Classifications

• • 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
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
  • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
  • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
  • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
  • C21D8/0436—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
  • C21D8/0442—Flattening; Dressing; Flexing
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
  • C21D8/0473—Final recrystallisation annealing
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/004—Dispersions; Precipitations

Definitions

• the present invention relates to a high-strength steel sheet for cans, which is suitable as a material for cans in which the diameter shape is reduced or increased after three-piece processing, such as welding, or two-piece processing, such as drawing and ironing, and to a method for manufacturing the high-strength steel sheet for cans.
• Patent Document 1 proposes a method of performing hot rolling at a temperature of (Ar3 transformation point—30° C.) or more, performing cold rolling, and then performing continuous annealing, while controlling the steel components within a certain range.
• Patent Document 1 in which P is 0.02% by weight or less to prevent deterioration in flanging and necking formability and corrosion resistance, and the draft in second cold rolling ranges from 15% to 30%, it is difficult to efficiently treat and manufacture thin products, and defective appearance tends to occur. Furthermore, stable manufacturing is difficult to achieve, and therefore some improvements are needed.
• Patent Document 2 proposes a method for manufacturing a steel sheet for cans that has a yield stress of at least 550 MPa after coating and baking, the method including hot rolling at a temperature of (Ar3 transformation point—30° C.) or more, predetermined cooling, coiling, water cooling, cold rolling, and subsequent continuous annealing in a predetermined heating pattern, while the steel components and dissolved N are controlled within a certain range.
• Non-patent Document 1 The following methods are proposed as representative methods for manufacturing a high-strength steel sheet for cans, and have been appropriately used depending on the type of annealing (for example, Non-patent Document 1).
• Hot rolling pickling ⁇ cold rolling ⁇ continuous annealing (CAL) ⁇ second cold rolling (draft: 20% to 50%)
• the present invention is as follows:
• a high-strength steel sheet for cans containing, on the basis of mass percent, C: more than 0.02% and 0.10% or less, Si: 0.10% or less, Mn: 1.5% or less, P: 0.20% or less, S: 0.20% or less, Al: 0.10% or less, N: 0.0120% to 0.0250%, dissolved N being 0.0100% or more, and the balance being Fe and incidental impurities.
• a method for manufacturing a high-strength steel sheet for cans including: hot rolling a steel slab at a slab extraction temperature of 1200° C. or more and a finish rolling temperature of (Ar3 transformation temperature—30)° C. or more, the steel slab containing, on the basis of mass percent, C: more than 0.02% but 0.10% or less, Si: 0.10% or less, Mn: 1.5% or less, P: 0.20% or less, S: 0.20% or less, Al: 0.10% or less, N: 0.0120% to 0.0250%, and the balance being Fe and incidental impurities; coiling at a temperature of 650° C. or less; pickling; cold rolling; and then continuously annealing.
• high-strength steel sheet for cans refers to a steel sheet for cans that has a yield stress YP of at least 500 MPa after coating and baking.
• a high-strength steel sheet for cans according to the present invention is intended for a material for cans.
• the high-strength steel sheet for cans may be subjected to tin plating, nickel-tin plating, chromium plating (so-called tin-free plating), or organic coating, and can be used in a wide variety of applications.
• the thickness of the steel sheet is not limited to a particular value, but is preferably 0.3 mm or less and more preferably 0.2 mm or less to get the most out of the present invention. 0.170 mm or less is particularly preferred.
• a high-strength material can be obtained by using a low carbon material as the composition, maintaining the absolute quantity of dissolved N at a certain value or more, and performing hardening by quench aging and strain aging, for example, in a printing process, a film lamination process, or a drying and baking process before can manufacturing.
• a high-strength steel sheet for cans according to the present invention is a steel sheet for cans that has a yield stress YP of at least 500 MPa after coating and baking.
• a high-strength steel sheet for cans can be efficiently produced without second cold rolling or by second cold rolling at a low draft.
• a steel sheet for cans manufactured without second cold rolling that is, manufactured by temper rolling of about 1% after continuous annealing has a total elongation E1 of at least 20% after coating and baking.
