. Further, the flange workability was evaluated by the presence or absence of occurrence of flange cracking by forming a can body of a 190 g beverage can size.
- FIG. 1 shows the relationship between the C content, average r value, flange workability, and strength in the direction perpendicular to the rolling.
- the case where the crack occurred was marked by ⁇
- the case where a large crack (length of 1 mm or more) occurred was marked by ⁇ .
- the C content is less than 0.040%
- a steel sheet having an average r value of 1.0 or less has a flange crack. Therefore, it can be seen that in order to prevent flange cracking, the C content needs to be less than 0.040% and the average r value needs to exceed 1.0.
- the steel sheet for cans of the present invention is a high-strength steel sheet for cans that has a tensile strength in the direction perpendicular to the rolling of 520 MPa or more, an elongation at break of 7% or more, and an excellent average r value of more than 1.0.
- a steel plate is manufactured by keeping C content low and making a secondary cold rolling rate into a suitable range with respect to steel containing a lot of N. Specifically, hot rolling is performed, winding is performed at a temperature below 630 ° C., then primary cold rolling is performed at a rolling rate of 91.5% or more, followed by annealing, and then secondary rolling at a rolling rate of 20% or less. It becomes possible to manufacture by performing cold rolling. These are the most important requirements of the present invention.
- C 0.001% or more and less than 0.040%
- the C content is 0.040% or more
- the hardening of the can body weld becomes excessive, causing stress concentration in the vicinity of the weld during flange processing, leading to flange cracking.
- the C content is less than 0.001%
- the solid solution C amount necessary for securing the strength cannot be obtained, and the strength becomes insufficient.
- the C content is 0.001% or more and less than 0.040%, the strength of 520MPa or more is secured and the flange workability is improved without excessive hardening of the welded portion of the can body, so the C content is 0.001% or more and less than 0.040%.
- the C content is more preferably 0.020% or more and 0.039% or less. In order to obtain higher strength, the C content is most preferably 0.025% or more and 0.035% or less.
- the Si amount is preferably 0.100% or less. Further, if it is 0.003% or more, the necessary amount of surface treatment and corrosion resistance can be obtained without requiring an excessive refining cost. Therefore, the Si amount is preferably 0.003% or more.
- Mn 0.10% or more and 0.60% or less Mn has an effect of refining crystal grains and is an element necessary for securing a desirable material. If the Mn content is 0.10% or more, the crystal grain refinement effect can be obtained. On the other hand, when the Mn content is 0.60% or less, good characteristics can be obtained for both corrosion resistance and r value. Accordingly, the Mn content is desirably 0.10% or more and 0.60% or less.
- P 0.001% or more and 0.100% or less
- P is a harmful element that hardens steel and deteriorates workability and at the same time deteriorates corrosion resistance.
- the content is 0.100% or less, both workability and corrosion resistance can be improved, so the P content is preferably 0.100% or less.
- S 0.001% or more and 0.020% or less
- S is a harmful element that exists as an inclusion in steel and causes deterioration in ductility and corrosion resistance. If the amount of S is 0.020% or less, the amount of inclusions in the steel can be sufficiently reduced, and a decrease in ductility and corrosion resistance can be prevented. Therefore, the amount of S is preferably 0.020% or less.
- the S content is desirably 0.001% or more and 0.020% or less.
- Al 0.005% or more and 0.100% or less
- Al is an element necessary as a deoxidizer during steelmaking.
- the Al content is 0.005% or more, sufficient deoxidation is possible, inclusions are reduced, and good workability can be obtained.
- the Al content is 0.100% or less, the occurrence of surface defects due to alumina clusters or the like can be suppressed. Therefore, the Al content is desirably 0.005% or more and 0.100% or less.
- N more than 0.0130% and 0.0170% or less
- the steel sheet of the present invention ensures strength by containing a large amount of N.
- N is more than 0.0130%, a sufficient amount of N total- (N as AlN) described later can be obtained, and the necessary strength can be ensured.
- N exceeds 0.0170%, the ductility decreases, but if it is 0.0170% or less, sufficient ductility can be obtained and good flange workability can be exhibited.
- the N content is desirably more than 0.0130% and not more than 0.0170%. In order to obtain better strength and flange workability, it is more preferably 0.0140% or more and 0.0160% or less.
- N total- (N as AlN): 0.0100% or more and 0.0160% or less N contributing to strength is mainly solid solution N.
- a certain amount of solid solution N is required.
- N as AlN) can be regarded as the solute N amount. It is desirable to ensure this amount sufficiently, and if it is 0.0100% or more, the required strength can be obtained.
- the amount of N total- (N as AlN) is preferably 0.0100% or more and 0.0160% or less. Furthermore, from the viewpoint of strength and prevention of HAZ softening, it is more desirable that the amount of N total- (N as AlN) is 0.0110% or more and 0.0130% or less.
