WO2011021646A1 - Highly processable steel sheet for three-piece welded can and method for producing same - Google Patents
Highly processable steel sheet for three-piece welded can and method for producing same Download PDFInfo
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- WO2011021646A1 WO2011021646A1 PCT/JP2010/063951 JP2010063951W WO2011021646A1 WO 2011021646 A1 WO2011021646 A1 WO 2011021646A1 JP 2010063951 W JP2010063951 W JP 2010063951W WO 2011021646 A1 WO2011021646 A1 WO 2011021646A1
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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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/0405—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 of ferrous alloys
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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
- C21D8/0463—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 following 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
- C21D8/0447—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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- 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
Definitions
- the present invention relates to a steel plate for cans having good workability even when the plate thickness is reduced, and a method for producing the same.
- SR Single Reduce
- a means for thinning the steel plate there is a method using a DR (Double Reduce) material that is cold-rolled again after annealing, and it is easy to reduce the plate thickness as compared with the SR material.
- This DR material is mainly used for a drawn can as a steel plate for a can.
- Cylindrical forming mainly uses a method in which a rectangular steel plate is rolled and energized and welded, but when a DR material is used, the steel plate may be cracked in the vicinity of the weld during flange processing.
- a method for producing a three-piece beverage can recently, a method of welding the can body along the rolling direction of the steel sheet has been mainstream. Therefore, elongation deformation in flange processing is mainly in the direction perpendicular to the rolling direction of the steel sheet, and workability in this direction is important.
- some canned beverages such as coffee go through a retort sterilization process after filling the contents.
- the strength of the can that can withstand the external pressure is required.
- it is the strength of the steel plate in the circumferential direction of the can body that affects the strength of the can body.
- the strength of the steel plate in the direction perpendicular to the rolling direction is important.
- Patent Document 1 discloses a method for improving the workability of the welded portion by adding B in an amount corresponding to the amount of C and the thickness of the ultra-low carbon steel.
- Patent Document 2 discloses a method of manufacturing a steel sheet having excellent weldability equivalent to a tempering degree T3 by appropriately controlling the weight ratio of B and N in an ultra-low carbon steel.
- Patent Document 3 discloses a method of manufacturing a steel sheet having high workability by controlling the form, type, and amount of nitride and sulfide in the B-added ultra-low carbon steel within an appropriate range. .
- Patent Document 1 Since the steel sheet described in Patent Document 1 has a high secondary rolling rate, the ductility in the direction perpendicular to the rolling direction is insufficient, and there is no problem when welding is performed along the direction perpendicular to the rolling direction of the steel sheet. When the can body is welded, there is a high possibility of cracking during flange processing, which is not suitable as a steel plate for a three-piece beverage can.
- Patent Document 2 The steel sheet manufacturing method described in Patent Document 2 is insufficient in steel sheet strength to be applied to the thinning of a three-piece beverage can steel sheet because the steel sheet to be manufactured has a hardness of about tempering T3.
- secondary rolling with a specified rolling rate of 3.5 to 6% is too large to produce in a temper rolling facility with a rolling rate of usually 1 to 2%, and the load on the facility is excessive. Therefore, the rolling rate is too small to produce in a secondary rolling facility that uses a large amount of lubricant, and there is a high possibility that rolling defects such as chattering will occur.
- the present invention has been made in view of such circumstances, and a steel plate for a highly workable three-piece welded can having a rolled perpendicular direction tensile strength of 400 Mpa or more suitable for practical use as a steel plate for a three-piece beverage can and excellent flange workability. And it aims at providing the manufacturing method.
- the present inventors have conducted intensive research to solve the above problems. As a result, the following knowledge was obtained.
- DR material Since DR material is cold-rolled again after annealing, it becomes harder than SR material. Therefore, in order for a steel plate to have favorable workability, it is necessary to have sufficient elongation at break, that is, a soft material. In this respect, the carbon steel becomes softer as the C content is smaller. Therefore, in the present invention, an extremely low carbon steel is used.
- the DR material is strained by secondary cold rolling, and recrystallization occurs in the vicinity of the weld due to heat applied during welding. Since the recrystallized region is softer than the other portions, deformation concentrates during the flange processing and causes cracks. In order to prevent this, it is necessary to impart hardenability to the steel sheet. By adding an appropriate amount of B, the hardenability at the time of welding is increased, and softening in the vicinity of the welded portion can be prevented.
