WO2012073914A1 - Steel sheet for can, and process for producing same - Google Patents
Steel sheet for can, and process for producing same Download PDFInfo
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- WO2012073914A1 WO2012073914A1 PCT/JP2011/077446 JP2011077446W WO2012073914A1 WO 2012073914 A1 WO2012073914 A1 WO 2012073914A1 JP 2011077446 W JP2011077446 W JP 2011077446W WO 2012073914 A1 WO2012073914 A1 WO 2012073914A1
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
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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
- C21D8/0426—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
- C21D8/04—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
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
Definitions
- the present invention relates to a steel plate for cans having high strength and high workability, and a method for producing the same.
- DR Double Reduce
- steel plates called DR (Double Reduce) materials may be used for lids, bottoms, three-piece can bodies, drawn cans, and the like.
- the DR material that undergoes cold rolling (secondary cold rolling) again after annealing is easier to reduce the plate thickness than SR (Single Reduce) material that performs only temper rolling with a small rolling rate, By using a thin steel plate, the can manufacturing cost can be reduced.
- the DR material is a thin and hard steel plate because work hardening occurs by performing cold rolling after annealing, but the DR material is inferior in workability compared to the SR material because the DR material is poor in ductility.
- EOE Easy Open End
- a lid for beverage cans and food cans.
- EOE Easy Open End
- the body of a three-piece beverage can is molded into a cylindrical shape and then flanged at both ends in order to tighten the lid and bottom, the can body end also has an elongation of about 10%. Required.
- a steel plate as a can-making material is required to have a strength corresponding to the plate thickness, and in the case of a DR material, a tensile strength of about 500 MPa or more is required to ensure the strength of the can by making it thin.
- DR materials are difficult to achieve both the above ductility and strength, and SR materials have been used for EOE and beverage can bodies.
- this material can also be used as a raw material for steel plates for cans such as 2-piece can bodies, DI (Drawn and Ironed) cans, DRD (Draw-Redraw) cans, aerosol cans and bottom ends.
- Patent Document 1 discloses a method for producing a steel sheet having a high r value and excellent flange workability by producing a DR material of low carbon steel at a primary cold rolling rate of 85% or less. Has been.
- Patent Document 2 discloses a method of manufacturing a DR material that achieves both hardness and workability by performing nitriding in a low carbon steel annealing process.
- Patent Document 3 discloses a steel slab containing C: 0.01 to 0.08%, Mn: 0.05 to 0.50%, Al: 0.01 to 0.15%, and below the Ar 3 transformation point.
- a thin steel plate having a thickness of less than 0.21 mm obtained by performing hot finish rolling, followed by cold rolling, followed by recrystallization annealing by continuous annealing, and then skin-passing at a rolling reduction of 5 to 10%.
- cover for easy open cans which performs score processing from which the ratio of score remaining thickness / steel plate thickness becomes 0.4 or less is disclosed.
- Patent Document 4 C: 0.04 to 0.08%, Si: 0.03% or less, Mn: 0.05 to 0.50%, P: 0.02% or less, S: 0.02%
- Al 0.02 to 0.10%
- N 0.008 to 0.015%
- the amount of (N total-N as AlN) in the steel sheet is 0.007% or more
- rolling When the total elongation value in the direction is represented by X and the average value is represented by Y, excellent flange workability equal to or better than that of batch-annealed DR steel sheet when the relationship of X ⁇ 10% and Y ⁇ ⁇ 0.05X + 1.4 is satisfied.
- a continuous annealed DR steel sheet for welding cans and a manufacturing method thereof are disclosed.
- the amount of Mn is suppressed to a low value of 0.05 to 0.50 wt%, and it is not possible to cope with an increase in strength for securing a pressure resistance strength by thinning. .
- the present invention has been made in view of such circumstances, and is applicable to lids, bottoms, three-piece can bodies and two-piece can bodies, DI cans, DRD cans, aerosol cans, bottom ends, and the like, and in particular, materials for EOE.
- An object of the present invention is to provide a steel plate for a high-strength and highly workable can that is suitable as a manufacturing method and a method for producing the same.
- the gist of the present invention is as follows.
- 1st invention is the mass%, C: 0.070% or more and less than 0.080%, Si: 0.003% or more and 0.10% or less, Mn: 0.51% or more and 0.60% or less, P : 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: 0.010% or less, the balance Is composed of Fe and unavoidable impurities, and has an average crystal grain size of 5 ⁇ m or more and a crystal grain elongation of 2.0 or less in the cross section in the rolling direction, and from a depth of 3/8 of the plate thickness to 4 of the plate thickness.
- the difference in hardness obtained by subtracting the average Vickers hardness of the cross section from the surface to the depth of 1/8 of the plate thickness from the average Vickers hardness of the cross section up to a depth of / 8 is 10 points or more and / or Maximum Vickers hardness of cross section between 3/8 depth and 4/8 depth of plate thickness
- the hardness difference obtained by subtracting the maximum Vickers hardness of the cross section from the surface to the depth of 1/8 of the plate thickness is 20 points or more
- the tensile strength is 500 MPa or more
- the elongation at break is 10% or more. It is a steel plate for cans with high strength and high workability.
- the second invention relates to the crystal grain size from an average crystal grain size between the surface and a depth of 1/8 of the plate thickness, from a depth of 3/8 of the plate thickness to a depth of 4/8 of the plate thickness.
- the average crystal grain size difference obtained by subtracting the average crystal grain size is 1 ⁇ m or more, and the high strength and high workability steel sheet for cans according to the first invention.
- the third invention relates to the nitrogen amount from an average N amount between a depth of 3/8 of the plate thickness to a depth of 4/8 of the plate thickness, to a depth of 1/8 of the plate thickness from the surface.
- the difference in average N amount obtained by subtracting the average N amount between them is 10 ppm or more, and the steel sheet for high strength and high workability cans according to the first invention or the second invention.
- the fourth invention relates to a nitride having a diameter of 1 ⁇ m or less and 0.02 ⁇ m or more, and has a depth of 1/4 of the plate thickness from the surface rather than the average nitride number density from the surface to a depth of 1/8 of the plate thickness.
- the steel sheet for a high-strength and high-workability can according to any one of the first to third inventions, wherein the average nitride number density is high.
- the fifth invention relates to the nitride having a diameter of 1 ⁇ m or less and 0.02 ⁇ m or more, and the average nitride number density from the surface to a depth of 1/20 of the plate thickness is set to a depth of 1/4 of the plate thickness from the surface.
- the steel sheet for a high-strength and high-workability can according to any one of the first to fourth inventions, wherein a value divided by an average nitride number density is less than 1.5.
- a sixth invention is a steel plate for a high-strength, high-workability can according to any one of the first to fifth inventions, wherein the amount of solid solution C in the steel is 51 ppm or more with respect to the carbon content. is there.