• a steel sheet for cans subjected to second cold rolling at a draft of 10% or more but less than 15% has a total elongation E1 above 10% after coating and baking.
• composition of a steel sheet for containers according to the present invention will be described below.
• C More than 0.02% but 0.10% or less
• C is effective in increasing the strength of steel by solid solution strengthening, but forms carbide, thus reducing the ductility and therefore the processibility of a steel sheet.
• a higher amount of C component results in a hard steel sheet after second cold rolling, thus reducing can productivity and necking formability.
• C greatly increases the hardness of a weld, thus causing HAZ cracking in flanging. Because more than 0.10% C significantly exhibits these effects, C is 0.10% or less.
• C is more than 0.02%.
• C ranges from 0.03% to 0.05%.
• Si increases the strength of steel by solid solution strengthening.
• the addition of a large amount of Si causes problems, such as deterioration in surface treatment and corrosion resistance.
• Si is limited to 0.10% or less.
• Si is preferably 0.02% or less.
• Mn is effective in preventing hot tearing caused by S.
• Mn is appropriately added depending on the S content to effectively prevent cracking.
• at least 0.20% Mn is preferably added.
• Mn also has an effect of reducing the size of crystal grains.
• the addition of a large amount of Mn tends to cause a deterioration in corrosion resistance, provides a steel sheet that is harder than required, and causes a deterioration in flanging and necking formability.
• the upper limit is 1.5%.
• Mn ranges from 0.20% to 0.30%.
• P provides very hard steel, causes a deterioration in flanging and necking formability, and causes a considerable deterioration in corrosion resistance.
• P is limited to 0.20% or less.
• P ranges from 0.001% to 0.018%.
• S exists as an inclusion in steel, reduces the ductility of a steel sheet, and causes a deterioration in corrosion resistance.
• S is 0.20% or less.
• S ranges from 0.001% to 0.018%.
• Al combines with dissolved N to form AlN and is effective in reducing the amount of dissolved N.
• An increase in Al content results in an increase in recrystallization temperature.
• the annealing temperature must be increased.
• the formation of AlN reduces the amount of dissolved N, reduces age hardening, and therefore reduces the strength of a steel sheet.
• Al is limited to 0.10% or less.
• Al is desirably 0.020% or more in view of stable operation of a steel melting process.
• Al ranges from 0.020% to 0.060%.
• N promotes age hardening.
• N is positively included.
• age hardening is highly promoted at a N content of 0.0120% or more.
• N content above 0.0250% the risk of cracking in rolled material (slab) increases considerably.
• N ranges from 0.0120% to 0.0250%.
• the amount of dissolved N in a steel sheet for cans must be 0.0100% or more. This is the most important requirement in the present invention.
• a cold-rolled steel sheet according to the present invention is preferably manufactured by pickling a hot-rolled sheet, performing cold rolling, performing continuous annealing, and, if necessary, performing second cold rolling.
• this continuous annealing process because AlN tends to be precipitated out, it is important to control a process in which the amount of dissolved N in a steel sheet for cans (cold-rolled steel sheet) is not less than 0.0100%.
• the amount of N in the form of AlN (hereinafter referred to as “N as AlN”) is determined by an extraction analysis after dissolution in bromine ester as usually performed, and the N as AlN is subtracted from the total N content to determine the amount of dissolved N.
• the total of the amount of dissolved N and the amount of dissolved C is 0.0150% or more.
• the amount of dissolved C may be determined by internal friction measurement or by subtracting the C content in a precipitate extracted from a steel sheet from the total C content.
• the remainder are Fe and incidental impurities.
• incidental impurities may be 0.01% or less Sn.
• a high-strength steel sheet for cans according to the present invention is manufactured by the following method.
• a molten steel having the composition described above is melted by a generally known melting method using a converter or the like and is formed into a rolled material (slab) by a generally known casting method, such as a continuous casting method.
• the rolled material is then hot-rolled into a hot-rolled sheet.