- the secondary cold rolling rate is reduced, the strength of the welded portion becomes larger than that of the surrounding base material due to the quenching effect, so that deformation concentrates on the base material in the vicinity of the welded portion at the time of flange processing, resulting in cracks. For this reason, it is necessary to restrict the rolling reduction of secondary cold rolling to an appropriate range.
- the present invention has been made based on the above findings, and the gist thereof is as follows.
- C By mass%, C: more than 0.0015% and 0.0030% or less, Si: 0.10% or less, Mn: 0.20% or more and 0.80% or less, P: 0.001% or more and 0.00. 020% or less, S: 0.001% or more and 0.020% or less, Al: more than 0.040% and 0.100% or less, N: 0.030% or less, B: 0.0002% or more and 0.0050% or less
- the balance is made of Fe and inevitable impurities, the tensile strength in the direction perpendicular to the rolling is 400 MPa or more, and the elongation at break in the direction perpendicular to the rolling is 15% or more.
- High workability 3 pin characterized by secondary cold rolling A method for producing steel plates for steel welding cans.
- % which shows the component of steel is mass% altogether.
- a steel sheet for a high workability three-piece weld can having a rolling perpendicular tensile strength of 400 Mpa or more and excellent flange workability can be obtained.
- the present invention provides a secondary cold rolling of a steel sheet for a three-piece welded can with excellent workability by adding B to an ultra-low carbon steel and setting the secondary cold rolling rate to an appropriate value. By the method, it can be reliably manufactured with a thin plate thickness.
- the steel sheet for a highly workable three-piece welded can of the present invention is characterized in that the tensile strength in the direction perpendicular to the rolling is 400 MPa or more and the elongation at break in the direction perpendicular to the rolling is 15% or more.
- the steel sheet for a three-piece welded can with high workability of the present invention adds B to the ultra-low carbon steel and imparts hardenability while remaining soft, and sets the secondary cold rolling rate to an appropriate condition. By doing so, it is manufactured as an ultrathin steel plate by the secondary cold rolling method while ensuring the flange workability of the welded portion.
- C more than 0.0015% and 0.0030% or less
- steel increases as the amount of C increases, so the upper limit of the C content is set to 0.0030%. If the amount of C exceeds 0.0030%, the workability of the steel sheet is impaired, and can manufacturing such as flange processing becomes difficult.
- the C content is 0.0015% or less, the decarburization cost increases in the refining process, which is not preferable. Therefore, the lower limit of the C content is more than 0.0015%.
- Si 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.
- Mn 0.20% or more and 0.80% 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. . In order to exert these effects, it is necessary to add at least 0.20% or more. On the other hand, if Mn is added in a large amount, the corrosion resistance is deteriorated and the steel sheet is hardened to deteriorate the flange workability and the neck workability, so the upper limit is made 0.80%.
- P 0.001% or more and 0.020% or less P is a harmful element that hardens steel, deteriorates flange workability and neck workability, and at the same time deteriorates corrosion resistance. .020%. Moreover, dephosphorization cost becomes excessive in order to make P amount less than 0.001%. Therefore, the lower limit of the P content is 0.001%.
- S 0.001% or more and 0.020% or less S exists as an inclusion in steel, and is a harmful element that causes reduction in ductility and deterioration in corrosion resistance. Further, if the amount of S is excessive, high temperature ductility becomes poor, which leads to slab cracking in continuous casting. If the S amount exceeds 0.020%, these adverse effects become obvious, so the S amount is limited to 0.020% or less. On the other hand, the desulfurization cost is excessive to make S less than 0.001%, and even if the amount of S is further lowered from 0.001%, the above-mentioned adverse effects are hardly received. Therefore, the lower limit of the S amount is 0.001%.
- Al more than 0.040% and 0.100% or less Al is an element necessary as a deoxidizer during steelmaking.
- the amount of Al is 0.040% or less, deoxidation becomes insufficient, inclusions increase, and flange workability deteriorates.
- the Al content exceeds 0.100%, the occurrence frequency of surface defects due to alumina clusters and the like increases. Therefore, the Al amount is set to more than 0.040% and 0.100% or less.
- N 0.030% or less
- the hot ductility deteriorates and cracking of the slab occurs in continuous casting. Therefore, the upper limit of the N amount is 0.030%.
- B 0.0002% or more and 0.0050% or less B is an essential element for preventing softening of the welded portion, and if it is less than 0.0002%, the performance is not sufficiently exhibited. Therefore, the lower limit of the B amount is 0.0002%. On the other hand, even if the amount of B exceeds 0.0050%, further performance improvement cannot be expected, but the cost is increased. Therefore, the upper limit of the B amount is set to 0.0050%. Preferably, it is 0.0011% or more and 0.0020% or less.