- 7th invention is mass%, C: 0.070% or more and less than 0.080%, Si: 0.003% or more and 0.10% or less, Mn: 0.51% or more and 0.60% or less, P : 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: 0.010% or less, the balance Is a steel made of Fe and unavoidable impurities made into a slab by continuous casting, and after hot rolling, it is wound at a temperature of less than 620 ° C., and then primary cold rolling at a primary cold rolling rate of 86% or more in total.
- Rolling with a cold rolling reduction rate of 30% or more in the final stand of rolling is performed, followed by annealing in an atmosphere where ammonia gas is less than 0.020 vol%, and then performing secondary cold rolling at a rolling rate of 20% or less.
- High strength and high workability steel for cans It is a method of manufacture.
- the inventors have conducted intensive research to solve the above problems and obtained the following knowledge.
- an appropriate amount of C is added to give strength, while the rolling rate of the final stand of primary cold rolling is improved and strain is introduced into the surface layer, and then annealing is performed.
- the ammonia gas in the annealing atmosphere is suppressed to less than 0.020 vol%, and the secondary cold rolling rate is limited to an appropriate range, It is possible to achieve both strength and ductility by softening the surface layer of the steel sheet.
- the coiling temperature after hot rolling is high, the cementite that precipitates becomes coarse and the local elongation decreases, so it is necessary to limit the coiling temperature to an appropriate temperature range.
- the depth of 3/8 of the plate thickness indicates a position that is separated from the surface by a distance of 3/8 of the plate thickness in the center direction of the plate thickness. The same applies to the depth of 4/8 of the plate thickness, the depth of 1/8 of the plate thickness, the depth of 1/4 of the plate thickness, and the depth of 1/20 of the plate thickness.
- the steel plate for cans of the present invention is a steel plate for cans having a high strength and high workability having a tensile strength of 500 MPa or more and a breaking elongation of 10% or more. And such a steel plate uses the steel containing 0.070% or more and less than 0.080% C, and sets the coiling temperature after hot rolling and the secondary cold rolling rate to appropriate conditions. This makes it possible to manufacture.
- the secondary cold rolling rate is suppressed to ensure elongation, while high C content is exhibited by increasing the amount of C. If the C content is less than 0.070%, a tensile strength of 500 MPa necessary for obtaining a remarkable economic effect due to the thinning of the steel sheet cannot be obtained. Therefore, the C content is 0.070% or more. On the other hand, if the amount of C is 0.080% or more, it becomes excessively hard, and it becomes impossible to produce a thin steel plate by secondary cold rolling while ensuring workability. Therefore, the upper limit of the C amount is less than 0.080%.
- Si 0.003% or more and 0.10% or less If the amount of Si exceeds 0.10%, problems such as deterioration of surface treatment property and deterioration of corrosion resistance are caused, so the upper limit is made 0.10%. On the other hand, if it is less than 0.003%, the refining cost becomes excessive, so the lower limit is made 0.003%.
- Mn 0.51% or more and 0.60% or less
- Mn is an element necessary to prevent red heat embrittlement during hot rolling by S and to refine crystal grains and to secure a desirable material. . Further, in order to satisfy the can strength with the thinned material, it is necessary to increase the strength of the material. In order to cope with this increase in strength, it is necessary to add 0.51% or more of Mn. On the other hand, if Mn is added in a large amount, the corrosion resistance deteriorates and the steel plate becomes excessively hardened, so the upper limit is made 0.60%.
- 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. Therefore, the upper limit is made 0.100%. On the other hand, in order to make P less than 0.001%, the dephosphorization cost becomes excessive. Therefore, the lower limit is made 0.001%.
- 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 deterioration in corrosion resistance. Therefore, the upper limit is made 0.020%. On the other hand, desulfurization cost becomes excessive to make S less than 0.001%. Therefore, the lower limit is made 0.001%.
- Al 0.005% or more and 0.100% or less
- Al is an element necessary as a deoxidizer during steelmaking. When the addition amount is small, deoxidation becomes insufficient, inclusions increase, and workability deteriorates. If the content is 0.005% or more, it can be considered that deoxidation is sufficiently performed. On the other hand, when the content exceeds 0.100%, the frequency of occurrence of surface defects due to alumina clusters and the like increases. Therefore, the Al content is 0.005% or more and 0.100% or less.
- N 0.010% or less
- the hot ductility deteriorates and cracks of the slab occur in continuous casting. Therefore, the upper limit is made 0.010%.
- the N amount is preferably set to 0.001% or more. The balance is Fe and inevitable impurities.
- the tensile strength is 500 MPa or more. If the tensile strength is less than 500 MPa, the steel plate cannot be made thin enough to obtain a remarkable economic effect in order to secure the strength of the steel plate as a can-making material. Therefore, the tensile strength is 500 MPa or more.
- the elongation at break is 10% or more. If the elongation at break is less than 10%, cracking occurs during rivet processing when applied to EOE. Moreover, even when applied to a three-piece can body, cracking occurs during flange processing. Accordingly, the elongation at break is 10% or more.
- the said tensile strength and the said breaking elongation can be measured by the metallic material tension test method shown by "JISZ2241".
- the average grain size in the cross section in the rolling direction is 5 ⁇ m or more.
- the final mechanical properties of the steel plate for cans of the present invention are greatly influenced by the state of crystal grains.
- the average crystal grain size in the cross section in the rolling direction is less than 5 ⁇ m, the steel sheet is insufficiently stretched and the workability is impaired.
- the elongation of the crystal grains in the cross section in the rolling direction is set to 2.0 or less.
- the degree of extension is a value that represents the degree to which ferrite crystal grains are extended by processing, as shown in “JISG0202.”
- JISG0202. When the elongation of the crystal grains in the cross section in the rolling direction exceeds 2.0, the elongation in the direction perpendicular to the rolling, which is important for flange workability and neck workability, is insufficient.
- the elongation increases with the rolling ratio of the secondary cold rolling, in order to suppress the above-described elongation at the secondary cold rolling ratio of up to about 20%, the steel should have a C content of 0.070% or more. Need to contain.
- Vickers hardness can be measured by the hardness test method shown in “JIS Z 2244”. A Vickers hardness test at a load of 10 gf is performed so that the hardness distribution in the plate thickness direction in the cross section of the steel plate can be appropriately evaluated. The measurement is performed at 10 locations, and the average value of the measured values is taken as the average cross-sectional hardness of each. Moreover, let the largest thing of Vickers hardness measurements be cross-section Vickers maximum hardness.
- Hardness difference 10 points or more, 20 points or more
- the strength increases when the surface layer is hardened, but since the soft central layer is sandwiched between the hard surface layers, the entire plate is constrained and the elongation decreases, and the necking is reduced. It tends to occur and processability decreases.
