CN102482748A - 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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- CN102482748A CN102482748A CN2010800368973A CN201080036897A CN102482748A CN 102482748 A CN102482748 A CN 102482748A CN 2010800368973 A CN2010800368973 A CN 2010800368973A CN 201080036897 A CN201080036897 A CN 201080036897A CN 102482748 A CN102482748 A CN 102482748A
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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
Abstract
Disclosed is a highly processable steel sheet for a three-piece welded can, which is suitable for practical use. The highly processable steel sheet for a three-piece welded can contains, in mass%, more than 0.0015% but 0.0030% or less of C, 0.10% or less of Si, 0.20-0.80% (inclusive) of Mn, 0.001-0.020% (inclusive) of P, 0.001-0.020% (inclusive) of S, more than 0.040% but 0.100% or less of Al, 0.030% or less of N, 0.0002-0.0050% (inclusive) of B, with the balance made up of Fe and unavoidable impurities. The highly processable steel sheet for a three-piece welded can has a tensile strength in the transverse direction to the rolling direction of 400 MPa or more, and an elongation at break in the transverse direction to the rolling direction of 15% or more. The steel sheet is able to be obtained by hot rolling a steel, which has the above-described composition, at a finish rolling temperature of not less than the Ar3 transformation point but not more than 960 DEG C and a winding temperature of 560-750 DEG C (inclusive), then subjecting the resulting to a primary cold rolling at a reduction of 89-93% and an annealing at 600-790 DEG C, and then subjecting the resulting to a secondary cold rolling at a reduction of more than 6.0% but less than 10.0%.
Description
Technical field
Even the present invention relates to reduce steel plate for tanks and the method for manufacture thereof that thickness of slab also has good processibility.
Background technology
In recent years, in order to enlarge the demand of cylinder of steel, taking to reduce the strategy of system jar cost always.As one of strategy that reduces system jar cost, can enumerate raw-material cost degradation, much less carry out the Twopiece Can of pull and stretch processing, even cylinder is configured as the Three piece Can of main body, also advancing the thin-walled property of employed steel plate always.
For can body being carried out the cylinder shaping and through crimping the end and lid engaged the Three piece Can that forms with can body through welding; SR (the once cold rolling that use is made through once cold rolling and subsequent annealing, temper rolling; Single Reduce) material; For the beverages can of coffee etc., use the steel plate of the thickness of about 0.175mm.
In addition,, the method for carrying out cold rolling DR (secondary cold-rolling, Double Reduce) material after the annealing used is once more arranged, compare with the SR material and reduce thickness of slab easily as the method that makes the steel plate attenuation.Above-mentioned DR material is mainly used in deep-drawn ironed can etc. as steel plate for tanks.
The DR material is being used under the situation of Three piece Can, the processibility of steel plate becomes problem.For the Three piece Can body,,, implements cylinder the flange processing of the diameter at expansion two ends after being shaped for lid and bottom are carried out crimping.Cylinder is shaped and mainly uses the method that rectangular steel plate is rolled into cylinder and carries out electric welding, but under the situation of using the DR material, adds man-hour at flange, near weld part, produces the crackle of steel plate sometimes.Special, recently, as the method for manufacture of three beverages cans, main flow is the method for carrying out the welding of can body along the rolling direction of steel plate.Therefore, what in flange processing, extension strain takes place mainly is the rolling right angle orientation of steel plate, important thereby the processibility of this direction becomes.
In addition, a part of canned drinks such as coffee will pass through the distillation sterilization process after filling content.In this distillation sterilization process, jar exposes to the open air under the pressure of the water vapor above 100 ℃, therefore, needs to bear the tank intensity of above-mentioned external pressure.In this case, what influence tank intensity is the armor plate strength of can body circumferential direction, and under the situation of can body being welded along the rolling direction of steel plate, the armor plate strength of rolling right angle orientation becomes important.
Based on above background, disclose a kind of in the patent documentation 1 through in ultra low-carbon steel, adding the method that improves the processibility of weld part with the B of C amount and the corresponding amount of thickness of slab.
Disclose a kind of in the patent documentation 2 through the weight ratio of B in the ultra low-carbon steel and N suitably being controlled the method for the steel plate of making the excellent weldability that is equivalent to temper T3.
Disclose a kind of in the patent documentation 3 through nitride, the form of sulfide, kind, amount in the ultra low-carbon steel that adds B are controlled at the method for making the steel plate with high working property in the proper range.
The prior art document
Patent documentation
Patent documentation 1: No. 3379375 communique of Japanese Patent
Patent documentation 2: TOHKEMY 2001-247917 communique
Patent documentation 3: TOHKEMY 2003-231948 communique
Summary of the invention
Invent problem to be solved
Yet all there is following problem in above-mentioned prior art.