- the balance is Fe and inevitable impurities.
- the steel plate for high workability three-piece welded cans of the present invention is manufactured by applying hot rolling, primary cold rolling, annealing treatment and secondary cold rolling using a steel slab having the above composition produced by continuous casting.
- the steel plate manufactured according to the present invention is assumed to be applied to thinning of a steel plate for a three-piece beverage can. Therefore, the product sheet thickness is required to be thinner than the conventionally used steel sheet, and it is necessary to roll to about 0.15 mm or less. Usually, it is difficult to achieve a sheet thickness of 0.15 mm or less by only one cold rolling. That is, in order to obtain a thin plate thickness by cold rolling, the load on the rolling mill is excessive.
- the second cold rolling is performed after annealing.
- Finish rolling temperature Ar 3 transformation point or more and 960 ° C. or less When the final rolling temperature of hot rolling is less than Ar 3 transformation point, the recrystallized grain size after annealing becomes non-uniform, and when it exceeds 960 ° C., the recrystallized grain after annealing The diameter becomes coarser than necessary. Therefore, the finish rolling temperature of the hot rolling is set to Ar 3 transformation point or higher and 960 ° C. or lower. More preferably, it is 890 degreeC or more and 930 degrees C or less.
- the coiling temperature after hot rolling is set to 560 ° C. or higher and 750 ° C. or lower. More preferably, it is 600 degreeC or more and 720 degrees C or less.
- the primary cold rolling rate affects the grain size after annealing when the rolling rate is 89% or more and 93% or less. If it is less than 89%, the recrystallized grain size becomes excessive, and if it exceeds 93%, it becomes excessively small. . Therefore, the primary cold rolling rate is 89% or more and 93% or less. More preferably, it is 90% or more and 92% or less.
- the annealing temperature at 600 ° C. or higher and 790 ° C. or lower affects the recrystallization rate and the particle size. That is, when the temperature is lower than 600 ° C., the number of non-recrystallized grains becomes excessive and the workability is impaired. If it exceeds 790 ° C, the particle size becomes too large, and it becomes difficult to ensure the strength. Therefore, the annealing temperature is set to 600 ° C. or higher and 790 ° C. or lower. More preferably, it is 610 degreeC or more and 700 degrees C or less. Note that non-recrystallized grains may remain after annealing.
- the rolling rate is more than 6.0% and less than 10.0%, and the secondary cold rolling rate is 6.0% or less, the work hardening by the secondary cold rolling is insufficient and necessary.
- the strength of the steel sheet is not obtained. Further, the strength difference between the welded portion whose strength is increased by the quenching effect at the time of welding and the base material becomes large, and a crack occurs in the vicinity of the welded portion during the flange processing.
- the secondary cold rolling rate is 10.0% or more, work hardening by secondary cold rolling becomes excessive, and sufficient elongation at break cannot be obtained.
- the ratio of recrystallized grains (recrystallization rate) in the vicinity of the welded portion increases, and the strength in the vicinity of the welded portion decreases, resulting in cracking during flange processing It becomes easy. From the above, the secondary cold rolling rate is more than 6.0% and less than 10.0%.
- the subsequent steps such as plating are performed as usual, and finished as a steel plate for cans.
- the steel plate for high workability 3 piece welding cans of this invention is obtained. And this workability is high, and the steel plate for 3 piece welding cans has a tensile strength in the direction perpendicular to the rolling of 400 MPa or more and a breaking elongation in the direction perpendicular to the rolling of 15% or more.
- the strength in the direction perpendicular to the rolling direction is important in order to withstand the external pressure in the retort sterilization process when applied to a three-piece beverage can body that is welded along the rolling direction.
- the tensile strength in the direction perpendicular to the rolling direction is 400 MPa or more. Even if exposed to the environment, there will be no dents or buckling.
- the elongation at break in the direction perpendicular to the rolling direction is important in order to prevent cracking during flange processing when applied to a three-piece beverage can body that is welded along the rolling direction. By doing so, it becomes possible to perform flange processing without causing any cracks.
- a tensile test was performed on the plated steel sheet (blink) obtained as described above after a heat treatment equivalent to coating baking at 210 ° C. for 20 minutes.