- the surface layer is soft and the central layer is hard, only the central layer of the plate is constrained, so that the strength is high, and a high-strength and highly workable steel plate that does not cause reduction in elongation and constriction is obtained.
- the difference in cross-sectional average hardness is less than 10 points and / or the maximum cross-section hardness is less than 20 points, the entire plate is homogeneous, so there is no difference from the current material, and a high strength and high workability steel sheet is obtained. I can't do that.
- the difference in cross-sectional average hardness is 10 points or more and / or the maximum cross-section hardness is 20 points or more, the tensile strength can be 500 MPa or more and the elongation at break can be 10% or more.
- Average crystal grain size difference 1 ⁇ m or more
- the above-mentioned crystal grain size is determined from the average crystal grain size between the surface and a depth of 1/8 of the plate thickness. It is preferable that an average crystal grain size difference obtained by subtracting an average crystal grain size from a depth of 3/8 to a depth of 4/8 of the plate thickness is 1 ⁇ m or more. This is because a steel sheet having both excellent strength and ductility properties can be obtained when the average crystal grain size difference is 1 ⁇ m or more.
- the crystal grain size is 1 / 8th of the plate thickness and softens due to the large crystal grain size, so that the elongation is improved, and the crystal grains having a depth of 3 / 8th of the plate thickness to 4 / 8th of the plate thickness. Since the diameter is small and it is hard and has high strength, high strength and ductility are compatible, and the tensile strength can be easily set to 500 MPa or more and the breaking elongation can be set to 10% or more.
- the average amount of N between the depth of 3/8 of the plate thickness and the depth of 4/8 of the plate thickness is the amount of N using the combustion method for the samples subjected to the electropolishing to the depth of 3/8 of the plate thickness. It was measured.
- the average N amount from the surface to the depth of 1/8 of the plate thickness is obtained by tape-sealing one side of the sample and then chemically polishing from the surface to the depth of 1/8 of the plate thickness using oxalic acid.
- the amount of N was measured using a combustion method.
- Average N amount difference 10 ppm or more If the average N amount difference is less than 10 ppm, since the entire plate has a uniform N amount, large softening due to a decrease in the N amount of the surface layer cannot be expected, but the difference in the average N amount is By setting the surface layer to 10 ppm or more, the surface layer is softened by a small amount of solid solution N that contributes to solid solution strengthening because the amount of N is low, and the center layer is hard because the amount of N is high and hard, so both high strength and ductility are achieved.
- the tensile strength can easily be 500 MPa or more and the elongation at break can be 10% or more. Therefore, it is easy to obtain a high-strength and highly workable steel plate.
- the number density of nitride is chemically polished to a predetermined position with oxalic acid, etc., electrolyzed with 10 ⁇ m using the SPEED method, an extraction replica is prepared, and the number of nitride per unit field of 1 ⁇ m square is measured using TEM. did.
- the nitride was identified by analysis using EDX.
- the average nitride number density between the surface and the depth of 1/8 of the plate thickness is more than the depth between the surface and the depth of 1/4 of the plate thickness.
- a higher average nitride number density is preferred. This is because if the average nitride number density from the surface to the depth of 1/8 of the plate thickness is small, the number of fine precipitates is small, so that the softening occurs and the surface to the depth of 1/4 of the plate thickness.
- the amount of solid solution C was calculated from the peak of internal friction.
- the internal friction is measured using a torsional vibration type internal friction measuring device manufactured by Vibran at a test piece shape of 1 mm ⁇ 1 mm ⁇ 80 mm, a measurement frequency of 0.001 to 10 Hz, and a temperature of 0 ° C. After removing the background, the peak value Q-1 was read and calculated from the calibration curve of Q-1 and the amount of dissolved C. If the amount of solute C in the steel is large, the strength is increased due to strengthening by the solute C, and the elongation is improved because the amount of carbide that becomes the starting point of fracture decreases.
- the steel sheet for a high-strength, high-workability can of the present invention uses a steel slab having the above composition produced by continuous casting, and after being hot-rolled, wound at a temperature of less than 620 ° C., and then 86% or more At the primary cold rolling rate, rolling is performed with a cold rolling rate of 30% or more in the final stand of the primary cold rolling, followed by annealing in an atmosphere where the ammonia gas is less than 0.020 vol%, and then 20% or less. It is created by performing secondary cold rolling at a rolling rate of.
- the second cold rolling is performed after annealing to obtain an extremely thin steel plate.
- Winding temperature after hot rolling less than 620 ° C. If the winding temperature after hot rolling is 620 ° C. or more, the pearlite structure to be formed becomes coarse, and this becomes the starting point of brittle fracture, so the local elongation decreases. Thus, the elongation at break of 10% or more cannot be obtained. Therefore, the coiling temperature after hot rolling is less than 620 ° C. More preferably, it is 560 ° C to 620 ° C.
- Primary cold rolling rate 86% or more
- the primary cold rolling rate is small, it is necessary to increase the rolling rate of hot rolling and secondary cold rolling in order to finally obtain a very thin steel plate. Increasing the hot rolling rate is not preferable for the above-described reason, and the secondary cold rolling rate needs to be limited for the reason described later.
- the primary cold rolling rate is 86% or more. More preferably, it is 90 to 92%.
- Final stand rolling ratio of primary cold rolling 30% or more
- Annealing requires that the concentration of ammonia gas in the atmosphere be less than 0.020 vol% in order to suppress nitridation of the surface layer. Preferably it is 0.018 vol% or less, More preferably, it is 0.016 vol% or less. Moreover, it is necessary to complete recrystallization by annealing.
- the soaking temperature is preferably 600 to 750 ° C. from the viewpoint of operation efficiency and prevention of breakage during annealing of the thin steel sheet.
- Secondary cold rolling rate 20% or less
- the secondary cold rolling rate is 20% or less. If the secondary cold rolling rate exceeds 20%, work hardening by secondary cold rolling becomes excessive, and a breaking elongation of 10% or more cannot be obtained. Therefore, the secondary cold rolling rate is 20% or less. Preferably it is 15% or less, More preferably, it is 10% or less.
- the plating and other processes are performed as usual, and finished as a steel plate for cans.
- a steel containing the component composition shown in Table 1 and the balance being Fe and inevitable impurities was made as a trial, and a steel slab was obtained by casting.
- hot rolling and primary cold rolling were performed under the conditions shown in Table 2.
- the finish rolling temperature of hot rolling is 890 ° C., and pickling is performed after rolling.
- the secondary cold rolling was performed under the conditions shown in Table 2 and continuous annealing at a soaking temperature of 630 ° C. and a soaking time of 25 seconds.
- 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 .
- the test results are shown in Tables 2 and 3.
- the crystal grain size, N content, and nitride number density mean the average crystal grain size, average N content, and average nitride number density, respectively.
- the plated steel sheet (cover) obtained as described above was subjected to a heat treatment equivalent to baking at 210 ° C. for 10 minutes, and then subjected to a tensile test.