• the slab extraction temperature is 1200° C. or more
• the finish rolling temperature is (Ar3 transformation temperature—30)° C. or more (suitably, at least Ar3 transformation temperature).
• the hot-rolled sheet is then coiled at 650° C. or less, is pickled, is cold-rolled, and is continuously annealed.
• second cold rolling is further performed at a draft of 10% or more but less than 20% (suitably, 10% or more but less than 15%).
• Plating may also be performed.
• a slab is heated in a furnace and is extracted at a temperature of 1200° C. or more. This aims at promoting the decomposition of AlN to achieve a predetermined amount of dissolved N.
• a slab is introduced into and heated in a furnace maintained at this temperature. Finish rolling temperature: (Ar 3 transformation point—30° C.) or more
• the finish rolling temperature in hot rolling is (Ar 3 transformation point—30° C.) or more to effectively reduce the precipitation of AlN and to prevent a deterioration in anisotropy and processibility.
• a finish rolling temperature below (Ar 3 transformation point—30° C.) AlN is precipitated out considerably, dissolved N decreases, and anisotropy and processibility deteriorates.
• the finish rolling temperature is at least the Ar 3 transformation point.
• forced cooling is performed by water cooling. This can reduce the precipitation of AlN.
• the coiling temperature is 650° C. or less to reduce nitrogen fixation by Al. At a coiling temperature above 650° C., the precipitation of AlN increases considerably, and dissolved N decreases. Thus, the intended age hardening cannot be achieved. More preferably, the coiling temperature is 600° C. or less to consistently achieve substantial age hardening.
• air cooling or water cooling is preferably performed in a coiled state. While water cooling can increase productivity, air cooling is preferred in terms of uniform quality of a steel sheet in the sheet width direction and the longitudinal direction.
• a hot-rolled sheet thus manufactured is pickled and cold-rolled into a cold-rolled sheet.
• Pickling follows a routine procedure, and surface scale is removed with an acid, such as hydrochloric acid or sulfuric acid.
• the cold-rolling draft also follows a routine procedure and increases with decreasing sheet thickness.
• soaking is preferably performed at a temperature of 600° C. or more.
• a soaking temperature of 600° C. or more recrystallization proceeds fast, strain caused by cold rolling does not remain, and a sheet has high ductility and is suitable for press working. Soaking at the Ar1 transformation point or higher can further improve the strength and is therefore preferred. It is surmised that soaking at the Ar1 transformation point or higher partly forms a pearlite structure, which contributes to the improved strength.
• temper rolling of about 1% is preferably performed to control the surface roughness and the hardness.
• a cold-rolled steel sheet manufactured through these processes has a total elongation E1 of at least 20% after coating and baking and is a steel sheet for cans that has excellent processibility.
• second cold rolling at a draft of 10% or more but less than 20% may be performed.
• the second cold rolling mainly aims at further increasing the strength.
• the strength can be further increased.
• the strengthening effect can be achieved while the elongation (the total elongation E1 in the range of 8% to 15% after coating and baking) and the processibility are maintained.
• the total elongation E1 above 10% after coating and baking can be achieved.
• a cold-rolled steel sheet subjected to the second cold rolling at a draft of 10% or more but less than 20% has a total elongation E1 in the range of 8% to 15% after coating and baking and is a very high strength steel sheet for cans that has excellent processibility.
• the draft is preferably 10% or more but less than 15%, and a cold-rolled steel sheet having a total elongation E1 of 10% or more after coating and baking can be manufactured.
• a cold-rolled steel sheet is manufactured through these processes.
• the cold-rolled steel sheet is a hard material due to coating and baking before can manufacturing (before press working), and its superiority is more effectively demonstrated when the cold-rolled steel sheet is applied to an ultrathin steel sheet having a thickness of 0.3 mm or less.
• the cold-rolled steel sheet manufactured through the processes described above is a high-strength steel sheet for cans that contains 0.0100% or more dissolved N and that has a yield stress YP of at least 500 MPa after coating and baking.
• a steel sheet for cans according to the present invention can exhibit large elongation and therefore has excellent processibility.