- tensile strength breaking strength
- elongation at break in the direction perpendicular to rolling were measured in accordance with JIS Z2241 using a JIS No. 5 size tensile test piece.
- a can body having an outer diameter of 52.8 mm was formed by seam welding using a steel plate that had been subjected to heat treatment equivalent to paint baking, and the end portion was necked in to an outer diameter of 50.4 mm and then flanged to an outer diameter of 55.4 mm. Processing was performed to evaluate the presence or absence of flange cracking. The case where cracking occurred at the flange processed part was evaluated as x, and the case where cracking did not occur was evaluated as ⁇ .
- the can body was formed into a 190 g beverage can size and welded 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.
- a paneling test was conducted to evaluate the strength of the can body.
- a hollow can body was manufactured by performing the above-described processing and tightening of the lid and the bottom, and an external pressure was applied by air pressure in a sealed chamber, and a pressure at which the can body was crushed was measured. Crushing pressure was evaluated as ⁇ and the case where less than 1.7kg / cm 2 ⁇ , of 1.7 kg / cm 2 or more. This standard is set as the strength that can withstand the pressure during general retort processing.
- 15 bead processes were given to the center part of the can body before the neck-in process.
- the bead spacing is 4 mm and the depth is 0.5 mm.
- Nos. 1 to 7 are excellent in strength and have achieved a tensile strength in the perpendicular direction of rolling of 400 MPa or more, which is necessary for thinning several percent of the can body of a three-piece can.
- the elongation at break in the direction perpendicular to the rolling is also 15% or more.
- it is excellent in workability, and no cracks are generated in flange processing.
- the strength of the can after the can-making is sufficient.
- the steel plate for a three-piece welded can of the present invention has high workability and excellent flange workability, it is suitably used for beverage cans such as coffee. Furthermore, it is possible to obtain a steel plate for a highly workable can with a thin plate thickness, and a significant reduction in the thickness of a three-piece can is achieved.
Abstract
Description
[1]質量%で、C:0.0015%超0.0030%以下、Si:0.10%以下、Mn:0.20%以上0.80%以下、P:0.001%以上0.020%以下、S:0.001%以上0.020%以下、Al:0.040%超0.100%以下、N:0.030%以下、B:0.0002%以上0.0050%以下を含有し、残部はFeおよび不可避的不純物からなり、圧延直角方向の引張強度が400MPa以上であり、かつ、圧延直角方向の破断伸びが15%以上であることを特徴とする高加工性3ピース溶接缶用鋼板。
[2]質量%で、C:0.0015%超0.0030%以下、Si:0.10%以下、Mn:0.20%以上0.80%以下、P:0.001%以上0.020%以下、S:0.001%以上0.020%以下、Al:0.040%超0.100%以下、N:0.030%以下、B:0.0002%以上0.0050%以下を含有し、残部はFeおよび不可避的不純物からなる成分を有する鋼を、連続鋳造によりスラブとし、該スラブを仕上げ圧延温度Ar3変態点以上960℃以下、巻き取り温度560℃以上750℃以下で熱間圧延し、次いで、圧延率89%以上93%以下で一次冷間圧延し、600℃以上790℃以下で焼鈍処理を施し、次いで、圧延率6.0%超10.0%未満で二次冷間圧延を施すことを特徴とする高加工性3ピース溶接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。 The present invention has been made based on the above findings, and the gist thereof is as follows.
[1] By mass%, C: more than 0.0015% and 0.0030% or less, Si: 0.10% or less, Mn: 0.20% or more and 0.80% or less, P: 0.001% or more and 0.00. 020% or less, S: 0.001% or more and 0.020% or less, Al: more than 0.040% and 0.100% or less, N: 0.030% or less, B: 0.0002% or more and 0.0050% or less The balance is made of Fe and inevitable impurities, the tensile strength in the direction perpendicular to the rolling is 400 MPa or more, and the elongation at break in the direction perpendicular to the rolling is 15% or more. Steel plate for welding cans.
[2] By mass%, C: more than 0.0015% to 0.0030% or less, Si: 0.10% or less, Mn: 0.20% to 0.80%, P: 0.001% to 0.000. 020% or less, S: 0.001% or more and 0.020% or less, Al: more than 0.040% and 0.100% or less, N: 0.030% or less, B: 0.0002% or more and 0.0050% or less The balance is made of steel having a component composed of Fe and inevitable impurities, and the slab is made into a slab by continuous casting, and the slab is finished at the rolling temperature Ar 3 transformation point to 960 ° C., and the winding temperature is 560 ° C. to 750 ° C. Hot-rolled, then primary cold-rolled at a rolling rate of 89% to 93%, annealed at 600 ° C to 790 ° C, and then rolled at a rolling rate of more than 6.0% and less than 10.0%. High workability 3 pin characterized by secondary cold rolling A method for producing steel plates for steel welding cans.