- tensile strength breaking strength
- elongation at break were measured at a tensile speed of 10 mm / min using a JIS No. 5 size tensile test piece.
- the sample of the plated steel plate was extract
- the average crystal grain size and the degree of crystal grain elongation in the cross section in the rolling direction are determined by grinding the vertical cross section of the steel sheet and revealing the grain boundary by night etching, and then cutting with the straight test line described in “JISG 0551” Measured by the method.
- the pressure strength is measured by forming a sample with a thickness of 0.21 mm into a 63 mm ⁇ lid, then winding it around a 63 mm ⁇ weld can body, introducing compressed air into the can, and the pressure when the can lid is deformed.
- the can lid was deformed at ⁇ , 0.19 MPa or less, it was rated as x.
- the moldability was tested by a method specified in JIS Z 2247 using a tester specified in JIS B 7729.
- the Erichsen value (molding height at the time of the occurrence of through cracking) is 6.5 mm or more, ⁇ ⁇ , less than 6.5 mm, 6.0 mm or more is ⁇ , and less than 6.0 mm is x.
- Tables 1 to 3 show examples of invention numbers. 6 ⁇ No. Nos. 12 and 18 are excellent in strength, and have achieved a tensile strength of 500 MPa or more necessary for an extremely thin steel plate for cans. Moreover, it is excellent in workability and has an elongation of 10% or more necessary for processing of a lid or a three-piece can body.
- the comparative example No. No. 1 has insufficient tensile strength because the C content is too small. Moreover, No. of the comparative example. In No. 2, since the C content is too large, ductility is impaired by secondary cold rolling, and the elongation at break (denoted as “total elongation” in Table 2) is insufficient. Comparative Example No. Since No. 3 has too little Mn content, the tensile strength is insufficient. Comparative Example No. Since No. 4 has too much Mn content, ductility is impaired by secondary cold rolling and the elongation at break is insufficient. Moreover, No. of the comparative example. Since No. 5 has too much N content, ductility is impaired by secondary cold rolling and elongation at break is insufficient.
- a steel plate for a can having a high strength such as a tensile strength of 500 MPa or more and a breaking elongation of 10% or more and high workability.
- a high strength such as a tensile strength of 500 MPa or more and a breaking elongation of 10% or more and high workability.
- cracks do not occur even during rivet processing of EOE or flange processing of a three-piece can. Therefore, it is possible to make cans using a DR material having a thin plate thickness, and a significant reduction in the thickness of the steel plate for cans can be achieved.
Abstract
Description
また、板厚の3/8の深さとは、表面から板厚中心方向に板厚の3/8の距離を隔てた位置を示す。その他の、板厚の4/8の深さ、板厚の1/8の深さ、板厚の1/4の深さ、板厚の1/20の深さも同様である。 In addition, in this specification,% which shows the component of steel is mass% altogether.
Further, the depth of 3/8 of the plate thickness indicates a position that is separated from the surface by a distance of 3/8 of the plate thickness in the center direction of the plate thickness. The same applies to the depth of 4/8 of the plate thickness, the depth of 1/8 of the plate thickness, the depth of 1/4 of the plate thickness, and the depth of 1/20 of the plate thickness.
本発明の缶用鋼板は、引張強度が500MPa以上でかつ破断伸びが10%以上の高強度高加工性缶用鋼板である。そして、このような鋼板は、0.070%以上0.080%未満のCを含有する鋼を用いて、熱間圧延後の巻き取り温度および二次冷間圧延率を適正な条件に設定することにより、製造することが可能となる。 Hereinafter, the present invention will be described in detail.
The steel plate for cans of the present invention is a steel plate for cans having a high strength and high workability having a tensile strength of 500 MPa or more and a breaking elongation of 10% or more. And such a steel plate uses the steel containing 0.070% or more and less than 0.080% C, and sets the coiling temperature after hot rolling and the secondary cold rolling rate to appropriate conditions. This makes it possible to manufacture.
本発明の缶用鋼板においては、二次冷間圧延率を抑えて伸びを確保する一方、C量を高めとすることで高強度を発揮する。C量が0.070%未満であると、鋼板の薄肉化による顕著な経済効果を得るために必要な引張強度500MPaが得られない。したがって、C量は0.070%以上とする。一方、C量が0.080%以上では過剰に硬質となり、加工性を確保したまま二次冷間圧延で薄い鋼板を製造することが不可能となる。したがって、C量の上限は0.080%未満とする。 C: 0.070% or more and less than 0.080% In the steel plate for cans of the present invention, the secondary cold rolling rate is suppressed to ensure elongation, while high C content is exhibited by increasing the amount of C. If the C content is less than 0.070%, a tensile strength of 500 MPa necessary for obtaining a remarkable economic effect due to the thinning of the steel sheet cannot be obtained. Therefore, the C content is 0.070% or more. On the other hand, if the amount of C is 0.080% or more, it becomes excessively hard, and it becomes impossible to produce a thin steel plate by secondary cold rolling while ensuring workability. Therefore, the upper limit of the C amount is less than 0.080%.
Si量が0.10%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、上限は0.10%とする。一方、0.003%未満とするには精錬コストが過大となるため、下限は0.003%とする。 Si: 0.003% or more and 0.10% or less If the amount of Si exceeds 0.10%, problems such as deterioration of surface treatment property and deterioration of corrosion resistance are caused, so the upper limit is made 0.10%. On the other hand, if it is less than 0.003%, the refining cost becomes excessive, so the lower limit is made 0.003%.
Mnは、Sによる熱延中の赤熱脆性を防止し、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。さらに薄肉化した材料で缶強度を満足するには材料の高強度化が必要である。この高強度化に対応するためにはMn量は0.51%以上の添加が必要である。一方、Mnを多量に添加し過ぎると、耐食性が劣化し、また鋼板が過剰に硬質化するので、上限は0.60%とする。 Mn: 0.51% or more and 0.60% or less Mn is an element necessary to prevent red heat embrittlement during hot rolling by S and to refine crystal grains and to secure a desirable material. . Further, in order to satisfy the can strength with the thinned material, it is necessary to increase the strength of the material. In order to cope with this increase in strength, it is necessary to add 0.51% or more of Mn. On the other hand, if Mn is added in a large amount, the corrosion resistance deteriorates and the steel plate becomes excessively hardened, so the upper limit is made 0.60%.
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。そのため、上限は0.100%とする。一方、Pを0.001%未満とするには脱リンコストが過大となる。よって、下限は0.001%とする。 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. Therefore, the upper limit is made 0.100%. On the other hand, in order to make P less than 0.001%, the dephosphorization cost becomes excessive. Therefore, the lower limit is made 0.001%.