• a steel sheet for cans according to the present invention has undergone substantial age hardening because of dissolved N.
• a steel sheet for cans according to the present invention has a yield stress YP of at least 500 MPa after coating and baking, and the reduction in the thickness of the steel sheet can be achieved advantageously.
• a cold-rolled steel sheet according to the present invention effectively utilizing the effects of dissolved N, has an increased strength after reflowing after plating, and a substantial age hardening phenomenon may occur during a coating and baking process after press forming, thus resulting in a tremendous increase in the strength of cans.
• a plated layer may be formed on a surface (at least one side) of a cold-rolled steel sheet thus manufactured to form a plated steel sheet.
• any plated layer to be applied to a steel sheet for cans is applicable.
• the plated layer include tin plating, chromium plating, nickel plating, and nickel chromium plating. After the plating, coating or an organic resin film may be applied without any problem.
• a steel composed of the components shown in Table 1 was melted in a converter and was formed into a slab by a continuous casting method.
• the slab was then hot-rolled under the conditions shown in Table 2 to form a hot-rolled sheet having a thickness of 2.0 mm.
• the hot-rolled sheet thus formed was then descaled by pickling, was cold-rolled, and was continuously annealed under the conditions shown in Table 2. Part of the sheets were subjected to second rolling. Thus, a cold-rolled steel sheet having a final thickness of 0.17 mm was manufactured.
• the cold-rolled steel sheet thus manufactured was subjected to the measurement of the amount of dissolved N and a tensile test before and after a bake hardenability test.
• the N content in a cold-rolled steel sheet was analyzed by chemical analysis, and the amount of N in the form of AlN was determined by an extraction analysis after dissolution in bromine ester.
• the amount of dissolved N in the cold-rolled steel sheet was calculated by ((the N content in the cold-rolled steel sheet) ⁇ (the amount of N in the form of AlN)).
• a JIS 13-B test piece for tensile test was sampled in the rolling direction from the central part of a cold-rolled steel sheet in the width direction and was subjected to a tensile test at a strain rate crosshead speed of 10 m/s to determine the yield stress YP and the total elongation E1. The tensile test was performed within one day after manufacture. The JIS 13-B test piece for tensile test was selected to minimize the breakage outside the gage marks.
• a JIS 13-B test piece for tensile test was sampled in the rolling direction from the central part of a cold-rolled steel sheet in the width direction, was subjected to 2% tensile prestraining, was then temporarily unloaded, and was subjected to heat treatment at 210° C. for 20 min, which corresponded to coating and baking. Before and after this test, the tensile test described in (ii) was performed.
• Table 3 shows that Nos. 1, 4, 5, and 6 according to working examples had a sufficient yield stress YP and total elongation E1 after coating and baking and had a sufficient strength and processibility, for example, for three-piece processing.
• No. 6 according to a working example which was subjected to second cold rolling at a draft of 10%, had a total elongation E1 above 10%, that is, 12% after coating and baking, in spite of the second cold rolling.
• Nos. 2 and 3 according to comparative examples had an insufficient yield stress YP, did not have the strength and processibility required for three-piece processing, and therefore cannot be subjected to specified processing.
• the present invention can provide a high-strength steel sheet for cans that has a yield stress YP of at least 500 MPa after coating and baking.
• a high-strength steel sheet for cans can be efficiently produced without second cold rolling or by second cold rolling at a low draft.
• a high-strength steel sheet for cans according to the present invention manufactured without second cold rolling, that is, manufactured by temper rolling of about 1% after continuous annealing has a total elongation E1 of at least 20% after coating and baking.
• the draft in the second cold rolling can be set at a suitable range of 10% or more but less than 15% to achieve the total elongation E1 above 10% after coating and baking.
• coating and baking after forming greatly increases the yield stress and accordingly the strength of cans, thus contributing to the reduction in the thickness of the steel sheet.

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• 2009
  • 2009-04-01 WO PCT/JP2009/057153 patent/WO2009123356A1/ja active Application Filing
  • 2009-04-01 US US12/935,564 patent/US20110076177A1/en not_active Abandoned
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