In addition, in this specification,% which shows the component of steel is mass% altogether.
本発明においては、二次冷間圧延後の加工性を確保するため、素材を軟質な鋼とする必要がある。一般にC量が多くなるほど鋼は硬くなるので、C含有量の上限は0.0030%とする。C量が0.0030%を超えると、鋼板の加工性が損なわれ、フランジ加工等の製缶加工が困難になる。一方、C量を0.0015%以下とするには精錬工程において脱炭コストが大きくなり、好ましくないので、C含有量の下限は0.0015%超とする。 C: more than 0.0015% and 0.0030% or less In the present invention, in order to ensure the workability after secondary cold rolling, it is necessary to use a soft steel material. Generally, steel increases as the amount of C increases, so the upper limit of the C content is set to 0.0030%. If the amount of C exceeds 0.0030%, the workability of the steel sheet is impaired, and can manufacturing such as flange processing becomes difficult. On the other hand, if the C content is 0.0015% or less, the decarburization cost increases in the refining process, which is not preferable. Therefore, the lower limit of the C content is more than 0.0015%.
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、0.10%以下とする。 Si: 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.
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。これらの効果を発揮するためには少なくとも0.20%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、また鋼板が硬質化して、フランジ加工性、ネック加工性を劣化させるので、上限は0.80%とする。 Mn: 0.20% or more and 0.80% 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. . In order to exert these effects, it is necessary to add at least 0.20% or more. On the other hand, if Mn is added in a large amount, the corrosion resistance is deteriorated and the steel sheet is hardened to deteriorate the flange workability and the neck workability, so the upper limit is made 0.80%.
Pは、鋼を硬質化させ、フランジ加工性やネック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ため、その上限を0.020%とする。また、P量を0.001%未満とするには脱リンコストが過大となる。よって、P量の下限は0.001%とする。 P: 0.001% or more and 0.020% or less P is a harmful element that hardens steel, deteriorates flange workability and neck workability, and at the same time deteriorates corrosion resistance. .020%. Moreover, dephosphorization cost becomes excessive in order to make P amount less than 0.001%. Therefore, the lower limit of the P content is 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。また、S量が過大であると高温延性が乏しくなるため、連続鋳造におけるスラブ割れにつながる。S量が0.020%を超えるとこれらの悪影響が顕在化するため、S量は0.020%以下に制限する。一方、Sを0.001%未満とするには脱硫コストが過大であり、0.001%よりさらにS量を下げても上記の悪影響はほとんど受けない。よって、S量の下限は0.001%とする。 S: 0.001% or more and 0.020% or less S exists as an inclusion in steel, and is a harmful element that causes reduction in ductility and deterioration in corrosion resistance. Further, if the amount of S is excessive, high temperature ductility becomes poor, which leads to slab cracking in continuous casting. If the S amount exceeds 0.020%, these adverse effects become obvious, so the S amount is limited to 0.020% or less. On the other hand, the desulfurization cost is excessive to make S less than 0.001%, and even if the amount of S is further lowered from 0.001%, the above-mentioned adverse effects are hardly received. Therefore, the lower limit of the S amount is 0.001%.
Alは、製鋼時の脱酸材として必要な元素である。Al量が0.040%以下であると、脱酸が不十分となり、介在物が増加し、フランジ加工性が劣化する。一方、Al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0.040%超0.100%以下とする。 Al: more than 0.040% and 0.100% or less Al is an element necessary as a deoxidizer during steelmaking. When the amount of Al is 0.040% or less, deoxidation becomes insufficient, inclusions increase, and flange workability deteriorates. On the other hand, when the Al content exceeds 0.100%, the occurrence frequency of surface defects due to alumina clusters and the like increases. Therefore, the Al amount is set to more than 0.040% 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、N量の上限は0.030%とする。 N: 0.030% or less When N is added in a large amount, the hot ductility deteriorates and cracking of the slab occurs in continuous casting.
Therefore, the upper limit of the N amount is 0.030%.