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。そのため、上限は0.020%とする。一方、Sを0.001%未満とするには脱硫コストが過大となる。よって、下限は0.001%とする。 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 deterioration in corrosion resistance. Therefore, the upper limit is made 0.020%. On the other hand, desulfurization cost becomes excessive to make S less than 0.001%. Therefore, the lower limit is made 0.001%.
Alは、製鋼時の脱酸材として必要な元素である。添加量が少ないと、脱酸が不十分となり、介在物が増加し、加工性が劣化する。含有量が0.005%以上であれば十分に脱酸が行われているとみなすことができる。一方、含有量が0.100%を超えると、アルミナクラスターなどに起因する表面欠陥の発生頻度が増加する。よって、Al量は0.005%以上0.100%以下とする。 Al: 0.005% or more and 0.100% or less Al is an element necessary as a deoxidizer during steelmaking. When the addition amount is small, deoxidation becomes insufficient, inclusions increase, and workability deteriorates. If the content is 0.005% or more, it can be considered that deoxidation is sufficiently performed. On the other hand, when the content exceeds 0.100%, the frequency of occurrence of surface defects due to alumina clusters and the like increases. Therefore, the Al content is 0.005% or more and 0.100% or less.
Nは多量に添加すると、熱間延性が劣化し、連続鋳造においてスラブの割れが発生する。よって、上限は0.010%とする。なお、N量を0.001%未満とするには精錬コストが過大となるので、N量は0.001%以上とすることが好ましい。
なお、残部はFeおよび不可避的不純物とする。 N: 0.010% or less When N is added in a large amount, the hot ductility deteriorates and cracks of the slab occur in continuous casting. Therefore, the upper limit is made 0.010%. In addition, since the refining cost is excessive to make the N amount less than 0.001%, the N amount is preferably set to 0.001% or more.
The balance is Fe and inevitable impurities.
なお、上記圧延方向断面における平均結晶粒径および上記圧延方向断面における結晶粒の展伸度は「JIS G 0551」に示される結晶粒度の顕微鏡試験方法により測定することができる。 Further, the elongation of the crystal grains in the cross section in the rolling direction is set to 2.0 or less. The degree of extension is a value that represents the degree to which ferrite crystal grains are extended by processing, as shown in “JISG0202.” When the elongation of the crystal grains in the cross section in the rolling direction exceeds 2.0, the elongation in the direction perpendicular to the rolling, which is important for flange workability and neck workability, is insufficient. Although the elongation increases with the rolling ratio of the secondary cold rolling, in order to suppress the above-described elongation at the secondary cold rolling ratio of up to about 20%, the steel should have a C content of 0.070% or more. Need to contain. That is, when C is less than 0.070%, the number of cementite grains precipitated after hot rolling decreases, and as a result, a large amount of solid solution C remains. Since solute C suppresses the grain growth during annealing, the shape of the crystal grains flattened by the primary cold rolling remains, and the degree of elongation increases.
The average crystal grain size in the rolling direction section and the degree of elongation of the crystal grains in the rolling direction section can be measured by a crystal grain size microscopic test method described in “JIS G 0551”.
表層が硬質化した場合は強度が高くなるが、硬質な表層で軟質な中央層が挟まれるため、板全体が拘束されて伸びが低下し、くびれが発生しやすくなり加工性が低下する。表層が軟質で中央層が硬質な場合は板の中央層のみが拘束されるため強度が高く、伸びの低下とくびれが発生しない高強度高加工性鋼板が得られる。断面平均硬度の差が10ポイント未満以内、および/又は断面最大硬度が20ポイント未満以内では、板全体が均質な硬度のため、現行の材料と何ら変わりは無く、高強度高加工性鋼板を得ることは出来ない。断面平均硬度の差が10ポイント以上、および/又は断面最大硬度が20ポイント以上とすることで引張強度が500MPa以上、破断伸びが10%以上とすることが出来る。 Hardness difference: 10 points or more, 20 points or more The strength increases when the surface layer is hardened, but since the soft central layer is sandwiched between the hard surface layers, the entire plate is constrained and the elongation decreases, and the necking is reduced. It tends to occur and processability decreases. When the surface layer is soft and the central layer is hard, only the central layer of the plate is constrained, so that the strength is high, and a high-strength and highly workable steel plate that does not cause reduction in elongation and constriction is obtained. When the difference in cross-sectional average hardness is less than 10 points and / or the maximum cross-section hardness is less than 20 points, the entire plate is homogeneous, so there is no difference from the current material, and a high strength and high workability steel sheet is obtained. I can't do that. When the difference in cross-sectional average hardness is 10 points or more and / or the maximum cross-section hardness is 20 points or more, the tensile strength can be 500 MPa or more and the elongation at break can be 10% or more.
本発明の高強度加工性缶用鋼板においては、上記した結晶粒径に関し、表面から板厚の1/8の深さまでの間の平均結晶粒径から、板厚の3/8の深さから板厚の4/8の深さまでの間の平均結晶粒径を引いた平均結晶粒径差が1μm以上であるのが好ましい。この平均結晶粒径差が1μm以上である方が、強度と延性に対して優れた特性を両立する鋼板を得ることができるからである。これは、板厚の1/8の深さの結晶粒径が大きいことにより軟質化して伸びが向上し、板厚の3/8の深さから板厚の4/8の深さの結晶粒径が小さく硬質で高強度なため、高強度と延性が両立し、容易に引張強度が500MPa以上、破断伸びが10%以上とすることが出来る。 Average crystal grain size difference: 1 μm or more In the steel sheet for high-strength workable cans of the present invention, the above-mentioned crystal grain size is determined from the average crystal grain size between the surface and a depth of 1/8 of the plate thickness. It is preferable that an average crystal grain size difference obtained by subtracting an average crystal grain size from a depth of 3/8 to a depth of 4/8 of the plate thickness is 1 μm or more. This is because a steel sheet having both excellent strength and ductility properties can be obtained when the average crystal grain size difference is 1 μm or more. This is because the crystal grain size is 1 / 8th of the plate thickness and softens due to the large crystal grain size, so that the elongation is improved, and the crystal grains having a depth of 3 / 8th of the plate thickness to 4 / 8th of the plate thickness. Since the diameter is small and it is hard and has high strength, high strength and ductility are compatible, and the tensile strength can be easily set to 500 MPa or more and the breaking elongation can be set to 10% or more.
平均N量差が10ppm未満では、板全体が均質なN量のため、表層のN量が低下することによる大きな軟質化は期待できないが、平均N量の差が10ppm以上とすることで、表層はN量が低いことで固溶強化に寄与する固溶Nが少ないことにより軟質化し、中心層はN量が高く硬質なため、高強度と延性が両立し、容易に引張強度が500MPa以上、破断伸びが10%以上とすることが出来る。よって、高強度高加工性鋼板が得られ易い。 Average N amount difference: 10 ppm or more If the average N amount difference is less than 10 ppm, since the entire plate has a uniform N amount, large softening due to a decrease in the N amount of the surface layer cannot be expected, but the difference in the average N amount is By setting the surface layer to 10 ppm or more, the surface layer is softened by a small amount of solid solution N that contributes to solid solution strengthening because the amount of N is low, and the center layer is hard because the amount of N is high and hard, so both high strength and ductility are achieved. The tensile strength can easily be 500 MPa or more and the elongation at break can be 10% or more. Therefore, it is easy to obtain a high-strength and highly workable steel plate.