For the steel plate of record in the patent documentation 1; The reroll rate is big, and therefore, the ductility of rolling right angle orientation is not enough; No problem under the situation of welding along the rolling right angle orientation of steel plate; But under the situation of the welding of carrying out can body along rolling direction, it is bigger to add the possibility that cracks man-hour at flange, thereby is not suitable for as three beverage steel plate for tanks.
For the method for manufacture of the steel plate of record in the patent documentation 2, manufactured steel plates has the hardness of about temper T3, and therefore, when being applied to the thin-walled property of three beverage steel plate for tanks, armor plate strength is not enough.In addition; For the reroll that the rolling rate of defined is 3.5～6%, when utilizing rolling rate to be generally 1～2% temper rolling equipment to make, rolling rate is excessive; It is excessive that thereby equipment load becomes; And when utilizing the reroll equipment that makes in a large number with lubricator to make, rolling rate is too small, thereby the possibility of vibration rolling bad generations such as (チ ヤ タ リ Application グ) is high.
The steel plate that utilizes the method for manufacture of record in the patent documentation 3 and make contains a large amount of S, therefore, lacks high temperature ductility, thereby when making steel billet through continuous casting, may crack.
The present invention In view of the foregoing accomplishes, and its purpose is to provide and is fit to be applied to high working property three welding steel plate for tanks and method of manufacture thereof three beverage steel plate for tanks, that have above rolling right angle orientation tensile strength of 400MPa and good flange processibility.
The method that is used to deal with problems
The inventor furthers investigate in order to address the above problem.Opinion below the result has obtained.
The DR material is implemented cold rolling after annealing once more, therefore, compares with the SR material and to become harder.Therefore, possessing good processibility in order to make steel plate, need have enough elongation at breaks, promptly need be soft starting material.From above-mentioned aspect, the C of carbon steel amount is few more, can become soft more, therefore, is set at the use ultra low-carbon steel among the present invention.
In addition, for the DR material, introducing has the strain that is brought by secondary cold-rolling, because the heat that is provided during welding and recrystallize takes place near weld part zone.Recrystallize the zone compare deliquescing with other parts, therefore, add man-hour at flange, distortion is concentrated and is cracked.In order to prevent above-mentioned phenomenon, need give hardening capacity to steel plate.Through adding the B of appropriate amount, can improve the hardening capacity when welding, thereby can prevent near the softening of weld part.But, when the secondary cold-rolling rate diminishes,, the through hardening effect becomes bigger than mother metal on every side owing to making the intensity of weld part, therefore, add man-hour at flange, and distortion is concentrated and is cracked near the mother metal the weld part.Therefore, need the rolling rate of secondary cold-rolling be limited in the suitable scope.
The present invention is based on above opinion and accomplish, its purport is following.
[1] three welding of a kind of high working property steel plate for tanks; It is characterized in that; In quality %; Contain C: greater than 0.0015% and below 0.0030%, below the Si:0.10%, more than the Mn:0.20% and below 0.80%, more than the P:0.001% and below 0.020%, more than the S:0.001% and below 0.020%, Al: greater than 0.040% and below 0.100%, below the N:0.030%, more than the B:0.0002% and below 0.0050%; Surplus is made up of Fe and unavoidable impurities, and the tensile strength of rolling right angle orientation is more than the 400MPa and the elongation at break of rolling right angle orientation is more than 15%.
[2] method of manufacture of three welding of a kind of high working property steel plate for tanks is characterized in that, steel is processed steel billet through continuous casting, is Ar in finishing temperature
3Transformation temperature above and below 960 ℃, coiling temperature is more than 560 ℃ and under the condition below 750 ℃ said steel billet to be carried out hot rolling; Then; With more than 89% and 93% below rolling rate carry out once cold rolling; Implementing anneal more than 600 ℃ and under the temperature below 790 ℃; Then, with greater than 6.0% and implement secondary cold-rolling, wherein less than 10.0% rolling rate; Said steel has following composition; In quality %, contain C: greater than 0.0015% and below 0.0030%, below the Si:0.10%, more than the Mn:0.20% and below 0.80%, more than the P:0.001% and below 0.020%, more than the S:0.001% and below 0.020%, Al: greater than 0.040% and below 0.100%, below the N:0.030%, more than the B:0.0002% and below 0.0050%, surplus is made up of Fe and unavoidable impurities.
Need to prove that in this manual, the % of expression composition of steel all is quality %.
The invention effect
According to the present invention, can access three welding of high working property steel plate for tanks with the above rolling right angle orientation tensile strength of 400MPa and good flange processibility.
In detail, the present invention can utilize the secondary cold-rolling method to come to make reliably three welding steel plate for tanks of excellent processability with thin thickness of slab through in ultra low-carbon steel, adding B and the secondary cold-rolling rate being set at suitable value.