Bは溶接部の軟化を防ぐために必須の元素であり、0.0002%未満ではその性能が十分に発揮されない。従って、B量の下限は0.0002%とする。一方、B量が0.0050%を超えても更なる性能向上は望めず、却ってコスト高を招く。よって、B量の上限は0.0050%とする。好ましくは、0.0011%以上0.0020%以下である。 B: 0.0002% or more and 0.0050% or less B is an essential element for preventing softening of the welded portion, and if it is less than 0.0002%, the performance is not sufficiently exhibited. Therefore, the lower limit of the B amount is 0.0002%. On the other hand, even if the amount of B exceeds 0.0050%, further performance improvement cannot be expected, but the cost is increased. Therefore, the upper limit of the B amount is set to 0.0050%. Preferably, it is 0.0011% or more and 0.0020% or less.
熱間圧延の仕上げ圧延温度がAr3変態点未満であると焼鈍後の再結晶粒径が不均一となり、960℃を超えると焼鈍後の再結晶粒径が必要以上に粗大化する。したがって、熱間圧延の仕上げ圧延温度はAr3変態点以上960℃以下とする。より好ましくは890℃以上930℃以下である。 Finish rolling temperature Ar 3 transformation point or more and 960 ° C. or less When the final rolling temperature of hot rolling is less than Ar 3 transformation point, the recrystallized grain size after annealing becomes non-uniform, and when it exceeds 960 ° C., the recrystallized grain after annealing The diameter becomes coarser than necessary. Therefore, the finish rolling temperature of the hot rolling is set to Ar 3 transformation point or higher and 960 ° C. or lower. More preferably, it is 890 degreeC or more and 930 degrees C or less.
熱間圧延後の巻き取り温度が560℃未満であると焼鈍後の再結晶粒径が細かくなりすぎる。また、750℃を超えると鋼板全体の材質が不均一となり、スケール生成量も過大となるので好ましくない。よって、熱間圧延後の巻き取り温度は560℃以上750℃以下とする。より好ましくは、600℃以上720℃以下である。 If the coiling temperature after hot rolling is less than 560 ° C, the recrystallized grain size after annealing becomes too fine. Moreover, when it exceeds 750 degreeC, the material of the whole steel plate will become non-uniform | heterogenous, and since the amount of scale production | generation becomes excessive, it is unpreferable. Therefore, the coiling temperature after hot rolling is set to 560 ° C. or higher and 750 ° C. or lower. More preferably, it is 600 degreeC or more and 720 degrees C or less.
一次冷間圧延率は焼鈍後の粒径に影響し、89%未満であると再結晶粒径は過大となり、93%を超えると過小となる。従って、一次冷間圧延率は89%以上93%以下とする。より好ましくは、90%以上92%以下である。 Primary cold rolling The primary cold rolling rate affects the grain size after annealing when the rolling rate is 89% or more and 93% or less. If it is less than 89%, the recrystallized grain size becomes excessive, and if it exceeds 93%, it becomes excessively small. . Therefore, the primary cold rolling rate is 89% or more and 93% or less. More preferably, it is 90% or more and 92% or less.
焼鈍温度は再結晶率、粒径に影響を及ぼす。すなわち、600℃未満であると未再結晶粒が過多となり、加工性を損なう。790℃を超えると粒径が大きくなり過ぎ、強度の確保が困難となる。よって、焼鈍温度は600℃以上790℃以下とする。より好ましくは、610℃以上700℃以下である。なお、焼鈍後に未再結晶粒が残存していてもよい。 The annealing temperature at 600 ° C. or higher and 790 ° C. or lower affects the recrystallization rate and the particle size. That is, when the temperature is lower than 600 ° C., the number of non-recrystallized grains becomes excessive and the workability is impaired. If it exceeds 790 ° C, the particle size becomes too large, and it becomes difficult to ensure the strength. Therefore, the annealing temperature is set to 600 ° C. or higher and 790 ° C. or lower. More preferably, it is 610 degreeC or more and 700 degrees C or less. Note that non-recrystallized grains may remain after annealing.