平均窒化物数密度比が1.5以上では、表層の窒化物数密度が大きくなり、窒化物による析出強化が発生するため大きな軟質化は期待できないが、平均窒化物数密度比を1.5より小さくすることで容易に引張強度が500MPa以上、破断伸びが10%以上とすることが出来る。よって、高強度高加工性鋼板が得られ易い。 About Average Nitride Number Density Ratio: 1.5 or Less When the average nitride number density ratio is 1.5 or more, the nitride number density of the surface layer increases and precipitation strengthening due to nitride occurs, so it cannot be expected to be soft. However, by making the average nitride number density ratio smaller than 1.5, the tensile strength can be easily made 500 MPa or more and the breaking elongation can be made 10% or more. Therefore, it is easy to obtain a high-strength and highly workable steel plate.
本発明の高強度高加工性缶用鋼板は、連続鋳造によって製造された上記組成からなる鋼スラブを用い、熱間圧延を行った後に620℃未満の温度で巻き取り、次いで、86%以上の一次冷間圧延率で、一次冷間圧延の最終スタンドの冷間圧延率が30%以上の圧延を行い、引き続きアンモニアガスが0.020vol%未満の雰囲気中で焼鈍を行い、次いで、20%以下の圧延率で二次冷間圧延を行うことで作成する。 Next, the manufacturing method of the steel plate for cans of this invention is demonstrated.
The steel sheet for a high-strength, high-workability can of the present invention uses a steel slab having the above composition produced by continuous casting, and after being hot-rolled, wound at a temperature of less than 620 ° C., and then 86% or more At the primary cold rolling rate, rolling is performed with a cold rolling rate of 30% or more in the final stand of the primary cold rolling, followed by annealing in an atmosphere where the ammonia gas is less than 0.020 vol%, and then 20% or less. It is created by performing secondary cold rolling at a rolling rate of.
熱間圧延後の巻取り温度が620℃以上であると、形成するパーライト組織が粗大となり、これが脆性破壊の起点となるために局部伸びが低下して10%以上の破断伸びが得られない。よって、熱間圧延後の巻取り温度は620℃未満とする。より好ましくは、560℃~620℃である。 Winding temperature after hot rolling: less than 620 ° C. If the winding temperature after hot rolling is 620 ° C. or more, the pearlite structure to be formed becomes coarse, and this becomes the starting point of brittle fracture, so the local elongation decreases. Thus, the elongation at break of 10% or more cannot be obtained. Therefore, the coiling temperature after hot rolling is less than 620 ° C. More preferably, it is 560 ° C to 620 ° C.
一次冷間圧延率が小さい場合、最終的に極薄の鋼板を得るために熱間圧延と二次冷間圧延の圧延率を大きくする必要がある。熱間圧延率を大きくすることは上述の理由から好ましくなく、二次冷間圧延率は後述する理由により制限する必要がある。以上の理由により、一次冷間圧延率を86%未満とすると製造が困難となる。したがって、一次冷間圧延率は86%以上とする。より好ましくは、90~92%である。 Primary cold rolling rate: 86% or more When the primary cold rolling rate is small, it is necessary to increase the rolling rate of hot rolling and secondary cold rolling in order to finally obtain a very thin steel plate. Increasing the hot rolling rate is not preferable for the above-described reason, and the secondary cold rolling rate needs to be limited for the reason described later. For the above reasons, when the primary cold rolling rate is less than 86%, the production becomes difficult. Therefore, the primary cold rolling rate is 86% or more. More preferably, it is 90 to 92%.
鋼板の表層を粗大粒として軟質化するためには最終スタンドの圧延率を大きくして、鋼板表層に歪を導入することによって、焼鈍時のフェライト粒成長を促進する必要がある。中心層と比較して表層の結晶粒径を1μm粗大化させるには、一次冷間圧延の最終スタンド圧延率を30%以上とすることが必要である。 Final stand rolling ratio of primary cold rolling: 30% or more In order to soften the surface layer of the steel sheet as coarse grains, increase the rolling rate of the final stand and introduce strain into the steel sheet surface layer, thereby annealing ferrite during annealing. It is necessary to promote grain growth. In order to increase the grain size of the surface layer by 1 μm compared to the center layer, it is necessary to set the final stand rolling ratio of primary cold rolling to 30% or more.
焼鈍では、表層の窒化を抑制するために、雰囲気中のアンモニアガスの濃度を0.020vol%未満とすることが必要である。好ましくは0.018vol%以下であり、より好ましくは0.016vol%以下である。また、焼鈍により再結晶が完了する必要がある。操業効率および薄鋼板の焼鈍中の破断防止の観点から均熱温度は600~750℃とすることが好ましい。 Annealing requires that the concentration of ammonia gas in the atmosphere be less than 0.020 vol% in order to suppress nitridation of the surface layer. Preferably it is 0.018 vol% or less, More preferably, it is 0.016 vol% or less. Moreover, it is necessary to complete recrystallization by annealing. The soaking temperature is preferably 600 to 750 ° C. from the viewpoint of operation efficiency and prevention of breakage during annealing of the thin steel sheet.
二次冷間圧延率は20%以下とする。二次冷間圧延率を20%超えとすると、二次冷間圧延による加工硬化が過大となり、10%以上の破断伸びが得られなくなる。したがって、二次冷間圧延率は20%以下とする。好ましくは15%以下、より好ましくは、10%以下である。 Secondary cold rolling rate: 20% or less The secondary cold rolling rate is 20% or less. If the secondary cold rolling rate exceeds 20%, work hardening by secondary cold rolling becomes excessive, and a breaking elongation of 10% or more cannot be obtained. Therefore, the secondary cold rolling rate is 20% or less. Preferably it is 15% or less, More preferably, it is 10% or less.
以上により得られた鋼板にSnめっきを両面に連続的に施して、片面Sn付着量2.8g/m2のぶりきを得た。試験結果を表2、表3に示す。なお、表3中の結晶粒径、N量および窒化物数密度は、平均結晶粒径、平均N量および平均窒化物数密度をそれぞれ意味する。 A steel containing the component composition shown in Table 1 and the balance being Fe and inevitable impurities was made as a trial, and a steel slab was obtained by casting. After the obtained steel slab was reheated at 1250 ° C., hot rolling and primary cold rolling were performed under the conditions shown in Table 2. The finish rolling temperature of hot rolling is 890 ° C., and pickling is performed after rolling. Subsequently, after the primary cold rolling, the secondary cold rolling was performed under the conditions shown in Table 2 and continuous annealing at a soaking temperature of 630 ° C. and a soaking time of 25 seconds.