- the balance contains Fe and inevitable impurities. Furthermore, you may contain the component element generally contained in the steel plate for welding cans. For example, Cr: 0.10% or less, Cu: 0.20% or less, Ni: 0.15% or less, Mo: 0.05% or less, Ti: 0.3% or less, Nb: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less, Component elements such as Ca: 0.01% or less can be contained depending on the purpose.
- the average r value As described above, the larger the average r value, the smaller the thickness reduction during the flange processing, so that the occurrence of flange cracking can be prevented.
- the average r value should be more than 1.0. Therefore, it is desirable that the average r value is greater than 1.0.
- the average r value can be controlled by limiting the contents of C and Mn to the above-described ranges.
- the average r value can be measured and evaluated by the method shown in Annex JA of JIS Z 2254.
- Tensile strength in the direction perpendicular to rolling is 520 MPa or more, elongation at break is 7% or more. Tensile strength is necessary to ensure the pressure resistance of the lid, the piercing strength of the can and the strength of the can body.
- a method for forming a beverage can a method of welding along the rolling direction has increased, and in this case, the strength in the direction perpendicular to the rolling is required as the strength of the can body. Therefore, the tensile strength in the direction perpendicular to the rolling direction is preferably 520 MPa or more.
- the piercing strength of the can and the strength of the can body it is more desirable that the tensile strength in the direction perpendicular to the rolling is 530 MPa or more.
- the elongation at break is 7% or more, it is difficult to cause flange cracking, and it is easy to obtain good flange workability. Therefore, the elongation at break is preferably 7% or more.
- the tensile strength and elongation at break can be measured by a metal material tensile test method shown in “JIS Z 2241”.
- the steel plate for cans of the present invention is a slab formed by continuous casting of steel having the above composition, hot rolled, wound at a temperature below 630 ° C., and subjected to primary cold rolling at a rolling rate of 91.5% or more. Subsequently, it is manufactured by annealing and secondary cold rolling at a rolling rate of 20% or less.
- the slab reheating temperature before hot rolling is not particularly limited, but is preferably 1200 to 1300 ° C. If the slab reheating temperature is 1200 ° C. or higher, it is easy to ensure the final finishing rolling temperature. On the other hand, by setting the slab reheating temperature to 1300 ° C. or lower, it is possible to suppress generation of defects on the product surface and excessive increase in energy cost.
- Hot-rolled sheet by hot rolling Since the rolling load can be sufficiently reduced at the start of rolling, the rolling material is preferably 1100 ° C. or higher. Further, the finish temperature of hot finish rolling is preferably not less than the Ar3 transformation point from the viewpoint of preventing grain coarsening of the hot-rolled steel sheet and uniformity of precipitate distribution.
- the coiling temperature after hot rolling is desirably 500 ° C. or higher and lower than 630 ° C.
- pickling can be performed as necessary.
- the pickling is not particularly limited as long as the surface scale can be removed.
- the DR method is easier to reduce the plate thickness than the SR method, and it is possible to produce a steel plate with excellent strength.
- the DR method is adopted.
- the primary cold rolling rate is small, it is necessary to reduce the hot rolled finish thickness or increase the secondary cold rolling rate in order to produce an extremely thin steel sheet.
- the finish thickness of hot rolling becomes thin, it becomes difficult to ensure a predetermined finish rolling temperature.
- the primary cold rolling rate is desirably 91.5% or more.
- the primary cold rolling rate is 95% or less, rolling can be performed without imposing an excessive load on the cold rolling mill, so that the primary cold rolling rate is 91.5% or more and 95% or less. desirable.
- the annealing after the primary cold rolling can be performed by either batch annealing or continuous annealing.
- the soaking temperature is preferably not less than the recrystallization temperature and not more than 800 ° C.
- the secondary cold rolling rate is desirably 20% or less. More preferably, it is 10% or more and 15% or less.
- steps such as plating can be performed as usual, and finished as a steel plate for cans.
- a steel slab was obtained by continuous casting, containing the composition shown in Table 1, with the balance being Fe and unavoidable impurities, and melting in a converter.
- the obtained steel slab was reheated at 1250 ° C., then hot rolled at a rolling start temperature of 1150 ° C. to the thickness shown in Table 2, and wound at the winding temperature shown in Table 2.
- the finish rolling temperature of hot rolling is 880 ° C., and pickling is performed after hot rolling.
- primary cold rolling was performed at the rolling rates shown in Table 2, and continuous annealing was performed at a soaking temperature of 700 ° C., followed by secondary cold rolling at the rolling rates shown in Table 2.
- the steel plate obtained as described above was continuously subjected to Sn plating on both sides to obtain a tin plate having a single-side Sn adhesion amount of 2.8 g / m 2 and finished into a steel plate for cans.
- a tensile test was performed on the plated steel sheet (buri) obtained as described above after a heat treatment equivalent to a coating baking of 210 ° C. for 15 minutes.
- tensile strength breaking strength
- elongation at break in the direction perpendicular to rolling were measured in accordance with JIS Z 2241 using JIS5 size tensile test pieces.