二次冷間圧延率が6.0%以下であると、二次冷間圧延による加工硬化が不十分であり、必要とする鋼板強度が得られない。また、溶接時の焼き入れ効果により強度が上昇した溶接部と母材との強度差が大きくなり、フランジ加工時に溶接部近傍で割れが生じる。一方、二次冷間圧延率が10.0%以上とすると、二次冷間圧延による加工硬化が過大となり、十分な破断伸びが得られなくなる。また、二次冷間圧延による歪みの蓄積量が大きいため、溶接部近傍で再結晶する結晶粒の割合(再結晶率)が大きくなり、溶接部近傍の強度が低下することによりフランジ加工時に割れやすくなる。以上より、二次冷間圧延率は6.0%超10.0%未満とする。 If the rolling rate is more than 6.0% and less than 10.0%, and the secondary cold rolling rate is 6.0% or less, the work hardening by the secondary cold rolling is insufficient and necessary. The strength of the steel sheet is not obtained. Further, the strength difference between the welded portion whose strength is increased by the quenching effect at the time of welding and the base material becomes large, and a crack occurs in the vicinity of the welded portion during the flange processing. On the other hand, if the secondary cold rolling rate is 10.0% or more, work hardening by secondary cold rolling becomes excessive, and sufficient elongation at break cannot be obtained. In addition, since the accumulated amount of strain due to secondary cold rolling is large, the ratio of recrystallized grains (recrystallization rate) in the vicinity of the welded portion increases, and the strength in the vicinity of the welded portion decreases, resulting in cracking during flange processing It becomes easy. From the above, the secondary cold rolling rate is more than 6.0% and less than 10.0%.
圧延直角方向の強度は圧延方向に沿って溶接する3ピース飲料缶胴に適用した場合、レトルト殺菌工程における外圧に耐えるため重要であり、圧延直角方向の引張強度を400MPa以上とすることで、レトルト環境下に晒されても全く窪みや座屈を生じない。
また、圧延直角方向の破断伸びは圧延方向に沿って溶接する3ピース飲料缶胴に適用した場合、フランジ加工に際し割れを生じないために重要であり、圧延直角方向の破断伸びを15%以上とすることで、全く割れを生じることなく、フランジ加工を行うことが可能となる。 By the above, the steel plate for high workability 3 piece welding cans of this invention is obtained. And this workability is high, and the steel plate for 3 piece welding cans has a tensile strength in the direction perpendicular to the rolling of 400 MPa or more and a breaking elongation in the direction perpendicular to the rolling of 15% or more.
The strength in the direction perpendicular to the rolling direction is important in order to withstand the external pressure in the retort sterilization process when applied to a three-piece beverage can body that is welded along the rolling direction. The tensile strength in the direction perpendicular to the rolling direction is 400 MPa or more. Even if exposed to the environment, there will be no dents or buckling.
In addition, the elongation at break in the direction perpendicular to the rolling direction is important in order to prevent cracking during flange processing when applied to a three-piece beverage can body that is welded along the rolling direction. By doing so, it becomes possible to perform flange processing without causing any cracks.
パネリング試験を行い、缶体強度を評価した。上記加工および蓋と底の巻き締めを行って中空缶体を作製し、密閉チャンバー内で空気圧による外圧を加え、缶体の圧壊が生じる圧力を測定した。圧壊圧力が1.7kg/cm2未満の場合を×、1.7kg/cm2以上の場合を○と評価した。この基準は、一般的なレトルト処理時の圧力に耐え得る強度として設定したものである。なお、ネックイン加工の前に、缶胴中央部に15本のビード加工を施した。ビードの間隔は4mm、深さは0.5mmである。 The can body was formed into a 190 g beverage can size and welded 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.
A paneling test was conducted to evaluate the strength of the can body. A hollow can body was manufactured by performing the above-described processing and tightening of the lid and the bottom, and an external pressure was applied by air pressure in a sealed chamber, and a pressure at which the can body was crushed was measured. Crushing pressure was evaluated as ○ and the case where less than 1.7kg / cm 2 ×, of 1.7 kg / cm 2 or more. This standard is set as the strength that can withstand the pressure during general retort processing. In addition, 15 bead processes were given to the center part of the can body before the neck-in process. The bead spacing is 4 mm and the depth is 0.5 mm.
また、比較例のNo.9は、Bを含有していないため、溶接熱影響部が極端に軟質化し、フランジ加工で割れが発生している。
比較例のNo.10、11は、二次冷間圧延率が大きすぎるため、加工性が不足している。比較例のNo.12、13は、二次冷間圧延率が小さすぎるため強度が不足している。また、溶接により硬化した溶接部と母材の強度差が大きいため、フランジ加工において割れが生じている。 On the other hand, no. Since No. 8 has too much C content, ductility is impaired by secondary cold rolling, and workability is inferior.
Moreover, No. of the comparative example. Since No. 9 does not contain B, the weld heat affected zone is extremely softened, and cracks are generated in the flange processing.