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 . The test results are shown in Tables 2 and 3. In Table 3, the crystal grain size, N content, and nitride number density mean the average crystal grain size, average N content, and average nitride number density, respectively.
また、めっき鋼板のサンプルを採取し、圧延方向断面における、平均結晶粒径および結晶粒の展伸度を測定した。圧延方向断面における平均結晶粒径および結晶粒の展伸度は、鋼板の垂直断面を研磨しナイタルエッチングにより粒界を現出させた上で、「JISG 0551」に記載の直線試験線による切断法により測定した。 The plated steel sheet (cover) obtained as described above was subjected to a heat treatment equivalent to baking at 210 ° C. for 10 minutes, and then subjected to a tensile test. In the tensile test, tensile strength (breaking strength) and elongation at break were measured at a tensile speed of 10 mm / min using a JIS No. 5 size tensile test piece.
Moreover, the sample of the plated steel plate was extract | collected and the average crystal grain diameter and the expansion degree of the crystal grain in the cross section of a rolling direction were measured. The average crystal grain size and the degree of crystal grain elongation in the cross section in the rolling direction are determined by grinding the vertical cross section of the steel sheet and revealing the grain boundary by night etching, and then cutting with the straight test line described in “JISG 0551” Measured by the method.
エリクセン値(貫通割れ発生時の成形高さ)が6.5mm以上を◎、6.5mm未満で6.0mm以上を○、6.0mm未満を×とした。 The moldability was tested by a method specified in JIS Z 2247 using a tester specified in JIS B 7729.
The Erichsen value (molding height at the time of the occurrence of through cracking) is 6.5 mm or more, 未 満, less than 6.5 mm, 6.0 mm or more is ◯, and less than 6.0 mm is x.
Claims (7)
- 質量%で、C:0.070%以上0.080%未満、Si:0.003%以上0.10%以下、Mn:0.51%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:0.010%以下を含有し、残部はFeおよび不可避的不純物からなり、圧延方向断面において、平均結晶粒径が5μm以上、結晶粒の展伸度が2.0以下であり、板厚の3/8の深さから板厚の4/8の深さまでの間の断面の平均ビッカース硬度から、表面から板厚の1/8の深さまでの間の断面の平均ビッカース硬度を引いた硬度差が10ポイント以上、および/又は板厚の3/8の深さから板厚の4/8の深さまでの間の断面の最大ビッカース硬度から、表面から板厚の1/8の深さまでの間の断面の最大ビッカース硬度を引いた硬度差が20ポイント以上、引張強度が500MPa以上、破断伸びが10%以上であることを特徴とする高強度高加工性缶用鋼板。 In mass%, C: 0.070% or more and less than 0.080%, Si: 0.003% or more and 0.10% or less, Mn: 0.51% or more and 0.60% or less, P: 0.001% or more 0.100% or less, S: 0.001% or more and 0.020% or less, Al: 0.005% or more and 0.100% or less, N: 0.010% or less, the balance being Fe and inevitable impurities In the cross section in the rolling direction, the average crystal grain size is 5 μm or more and the degree of elongation of the crystal grains is 2.0 or less, from a depth of 3/8 of the plate thickness to a depth of 4/8 of the plate thickness. The difference in hardness obtained by subtracting the average Vickers hardness of the cross section between the surface and the depth of 1/8 of the plate thickness from the average Vickers hardness of the cross section between 10 points and / or the depth of 3/8 of the plate thickness From the maximum Vickers hardness of the cross-section between 1 to 4/8 of the plate thickness, from the surface High strength and high workability characterized by a hardness difference of 20 points or more, a tensile strength of 500 MPa or more, and a breaking elongation of 10% or more, which is obtained by subtracting the maximum Vickers hardness of the cross section between 1 / 8th of the thickness. Steel plate for cans.
- 前記結晶粒径に関して、表面から板厚の1/8の深さまでの間の平均結晶粒径から、板厚の3/8の深さから板厚の4/8の深さまでの間の平均結晶粒径を引いた平均結晶粒径差が1μm以上であることを特徴とする請求項1に記載の高強度高加工性缶用鋼板。 Regarding the crystal grain size, the average crystal grain size from the average crystal grain size between the surface and the depth of 1/8 of the plate thickness to the depth of 3/8 of the plate thickness to the depth of 4/8 of the plate thickness. The steel sheet for a high-strength, high-workability can according to claim 1, wherein a difference in average crystal grain size minus the grain size is 1 μm or more.
- 前記窒素量に関して、板厚の3/8の深さから板厚の4/8の深さまでの間の平均N量から、表面から板厚の1/8の深さまでの間の平均N量を引いた平均N量差が10ppm以上であることを特徴とする請求項1または2に記載の高強度高加工性缶用鋼板。 Regarding the nitrogen amount, the average N amount between the depth of 3/8 of the plate thickness and the depth of 4/8 of the plate thickness to the average N amount of 1/8 of the plate thickness from the surface. The steel sheet for a high-strength, high-workability can according to claim 1 or 2, wherein the drawn average N amount difference is 10 ppm or more.
- 直径1μm以下0.02μm以上の窒化物に関し、表面から板厚の1/8の深さまでの間の平均窒化物数密度よりも、表面から板厚の1/4の深さまでの間の平均窒化物数密度が大きいことを特徴とする請求項1乃至3のいずれかに記載の高強度高加工性缶用鋼板。 For nitrides having a diameter of 1 μm or less and 0.02 μm or more, the average nitridation between the surface and the depth of 1/4 of the plate thickness is greater than the average nitride number density between the surface and the depth of 1/8 of the plate thickness The steel sheet for a high-strength, high-workability can according to any one of claims 1 to 3, wherein the object number density is large.
- 前記直径1μm以下0.02μm以上の窒化物に関し、表面から板厚の1/20の深さまでの間の平均窒化物数密度を、表面から板厚の1/4の深さまでの間の平均窒化物数密度で割った値が1.5より小さいことを特徴とする請求項1乃至4のいずれかに記載の高強度高加工性缶用鋼板。 With respect to nitrides having a diameter of 1 μm or less and 0.02 μm or more, the average nitride number density from the surface to a depth of 1/20 of the plate thickness is defined as the average nitride number density from the surface to a depth of 1/4 of the plate thickness. The steel sheet for a high-strength and high-workability can according to any one of claims 1 to 4, wherein a value divided by the number density is smaller than 1.5.
- 前記炭素量に関して、鋼中固溶Cの量が51ppm以上であることを特徴とする請求項1乃至5のいずれかに記載の高強度高加工性缶用鋼板。 The steel sheet for a high-strength, high-workability can according to any one of claims 1 to 5, wherein the amount of solid solution C in the steel is 51 ppm or more with respect to the carbon content.