- the average r-value was measured using the natural vibration method described in Annex JA of JIS Z 2254.
- a can body with an outer diameter of 52.8mm is formed by seam welding using a steel plate that has been heat-treated equivalent to paint baking, and the end is necked in to an outer diameter of 50.4mm and then flanged to an outer diameter of 55.4mm. The presence or absence of flange cracking was evaluated.
- the can body was formed into a 190 g beverage can size, and welding was performed along the rolling direction of the steel sheet. Neck-in processing was performed by a die neck method, and flange processing was performed by a spin flange method.
- the inventive examples are excellent in strength and have achieved a tensile strength of 520 MPa or more required as an extremely thin steel plate for cans. It is also excellent in workability and has a break elongation of 7% or more necessary for processing of lids and 3-piece can bodies.
- No. 7 and No. 8 of the comparative examples have too much C content, so that the hardening of the can body welded portion is excessive, and a flange crack occurs in the vicinity of the welded portion.
- No. 9 of the comparative example has insufficient tensile strength because the N content is too small. Since No. 10 of the comparative example has too much N content, the ductility is impaired by secondary cold rolling, and the elongation at break is insufficient.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
特許文献3および特許文献4に記載の鋼は、N量が少なすぎるため、加工性は良好であるが、二次冷間圧延を施しても強度が不足である。
(1)鋼板の成分組成が、質量%で、
C:0.001%以上0.040%未満、
Si:0.003%以上0.100%以下、
Mn:0.10%以上0.60%以下、
P:0.001%以上0.100%以下、
S:0.001%以上0.020%以下、
Al:0.005%以上0.100%以下、
N:0.0130%超0.0170%以下を含有し、
残部はFeおよび不可避的不純物を含有し、
N total-(N as AlN)が0.0100%以上0.0160%以下、ここに、N totalは、Nの総量であり、N as AlNは、AlNとして存在するN量であり、
平均r値が1.0超である缶用鋼板。
(2)前記C含有量が、0.020%以上0.039%以下である(1)に記載の缶用鋼板。
(3)前記C含有量が、0.025%以上0.035%以下である(1)に記載の缶用鋼板。
(4)前記N含有量が、0.0140%以上0.0160%以下である(1)に記載の缶用鋼板。
(5)前記N total-(N as AlN)含有量が、0.0110%以上0.0130%以下である(1)に記載の缶用鋼板。
(6)前記鋼板の成分組成が、さらに、質量%で、
Cr:0.10%以下、
Cu:0.20%以下、
Ni:0.15%以下、
Mo:0.05%以下、
Ti:0.3%以下、
Nb:0.3%以下、
Zr:0.3%以下、
V:0.3%以下、
Ca:0.01%以下からなるグループから選択された少なくとも1種の元素を含有する請求項1に記載の缶用鋼板。
(7)前記缶用鋼板は、圧延直角方向の引張強度が520MPa以上の缶用鋼板である(1)に記載の缶用鋼板。
(8)前記缶用鋼板は、圧延直角方向の引張強度が530MPa以上の缶用鋼板である(1)に記載の缶用鋼板。
(9)前記缶用鋼板は、破断伸びが7%以上の缶用鋼板である(1)に記載の缶用鋼板。
(10)質量%で、
C:0.001%以上0.040%未満、
Si:0.003%以上0.100%以下、
Mn:0.10%以上0.60%以下、
P:0.001%以上0.100%以下、
S:0.001%以上0.020%以下、
Al:0.005%以上0.100%以下、
N:0.0130%超0.0170%以下を含有し、
残部はFeおよび不可避的不純物を含有する鋼を準備し、
該鋼を連続鋳造によりスラブとし、
該スラブを熱間圧延し、
500℃以上630℃未満の温度で該熱延板を巻取り、
91.5%以上の圧延率で該熱延板を一次冷間圧延し、
該一次冷延板を焼鈍し、
20%以下の圧延率で該焼鈍した一次冷延板を二次冷間圧延することを含む缶用鋼板の製造方法。
(11)前記熱間圧延前に前記スラブを1200℃以上1300℃以下に再加熱する(10)に記載の缶用鋼板の製造方法。
(12)前記熱間圧延を1100℃以上の温度で開始する(10)に記載の缶用鋼板の製造方法。
(13)前記熱間仕上圧延をAr3変態点以上の温度で終了する(10)に記載の缶用鋼板の製造方法。
(14)前記一次冷間圧延の前に酸洗する(10)に記載の缶用鋼板の製造方法。
(15)前記一次冷間圧延の圧延率が、91.5%以上95%以下である(10)に記載の缶用鋼板の製造方法。