Comparative Example No. Nos. 10 and 11 have insufficient workability because the secondary cold rolling rate is too large. Comparative Example No. 12 and 13 are insufficient in strength because the secondary cold rolling rate is too small. Further, since the strength difference between the welded portion hardened by welding and the base material is large, cracks are generated in the flange processing.
Claims (2)
- 質量%で、C:0.0015%超0.0030%以下、Si:0.10%以下、Mn:0.20%以上0.80%以下、P:0.001%以上0.020%以下、S:0.001%以上0.020%以下、Al:0.040%超0.100%以下、N:0.030%以下、B:0.0002%以上0.0050%以下を含有し、残部はFeおよび不可避的不純物からなり、圧延直角方向の引張強度が400MPa以上であり、かつ、圧延直角方向の破断伸びが15%以上であることを特徴とする高加工性3ピース溶接缶用鋼板。 By mass%, C: more than 0.0015% and 0.0030% or less, Si: 0.10% or less, Mn: 0.20% or more and 0.80% or less, P: 0.001% or more and 0.020% or less S: 0.001% or more and 0.020% or less, Al: 0.040% or more and 0.100% or less, N: 0.030% or less, B: 0.0002% or more and 0.0050% or less The balance consists of Fe and inevitable impurities, the tensile strength in the direction perpendicular to the rolling is 400 MPa or more, and the elongation at break in the direction perpendicular to the rolling is 15% or more. steel sheet.
- 質量%で、C:0.0015%超0.0030%以下、Si:0.10%以下、Mn:0.20%以上0.80%以下、P:0.001%以上0.020%以下、S:0.001%以上0.020%以下、Al:0.040%超0.100%以下、N:0.030%以下、B:0.0002%以上0.0050%以下を含有し、残部はFeおよび不可避的不純物からなる成分を有する鋼を、連続鋳造によりスラブとし、
該スラブを仕上げ圧延温度Ar3変態点以上960℃以下、巻き取り温度560℃以上750℃以下で熱間圧延し、次いで、圧延率89%以上93%以下で一次冷間圧延し、600℃以上790℃以下で焼鈍処理を施し、次いで、圧延率6.0%超10.0%未満で二次冷間圧延を施すことを特徴とする高加工性3ピース溶接缶用鋼板の製造方法。 By mass%, C: more than 0.0015% and 0.0030% or less, Si: 0.10% or less, Mn: 0.20% or more and 0.80% or less, P: 0.001% or more and 0.020% or less S: 0.001% or more and 0.020% or less, Al: 0.040% or more and 0.100% or less, N: 0.030% or less, B: 0.0002% or more and 0.0050% or less The balance is made of steel having a component consisting of Fe and inevitable impurities, and slab is formed by continuous casting.
The slab is hot-rolled at a finish rolling temperature Ar 3 transformation point or higher and 960 ° C. or lower, a coiling temperature 560 ° C. or higher and 750 ° C. or lower, and then primary cold-rolled at a rolling rate of 89% or higher and 93% or lower, and 600 ° C. or higher A method for producing a steel sheet for a high workability three-piece welded can, comprising annealing at 790 ° C. or lower and then performing secondary cold rolling at a rolling rate of more than 6.0% and less than 10.0%.
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WO2012144213A1 (en) * | 2011-04-21 | 2012-10-26 | Jfeスチール株式会社 | Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same |
EP2700731A1 (en) * | 2011-04-21 | 2014-02-26 | JFE Steel Corporation | Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same |
EP2700731A4 (en) * | 2011-04-21 | 2015-04-08 | Jfe Steel Corp | Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same |
US10174393B2 (en) | 2011-04-21 | 2019-01-08 | Jfe Steel Corporation | Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same |
CN103717770A (en) * | 2011-07-29 | 2014-04-09 | 杰富意钢铁株式会社 | High-strength high-processability steel sheet for cans and method for producing same |
US10392682B2 (en) | 2012-11-07 | 2019-08-27 | Jfe Steel Corporation | Steel sheet for three-piece can and method for manufacturing the same |
Also Published As
Publication number | Publication date |
---|---|
JP2011042816A (en) | 2011-03-03 |
KR101390263B1 (en) | 2014-04-29 |
CN102482748A (en) | 2012-05-30 |
JP5018843B2 (en) | 2012-09-05 |
EP2468909A4 (en) | 2013-05-29 |
KR20120031509A (en) | 2012-04-03 |
EP2468909A1 (en) | 2012-06-27 |
EP2468909B1 (en) | 2016-11-23 |
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