As a result, through improving the processibility of raw sheet (steel plate), add at the flange of Three piece Can and can not crack man-hour, make and utilize the system jar of the thin DR material of thickness of slab to become possibility, thereby can realize the significantly thin-walled property of Three piece Can.
Embodiment
Be elaborated in the face of the present invention down.
Three welding of high working property of the present invention steel plate for tanks is characterised in that the tensile strength of rolling right angle orientation is more than the 400MPa and the elongation at break of rolling right angle orientation is more than 15%.So; For the steel plate that three high welded tanks of processibility of the present invention are used; Under soft state, give hardening capacity and the secondary cold-rolling rate is set at suitable condition through in ultra low-carbon steel, adding B; Thereby can when guaranteeing the flange processibility of weld part, utilize secondary cold-rolling manufactured poling tole.
The one-tenth of three of high working properties of the present invention welding steel plate for tanks is grouped into describes.
C: greater than 0.0015% and below 0.0030%
Among the present invention,, need starting material be set at soft steel in order to ensure the processibility behind the secondary cold-rolling.Generally speaking, C amount is many more, and it is hard more that steel can become, therefore, make C content on be limited to 0.0030%.The C amount was greater than 0.0030% o'clock, and the processibility of steel plate suffers damage, the difficulty thereby jar processing of systems such as flange processing becomes.On the other hand, make the C amount below 0.0015%, the decarburization cost in the refining procedure can increase, thereby not preferred, and therefore, the lower limit that makes C content is greater than 0.0015%.
Below the Si:0.10%
The Si amount can cause problems such as the rational reduction in surface, erosion resistance variation greater than 0.10% o'clock, therefore, was below 0.10%.
More than the Mn:0.20% and below 0.80%
Mn has red shortness in the hot rolling that prevents to be caused by S, makes the effect of crystal grain miniaturization, is to guarantee the necessary element of preferred material.In order to bring into play these effects, need to add more than at least 0.20%.On the other hand, when excessively adding Mn in a large number, erosion resistance variation, and steel plate generation hardization, thus make flange processibility, undergauge processibility variation, therefore, make to be limited to 0.80%.
More than the P:0.001% and below 0.020%
P makes the steel hardization and makes flange processibility and undergauge processibility variation, makes the also harmful element of variation of erosion resistance simultaneously, therefore, makes to be limited to 0.020% on it.In addition, make the P amount be lower than 0.001%, it is excessive that the dephosphorization cost can become.Therefore, make the following of P amount be limited to 0.001%.
More than the S:0.001% and below 0.020%
S exists with the form of inclusion in steel and causes that ductility reduces, the harmful element of erosion resistance variation.In addition, S measures when excessive, and high temperature ductility lacks, and therefore, can cause the crackle of steel billet in the continuous casting.S measured greater than 0.020% o'clock, these detrimentally affect apparition, and therefore, the S amount is limited in below 0.020%.On the other hand, make S be lower than 0.001%, desulphurization cost can be excessive, and further reduce the S amount and be lower than 0.001% and also can receive above-mentioned detrimentally affect hardly.Therefore, make the following of S amount be limited to 0.001%.
Al: greater than 0.040% and below 0.100%
Al is as the deoxidation material in when steel-making and essential element.Al amount is 0.040% when following, and it is insufficient that deoxidation becomes, inclusion increase and flange processibility variation.On the other hand, the Al amount surpasses at 0.100% o'clock, increases because of aluminum oxide bunch crowd waits the occurrence frequency of the surface imperfection that causes.Therefore, make the Al amount greater than 0.040% and below 0.100%.
Below the N:0.030%
During heavy addition N, the high-temperature ductility variation, thus steel billet cracks in continuous casting.Therefore, make N amount on be limited to 0.030%.
More than the B:0.0002% and below 0.0050%
B is the softening necessary element that is used to prevent weld part, is lower than at 0.0002% o'clock, and its performance can not be not fully exerted.Therefore, make the following of B amount be limited to 0.0002%.On the other hand,, can not expect further to improve performance, cause cost to increase on the contrary even the B amount surpasses 0.0050%.Therefore, make B amount on be limited to 0.0050%.Be preferably more than 0.0011% and below 0.0020%.
Surplus is set at Fe and unavoidable impurities.
Next, the method for manufacture to three welding of high working property of the present invention steel plate for tanks describes.