(16)前記一次冷間圧延後の焼鈍が、再結晶温度以上800℃以下の焼鈍である(10)に記載の缶用鋼板の製造方法。
(17)前記二次冷間圧延の圧延率が、10%以上15%以下である(10)に記載の缶用鋼板の製造方法。
(18)前記二次冷間圧延後に、二次冷延板をめっき処理する(10)に記載の缶用鋼板の製造方法。
なお、本明細書において、鋼の成分を示す%は、すべて質量%である。また、高強度缶用鋼板とは、圧延直角方向の引張強度が520MPa以上の缶用鋼板である。
上記の実験結果では、C量が0.040%未満であっても平均r値が1.0以下の鋼板はフランジ割れを生じている。従って、フランジ割れを防ぐには、C量が0.040%未満で、かつ、平均r値を1.0超とする必要があることがわかる。
C量が0.040%以上となると、缶胴溶接部の硬化が過大となるため、フランジ加工時に溶接部近傍の応力集中を招き、フランジ割れにつながる。一方、C量が0.001%未満となると強度確保に必要な固溶C量が得られなくなり、強度不足となる。C量が0.001%以上0.040%未満の場合には、520MPa以上の強度を確保しつつ、缶胴溶接部の過大な硬化なくフランジ加工性が良好となるため、C量は0.001%以上0.040%未満であることが望ましい。また、530MPa以上のより高い強度を得る観点からは、C量は0.020%以上0.039%以下であることがより好ましい。さらに高強度を得るためには、C量は0.025%以上0.035%以下であることが最も望ましい。
Si量が0.100%を超えると、表面処理性の低下、耐食性の劣化等の問題を引き起こすので、 Si量は0.100%以下であることが望ましい。また、0.003%以上であれば過大な精錬コストを必要とせず必要な表面処理性、耐食性を得ることができるため、Si量は0.003%以上であることが望ましい。
Mnは結晶粒を微細化する作用を有し、望ましい材質を確保する上で必要な元素である。Mn量が0.10%以上であれば前記結晶粒微細化効果を得ることができる。一方、Mn量が0.60%以下である場合には、耐食性、r値とも良好な特性を得ることができる。従って、Mn量は0.10%以上0.60%以下であることが望ましい。
Pは、鋼を硬質化させ、加工性を悪化させると同時に、耐食性をも悪化させる有害な元素である。0.100%以下とした場合には加工性、耐食性とも良好とすることができるため、P量は0.100%以下であることが望ましい。一方、Pを0.001%未満とするには脱Pコストがかかるが、0.001%以上であれば過大な脱Pコストなく前記の加工性、耐食性を得ることが可能となるので、P量は0.001%以上であることが望ましい。
Sは、鋼中で介在物として存在し、延性の低下、耐食性の劣化をもたらす有害な元素である。S量が0.020%以下であれば鋼中介在物量が十分低減でき、延性の低下、耐食性劣化を防止できるため、S量は0.020%以下であることが望ましい。一方、Sを0.001%未満とするには脱Sコストがかかるが、0.001%以上であれば過大な脱Sコストなく前記の延性、耐食性を確保できる。従って、S量は0.001%以上0.020%以下であることが望ましい。
Alは、製鋼時の脱酸材として必要な元素である。Al含有量が0.005%以上の場合、十分な脱酸が可能となり、介在物を減少させて、良好な加工性を得ることができる。一方、Al含有量が0.100%以下であれば、アルミナクラスターなどに起因する表面欠陥の発生を抑制することができる。よって、Al量は0.005%以上0.100%以下であることが望ましい。
本発明の鋼板はNを多量に含むことにより強度を確保する。Nが0.0130%超である場合には、後述するN total-(N as AlN)の十分な量が得られ、必要強度が確保される。一方、Nが0.0170%を超えると延性が低下するが、0.0170%以下であれば十分な延性を得ることができ、良好なフランジ加工性を発揮することができる。したがって、N量は0.0130%超0.0170%以下であることが望ましい。さらに良好な強度とフランジ加工性を得るには、0.0140%以上0.0160%以下であることがより好ましい。
強度に寄与するNは主に固溶状態のNであり、本発明の鋼板において強度を確保するためにはある程度の固溶N量が必要となる。本発明の鋼板組成では、鋼中でNが形成する化合物として主にAlNが考えられ、Nの総量(N total)からAlNとして存在するN量(N as AlN)を差し引いた値N total-(N as AlN)を固溶N量とみなすことができる。この量を十分に確保することが望ましく、0.0100%以上であれば要求する強度が得られる。一方、上記N量範囲(0.0130%超0.0170%以下)の下でN total-(N as AlN)量が多くなれば、AlN量が少なくなる。鋼中に析出するAlNは溶接熱影響部(HAZ)の結晶粒成長を抑制し、軟化を防ぐ作用がある。N total-(N as AlN)量が0.0160%を超えるとHAZ軟化防止に十分な量のAlN量が得られなくなるのに対して、0.0160%以下であれば必要AlN量が確保され、HAZ軟化防止が可能となる。したがって、N total-(N as AlN)量は0.0100%以上0.0160%以下であることが望ましい。さらに、強度およびHAZ軟化防止の観点からは、N total-(N as AlN)量が0.0110%以上0.0130%以下であることがより望ましい。
さらに、溶接缶用鋼板中に一般的に含有される成分元素を含有していても良い。例えば、Cr:0.10%以下、Cu:0.20%以下、Ni:0.15%以下、Mo:0.05%以下、Ti:0.3%以下、Nb:0.3%以下、Zr:0.3%以下、V:0.3%以下、Ca:0.01%以下等の成分元素を目的に応じて含有させることができる。
引張強度は、蓋の耐圧強度や缶の突き刺し強度および缶体強度を確保するために必要である。近年、飲料缶の成形方法として、圧延方向に沿って溶接する方法が増えており、この場合、缶体強度として必要になるのは圧延直角方向の強度である。よって、引張強度は、圧延直角方向の引張強度が520MPa以上であることが好ましい。また、蓋の耐圧強度や缶の突き刺し強度および缶体強度をより安定して確保する上では、圧延直角方向の引張強度が530MPa以上であることがより望ましい。
巻取り温度を630℃未満とした場合、巻取り後に析出するAlN量を抑制して、強度を確保するために十分な量のN total-(N as AlN)量を得ることが容易になる。また、巻き取り温度が500℃以上である場合には圧延速度を落とさずに仕上圧延終了温度を確保することが容易となるので好ましい。従って、熱間圧延後の巻取り温度は500℃以上630℃未満であることが望ましい。