- 質量%で、C:0.070%以上0.080%未満、Si:0.003%以上0.10%以下、Mn:0.51%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:0.010%以下を含有し、残部はFeおよび不可避的不純物からなる鋼を連続鋳造によりスラブとし、熱間圧延を行った後に620℃未満の温度で巻き取り、次いで、トータルで86%以上の一次冷間圧延率で、一次冷間圧延の最終スタンドの冷間圧延率が30%以上の圧延を行い、引き続きアンモニアガスが0.020vol%未満の雰囲気中で焼鈍を行い、次いで、20%以下の圧延率で二次冷間圧延を行うことを特徴とする高強度高加工性缶用鋼板の製造方法。 In mass%, C: 0.070% or more and less than 0.080%, Si: 0.003% or more and 0.10% or less, Mn: 0.51% or more and 0.60% or less, P: 0.001% or more 0.100% or less, S: 0.001% or more and 0.020% or less, Al: 0.005% or more and 0.100% or less, N: 0.010% or less, the balance being Fe and inevitable impurities The steel comprising slab is made into a slab by continuous casting, and after hot rolling, it is wound at a temperature of less than 620 ° C., and then the primary cold rolling rate of 86% or more in total is used to cool the final stand of the primary cold rolling. The rolling is performed at a rolling rate of 30% or more, followed by annealing in an atmosphere where ammonia gas is less than 0.020 vol%, and then performing secondary cold rolling at a rolling rate of 20% or less. A method for producing steel sheets for high strength and high workability cans.
Priority Applications (5)
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EP11845152.5A EP2634282A1 (en) | 2010-12-01 | 2011-11-22 | Steel sheet for can, and process for producing same |
KR1020137016568A KR101570755B1 (en) | 2010-12-01 | 2011-11-22 | Steel sheet for can having high strength and high formability, and method for manufacturing the same |
CA2818682A CA2818682C (en) | 2010-12-01 | 2011-11-22 | Steel sheet for can having high strength and high formability, and method for manufacturing the same |
US13/990,596 US20130294963A1 (en) | 2009-12-02 | 2011-11-22 | Steel sheet for can having high strength and high formability, and method for manufacturing the same |
CN2011800575709A CN103270183A (en) | 2010-12-01 | 2011-11-22 | Steel sheet for can, and process for producing same |
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JP2010268084A JP4957843B2 (en) | 2009-12-02 | 2010-12-01 | Steel plate for can and manufacturing method thereof |
JP2010-268084 | 2010-12-01 |
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KR (1) | KR101570755B1 (en) |
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MX2016014062A (en) | 2014-04-30 | 2017-02-14 | Jfe Steel Corp | High strength steel sheet for container, and method for producing same. |
CN105838994B (en) * | 2016-04-26 | 2018-03-06 | 江苏省沙钢钢铁研究院有限公司 | Chrome plating and its manufacture method, crown plug |
CN106868401B (en) * | 2017-03-21 | 2018-10-12 | 德龙钢铁有限公司 | A kind of Low Defectivity bottle cap tinplate base-material and minimizing production technology |
WO2022129991A1 (en) * | 2020-12-16 | 2022-06-23 | Arcelormittal | Tin coated steel sheet and manufacturing method thereof |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6296618A (en) | 1985-10-23 | 1987-05-06 | Kawasaki Steel Corp | Manufacture of top for easy open can |
JPS637336A (en) | 1986-06-27 | 1988-01-13 | Nippon Steel Corp | Production of extra-thin steel sheet for welded can having excellent flanging property |
JP2004323905A (en) | 2003-04-24 | 2004-11-18 | Nippon Steel Corp | Extra thin steel sheet for container having remarkably excellent can characteristic, and its manufacturing method |
JP2006009069A (en) * | 2004-06-24 | 2006-01-12 | Nippon Steel Corp | High-rigidity steel sheet causing little damage to surface coating film after having been worked, and manufacturing method therefor |
JP2007177315A (en) | 2005-12-28 | 2007-07-12 | Nippon Steel Corp | Continuously annealed dr steel sheet for welded can having excellent flange formability and production method |
JP2009263788A (en) * | 2008-04-03 | 2009-11-12 | Jfe Steel Corp | High-strength steel plate for can and method for manufacturing the high-strength steel plate |
JP2011001609A (en) * | 2009-06-19 | 2011-01-06 | Jfe Steel Corp | Steel sheet for can having high strength and high workability and method for producing the same |
JP2011137223A (en) * | 2009-12-02 | 2011-07-14 | Jfe Steel Corp | Steel sheet for can and method for producing the same |
-
2011
- 2011-11-22 CA CA2818682A patent/CA2818682C/en not_active Expired - Fee Related
- 2011-11-22 EP EP11845152.5A patent/EP2634282A1/en not_active Withdrawn
- 2011-11-22 CN CN2011800575709A patent/CN103270183A/en active Pending
- 2011-11-22 KR KR1020137016568A patent/KR101570755B1/en not_active IP Right Cessation
- 2011-11-22 WO PCT/JP2011/077446 patent/WO2012073914A1/en active Application Filing
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6296618A (en) | 1985-10-23 | 1987-05-06 | Kawasaki Steel Corp | Manufacture of top for easy open can |
JPS637336A (en) | 1986-06-27 | 1988-01-13 | Nippon Steel Corp | Production of extra-thin steel sheet for welded can having excellent flanging property |
JP2004323905A (en) | 2003-04-24 | 2004-11-18 | Nippon Steel Corp | Extra thin steel sheet for container having remarkably excellent can characteristic, and its manufacturing method |
JP2006009069A (en) * | 2004-06-24 | 2006-01-12 | Nippon Steel Corp | High-rigidity steel sheet causing little damage to surface coating film after having been worked, and manufacturing method therefor |
JP2007177315A (en) | 2005-12-28 | 2007-07-12 | Nippon Steel Corp | Continuously annealed dr steel sheet for welded can having excellent flange formability and production method |
JP2009263788A (en) * | 2008-04-03 | 2009-11-12 | Jfe Steel Corp | High-strength steel plate for can and method for manufacturing the high-strength steel plate |
JP2011001609A (en) * | 2009-06-19 | 2011-01-06 | Jfe Steel Corp | Steel sheet for can having high strength and high workability and method for producing the same |
JP2011137223A (en) * | 2009-12-02 | 2011-07-14 | Jfe Steel Corp | Steel sheet for can and method for producing the same |
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CN103270183A (en) | 2013-08-28 |
KR101570755B1 (en) | 2015-11-27 |
CA2818682A1 (en) | 2012-06-07 |
KR20130087597A (en) | 2013-08-06 |
CA2818682C (en) | 2016-03-29 |
EP2634282A1 (en) | 2013-09-04 |
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