前述したように、SR法に比べてDR法は板厚を薄くすることが容易であり、強度に優れた鋼板を製造することが可能であるため、本発明においてはDR法を採用する。一次冷間圧延率が小さい場合、極薄の鋼板を製造するためには熱間圧延の仕上げ厚を薄くするか、二次冷間圧延率を大きくすることが必要となる。熱間圧延の仕上げ厚が薄くなると所定の仕上げ圧延温度を確保することが困難となる。また、二次冷間圧延率を大きくすることは後述の理由から好ましくない。一次冷間圧延率が91.5%以上であれば熱間圧延の仕上げ厚を薄くしたり、二次冷間圧延率を大きくする必要は無く、極薄の鋼板を製造することが可能である。したがって、一次冷間圧延率は91.5%以上であることが望ましい。また、一次冷間圧延率が95%以下であれば冷間圧延機に過大な負荷をかけることなく圧延が可能となるので、一次冷間圧延率は91.5%以上95%以下であることがさらに望ましい。
二次冷間圧延の圧延率を20%以下とした場合、二次冷間圧延による加工硬化を抑制して、7%以上の破断伸びを得ることが容易になる。したがって、二次冷間圧延率は20%以下とすることが望ましい。より好ましくは、10%以上15%以下である。
比較例のNo.9は、N含有量が少なすぎるため、引張強度が不足している。比較例のNo.10は、N含有量が多すぎるため、二次冷間圧延により延性が損なわれ、破断伸びが不足している。
以上の結果から、C含有量0.040%未満、N含有率0.0130%超0.0170%以下、N total-(N as AlN)量0.0100%以上0.0160%以下、Mn含有量0.60%以下であり、巻き取り温度630℃未満として、本発明の要件を満たした場合には、目的とする520MPa以上の圧延直角方向の強度、および良好なフランジ加工性を同時に有することがわかる。
Claims (18)
- 鋼板の成分組成が、質量%で、
C:0.001%以上0.040%未満、
Si:0.003%以上0.100%以下、
Mn:0.10%以上0.60%以下、
P:0.001%以上0.100%以下、
S:0.001%以上0.020%以下、
Al:0.005%以上0.100%以下、
N:0.0130%超0.0170%以下を含有し、
残部はFeおよび不可避的不純物を含有し、
N total-(N as AlN)が0.0100%以上0.0160%以下、ここに、N totalは、Nの総量であり、N as AlNは、AlNとして存在するN量であり、
平均r値が1.0超である缶用鋼板。 - 前記C含有量が、0.020%以上0.039%以下である請求項1に記載の缶用鋼板。
- 前記C含有量が、0.025%以上0.035%以下である請求項1に記載の缶用鋼板。
- 前記N含有量が、0.0140%以上0.0160%以下である請求項1に記載の缶用鋼板。
- 前記N total-(N as AlN)含有量が、0.0110%以上0.0130%以下である請求項1に記載の缶用鋼板。
- 前記鋼板の成分組成が、さらに、質量%で、
Cr:0.10%以下、
Cu:0.20%以下、
Ni:0.15%以下、
Mo:0.05%以下、
Ti:0.3%以下、
Nb:0.3%以下、
Zr:0.3%以下、
V:0.3%以下、
Ca:0.01%以下からなるグループから選択された少なくとも1種の元素を含有する請求項1に記載の缶用鋼板。 - 前記缶用鋼板は、圧延直角方向の引張強度が520MPa以上の缶用鋼板である請求項1に記載の缶用鋼板。
- 前記缶用鋼板は、圧延直角方向の引張強度が530MPa以上の缶用鋼板である請求項1に記載の缶用鋼板。
- 前記缶用鋼板は、破断伸びが7%以上の缶用鋼板である請求項1に記載の缶用鋼板。
- 質量%で、
C:0.001%以上0.040%未満、
Si:0.003%以上0.100%以下、
Mn:0.10%以上0.60%以下、
P:0.001%以上0.100%以下、
S:0.001%以上0.020%以下、
Al:0.005%以上0.100%以下、
N:0.0130%超0.0170%以下を含有し、
残部はFeおよび不可避的不純物を含有する鋼を準備し、
該鋼を連続鋳造によりスラブとし、
該スラブを熱間圧延し、
500℃以上630℃未満の温度で該熱延板を巻取り、
91.5%以上の圧延率で該熱延板を一次冷間圧延し、
該一次冷延板を焼鈍し、
20%以下の圧延率で該焼鈍した一次冷延板を二次冷間圧延することを含む缶用鋼板の製造方法。 - 前記熱間圧延前に前記スラブを1200℃以上1300℃以下に再加熱する請求項10に記載の缶用鋼板の製造方法。
- 前記熱間圧延を1100℃以上の温度で開始する請求項10に記載の缶用鋼板の製造方法。
- 前記熱間仕上圧延をAr3変態点以上の温度で終了する請求項10に記載の缶用鋼板の製造方法。
- 前記一次冷間圧延の前に酸洗する請求項10に記載の缶用鋼板の製造方法。
- 前記一次冷間圧延の圧延率が、91.5%以上95%以下である請求項10に記載の缶用鋼板の製造方法。
- 前記一次冷間圧延後の焼鈍が、再結晶温度以上800℃以下の焼鈍である請求項10に記載の缶用鋼板の製造方法。
- 前記二次冷間圧延の圧延率が、10%以上15%以下である請求項10に記載の缶用鋼板の製造方法。
- 前記二次冷間圧延後に、二次冷延板をめっき処理する請求項10に記載の缶用鋼板の製造方法。
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201280034146.7A CN103649353B (zh) | 2011-07-12 | 2012-07-11 | 罐用钢板及其制造方法 |
KR1020147002973A KR20140030334A (ko) | 2011-07-12 | 2012-07-11 | 캔용 강판 및 그 제조 방법 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011-153718 | 2011-07-12 | ||
JP2011153718A JP5794004B2 (ja) | 2011-07-12 | 2011-07-12 | フランジ加工性に優れる高強度缶用鋼板およびその製造方法 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013008457A1 true WO2013008457A1 (ja) | 2013-01-17 |
Family
ID=47505760
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2012/004467 WO2013008457A1 (ja) | 2011-07-12 | 2012-07-11 | 缶用鋼板およびその製造方法 |
Country Status (7)
Country | Link |
---|---|
JP (1) | JP5794004B2 (ja) |
KR (1) | KR20140030334A (ja) |
CN (1) | CN103649353B (ja) |
CO (1) | CO6880059A2 (ja) |
MY (1) | MY179974A (ja) |
TW (1) | TWI564403B (ja) |
WO (1) | WO2013008457A1 (ja) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP3138935A4 (en) * | 2014-04-30 | 2017-05-31 | JFE Steel Corporation | High strength steel sheet for container, and method for producing same |
WO2018181449A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
WO2018181451A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
WO2018181450A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
EP3663428A4 (en) * | 2017-07-31 | 2020-06-10 | JFE Steel Corporation | STEEL SHEET FOR CROWN CAPSULE, CROWN CAPSULE AND METHOD FOR PRODUCING STEEL SHEET FOR CROWN CAPSULE |
Families Citing this family (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5803510B2 (ja) * | 2011-09-29 | 2015-11-04 | Jfeスチール株式会社 | 高強度高加工性缶用鋼板およびその製造方法 |
JP6019719B2 (ja) * | 2012-05-02 | 2016-11-02 | Jfeスチール株式会社 | 高強度高延性鋼板の製造方法 |
CA2916040C (en) | 2013-07-17 | 2019-02-12 | Jfe Steel Corporation | Steel sheet for can and method for manufacturing the same |
CN106029926B (zh) * | 2014-02-25 | 2018-10-02 | 杰富意钢铁株式会社 | 瓶盖用钢板及其制造方法以及瓶盖 |
WO2015166646A1 (ja) * | 2014-04-30 | 2015-11-05 | Jfeスチール株式会社 | 高強度鋼板及びその製造方法 |
CN105251768B (zh) * | 2014-07-16 | 2017-05-24 | 鞍钢股份有限公司 | 一种极薄冷轧镀锡原板轧制方法 |
CN104195453A (zh) * | 2014-08-18 | 2014-12-10 | 常熟市新洲机械制造厂 | 食品加工机械材料的冶炼工艺 |
JP5958630B2 (ja) * | 2014-10-10 | 2016-08-02 | Jfeスチール株式会社 | 王冠用鋼板およびその製造方法 |
MY176043A (en) * | 2014-10-10 | 2020-07-22 | Jfe Steel Corp | Steel sheet for crown cap and method for producing the same |
JP6164273B2 (ja) * | 2015-01-09 | 2017-07-19 | Jfeスチール株式会社 | 缶用鋼板及び缶用鋼板の製造方法 |
AU2016225754B2 (en) | 2015-02-26 | 2019-08-22 | Jfe Steel Corporation | Steel sheet for crown caps, method for producing steel sheet for crown caps, and crown cap |
WO2016157761A1 (ja) * | 2015-03-27 | 2016-10-06 | Jfeスチール株式会社 | 缶用鋼板およびその製造方法 |
KR101996353B1 (ko) * | 2015-03-31 | 2019-07-04 | 제이에프이 스틸 가부시키가이샤 | 캔 뚜껑용 강판 및 그의 제조 방법 |
BR112018017156A2 (ja) * | 2016-02-29 | 2018-12-26 | Jfe Steel Corporation | A steel-for-can board and a manufacturing method for the same |
JP6515294B2 (ja) * | 2016-05-31 | 2019-05-22 | Jfeスチール株式会社 | 容器用鋼板 |
CN116657048A (zh) * | 2019-03-29 | 2023-08-29 | 杰富意钢铁株式会社 | 罐用钢板及其制造方法 |
JP7131596B2 (ja) * | 2019-12-04 | 2022-09-06 | 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 |
CN110983179A (zh) * | 2019-12-16 | 2020-04-10 | 首钢集团有限公司 | 一种一次冷轧连退包装用钢及其制备方法 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06116647A (ja) * | 1992-10-08 | 1994-04-26 | Kawasaki Steel Corp | 缶用鋼板の製造方法 |
JPH06264138A (ja) * | 1993-03-12 | 1994-09-20 | Nippon Steel Corp | 板取り性が優れた溶接缶用鋼板の製造法 |
JP2001303183A (ja) * | 2000-04-24 | 2001-10-31 | Nippon Steel Corp | 欠陥が少なく加工性に優れた缶用鋼板およびその製造方法 |
JP2004218061A (ja) * | 2002-11-21 | 2004-08-05 | Nippon Steel Corp | 耐変形性が著しく良好な容器用鋼板およびその製造方法 |
JP2004323905A (ja) * | 2003-04-24 | 2004-11-18 | Nippon Steel Corp | 缶特性が著しく良好な極薄容器用鋼板およびその製造方法 |
WO2008018531A1 (fr) * | 2006-08-11 | 2008-02-14 | Nippon Steel Corporation | Tôle d'acier pour emboutissage et procédé de fabrication de celle-ci |
JP2009084687A (ja) * | 2007-09-10 | 2009-04-23 | Nippon Steel Corp | 製缶用高強度薄鋼板及びその製造方法 |
WO2009123356A1 (ja) * | 2008-04-03 | 2009-10-08 | 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 |
WO2010134616A1 (ja) * | 2009-05-18 | 2010-11-25 | 新日本製鐵株式会社 | 極薄鋼板およびその製造方法 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60128212A (ja) * | 1983-12-14 | 1985-07-09 | Nippon Steel Corp | 温間強度特性のすぐれたイ−ジ−オ−プン缶用鋼板の製造法 |
JP3804220B2 (ja) * | 1997-04-30 | 2006-08-02 | Jfeスチール株式会社 | 均質性に優れた缶用鋼板の製造方法 |
EP0999288B1 (en) * | 1998-04-08 | 2007-11-07 | JFE Steel Corporation | Steel sheet for can and manufacturing method thereof |
WO2005103316A1 (ja) * | 2004-04-27 | 2005-11-03 | Jfe Steel Corporation | 缶用鋼板およびその製造方法 |
-
2011
- 2011-07-12 JP JP2011153718A patent/JP5794004B2/ja active Active
-
2012
- 2012-07-11 CN CN201280034146.7A patent/CN103649353B/zh active Active
- 2012-07-11 KR KR1020147002973A patent/KR20140030334A/ko not_active Application Discontinuation
- 2012-07-11 WO PCT/JP2012/004467 patent/WO2013008457A1/ja active Application Filing
- 2012-07-11 MY MYPI2013004745A patent/MY179974A/en unknown
- 2012-07-12 TW TW101125056A patent/TWI564403B/zh active
-
2014
- 2014-02-11 CO CO14028689A patent/CO6880059A2/es unknown
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06116647A (ja) * | 1992-10-08 | 1994-04-26 | Kawasaki Steel Corp | 缶用鋼板の製造方法 |
JPH06264138A (ja) * | 1993-03-12 | 1994-09-20 | Nippon Steel Corp | 板取り性が優れた溶接缶用鋼板の製造法 |
JP2001303183A (ja) * | 2000-04-24 | 2001-10-31 | Nippon Steel Corp | 欠陥が少なく加工性に優れた缶用鋼板およびその製造方法 |
JP2004218061A (ja) * | 2002-11-21 | 2004-08-05 | Nippon Steel Corp | 耐変形性が著しく良好な容器用鋼板およびその製造方法 |
JP2004323905A (ja) * | 2003-04-24 | 2004-11-18 | Nippon Steel Corp | 缶特性が著しく良好な極薄容器用鋼板およびその製造方法 |
WO2008018531A1 (fr) * | 2006-08-11 | 2008-02-14 | Nippon Steel Corporation | Tôle d'acier pour emboutissage et procédé de fabrication de celle-ci |
JP2009084687A (ja) * | 2007-09-10 | 2009-04-23 | Nippon Steel Corp | 製缶用高強度薄鋼板及びその製造方法 |
WO2009123356A1 (ja) * | 2008-04-03 | 2009-10-08 | 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 |
WO2010134616A1 (ja) * | 2009-05-18 | 2010-11-25 | 新日本製鐵株式会社 | 極薄鋼板およびその製造方法 |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP3138935A4 (en) * | 2014-04-30 | 2017-05-31 | JFE Steel Corporation | High strength steel sheet for container, and method for producing same |
US10415111B2 (en) | 2014-04-30 | 2019-09-17 | Jfe Steel Corporation | High-strength steel sheet for containers and method for producing the same |
WO2018181449A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
WO2018181451A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
WO2018181450A1 (ja) * | 2017-03-31 | 2018-10-04 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
JP6468406B1 (ja) * | 2017-03-31 | 2019-02-13 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
JP6468404B1 (ja) * | 2017-03-31 | 2019-02-13 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
JP6468405B1 (ja) * | 2017-03-31 | 2019-02-13 | Jfeスチール株式会社 | 鋼板およびその製造方法と王冠およびdrd缶 |
US10837078B2 (en) | 2017-03-31 | 2020-11-17 | Jfe Steel Corporation | Steel sheet, method of manufacturing same, crown cap, and drawing and redrawing (DRD) can |
EP3663428A4 (en) * | 2017-07-31 | 2020-06-10 | JFE Steel Corporation | STEEL SHEET FOR CROWN CAPSULE, CROWN CAPSULE AND METHOD FOR PRODUCING STEEL SHEET FOR CROWN CAPSULE |
US11459149B2 (en) | 2017-07-31 | 2022-10-04 | Jfe Steel Corporation | Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap |
Also Published As
Publication number | Publication date |
---|---|
KR20140030334A (ko) | 2014-03-11 |
CN103649353A (zh) | 2014-03-19 |
TW201311912A (zh) | 2013-03-16 |
JP5794004B2 (ja) | 2015-10-14 |
CO6880059A2 (es) | 2014-02-28 |
MY179974A (en) | 2020-11-19 |
TWI564403B (zh) | 2017-01-01 |
CN103649353B (zh) | 2016-11-09 |
JP2013019027A (ja) | 2013-01-31 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5794004B2 (ja) | フランジ加工性に優れる高強度缶用鋼板およびその製造方法 | |
JP5135868B2 (ja) | 缶用鋼板およびその製造方法 | |
TWI460029B (zh) | 高強度高加工性罐用鋼板及其製造方法 | |
TWI390054B (zh) | Steel plate for high strength container and method for manufacturing the same | |
JP5018843B2 (ja) | 高加工性3ピース溶接缶用鋼板およびその製造方法 | |
JP5854134B2 (ja) | 3ピース缶体およびその製造方法 | |
CN110983179A (zh) | 一种一次冷轧连退包装用钢及其制备方法 | |
JP5884161B2 (ja) | 缶用鋼板用原板と缶用鋼板の製造方法 | |
JP2010180423A (ja) | 高加工性缶用鋼板およびその製造方法 | |
JP2023507810A (ja) | 加工用錫メッキ原板およびその製造方法 | |
JP5672907B2 (ja) | 高強度高加工性缶用鋼板およびその製造方法 | |
JP6019719B2 (ja) | 高強度高延性鋼板の製造方法 | |
JP2015151620A (ja) | 缶用鋼板および缶用鋼板の製造方法 | |
JP6060603B2 (ja) | 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 | |
JP5540580B2 (ja) | 高強度高加工性缶用鋼板およびその製造方法 | |
JP4276388B2 (ja) | フランジ成形性に優れた高強度溶接缶用薄鋼板及びその製造方法 | |
JP5803510B2 (ja) | 高強度高加工性缶用鋼板およびその製造方法 | |
JP4810766B2 (ja) | 軽量2ピース缶用極薄高強度鋼板の製造方法 | |
JP5849666B2 (ja) | 高強度高加工性缶用鋼板およびその製造方法 | |
JP3598550B2 (ja) | 異方性が小さい高強度缶用薄鋼板の製造方法 | |
JP5464223B2 (ja) | 溶接缶用表面処理鋼板及びその製造方法 | |
JPH10245627A (ja) | ネック成形性に優れた溶接缶用極薄鋼板の製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 12811766 Country of ref document: EP Kind code of ref document: A1 |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 20147002973 Country of ref document: KR Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14028689 Country of ref document: CO |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 12811766 Country of ref document: EP Kind code of ref document: A1 |