Three welding of high working property of the present invention steel plate for tanks can be made through following method: use the steel billet of making through continuous casting with above-mentioned composition, implement hot rolling, once cold rolling, anneal and secondary cold-rolling.Imagination is applied to steel plate constructed in accordance the situation of the thin-walled property of three beverage steel plate for tanks.Therefore, it is thinner to require the goods thickness of slab to compare with the steel plate that uses in the past, thereby need be rolled down to below about 0.15mm.Usually, only be difficult to process the thickness of slab below the 0.15mm through once cold rolling.That is, for through the cold rolling thickness of slab that obtains approaching, the load of rolls is become excessive.In addition,, also consider in the hot rolling stage rolling to than thin thickness of slab usually, but when increasing the rolling rate of hot rolled, the temperature of rolling light plate reduces and becomes big in order to reduce the thickness of slab after cold rolling, thus the finishing temperature that can't obtain being scheduled to.And during thickness of slab before reducing to anneal, under the situation of implementing continuous annealing, the possibility that the problems such as fracture or distortion of steel plate take place in the annealing becomes big.For the foregoing reasons, be set among the present invention after annealing implement for the second time cold rolling.
Finishing temperature is Ar
3More than the transformation temperature and below 960 ℃
The hot rolled finishing temperature is lower than Ar
3During transformation temperature, the recrystallize particle diameter after the annealing becomes inhomogeneous, and when surpassing 960 ℃, thickization of recrystallize particle diameter after the annealing is to more than necessity.Therefore, making the hot rolled finishing temperature is Ar
3More than the transformation temperature and below 960 ℃.Be more preferably more than 890 ℃ and below 930 ℃.
Coiling temperature is more than 560 ℃ and below 750 ℃
When the coiling temperature after the hot rolling was lower than 560 ℃, the recrystallize particle diameter after the annealing became meticulous.In addition, when surpassing 750 ℃, the whole material of steel plate becomes inhomogeneous, and it is excessive that the oxide debris growing amount also becomes, therefore not preferred.Therefore, making the coiling temperature after the hot rolling is more than 560 ℃ and below 750 ℃.Be more preferably more than 600 ℃ and below 720 ℃.
With more than 89% and 93% below rolling rate carry out once cold rolling
The once cold rolling rate exerts an influence to the particle diameter after annealing, and is lower than at 89% o'clock, and the recrystallize particle diameter becomes excessive, becomes too small and surpass at 93% o'clock.Therefore, making the once cold rolling rate is more than 89% and below 93%.Be more preferably more than 90% and below 92%.
Carrying out anneal more than 600 ℃ and under the temperature below 790 ℃
Annealing temperature exerts an influence to recrystallize rate, particle diameter.That is, when being lower than 600 ℃, the crystal grain of non-recrystallization becomes too much and the infringement processibility.When surpassing 790 ℃, particle diameter becomes excessive and is difficult to guarantee intensity.Therefore, making annealing temperature is more than 600 ℃ and below 790 ℃.Be more preferably more than 610 ℃ and below 700 ℃.Need to prove crystal grain that can residual non-recrystallization after annealing.
With greater than 6.0% and carry out secondary cold-rolling less than 10.0% rolling rate
The secondary cold-rolling rate is 6.0% when following, and is insufficient by the work hardening that secondary cold-rolling brings, thereby can't obtain the armor plate strength that needs.In addition, because the through hardening effect in when welding, the weld part that intensity has raise becomes greatly with the intensity difference of mother metal, near weld part, cracks man-hour thereby add at flange.On the other hand, making the secondary cold-rolling rate is 10.0% when above, and the work hardening that is brought by secondary cold-rolling becomes excessive, thereby can't obtain sufficient elongation at break.In addition, the strained accumulation that is caused by secondary cold-rolling is big, and therefore, near the ratio (recrystallize rate) that the crystal grain of recrystallize takes place weld part becomes big, and near the intensity the weld part reduces, and therefore adds at flange to be easy to generate crackle man-hour.According to the above, making the secondary cold-rolling rate is greater than 6.0% and less than 10.0%.
Operations such as plating are afterwards carried out according to ordinary method, and are finish-machined to steel plate for tanks.
According to the above, can access three welding of high working property of the present invention steel plate for tanks.And the tensile strength of the rolling right angle orientation of the steel plate that three welded tanks that above-mentioned processibility is high are used is more than 400MPa, and to make the elongation at break of rolling right angle orientation be more than 15%.
Under the situation of three beverage can bodies that are applied to weld along rolling direction; In order to bear the external pressure in the distillation sterilization process; The intensity of rolling right angle orientation is important; Through the tensile strength that makes rolling right angle orientation is more than the 400MPa, even expose to the open air under the distillation environment, also can not produce pit fully or buckles.
In addition; Under the situation of three beverage can bodies that are applied to weld along rolling direction; Do not crack man-hour in order to add at flange; The elongation at break of rolling right angle orientation is important, is more than 15% through the elongation at break that makes rolling right angle orientation, can under the condition that does not crack fully, carry out flange processing.
Embodiment
To contain that the one-tenth shown in the table 1 is grouped into, surplus is by steel melting in actual converter that Fe and unavoidable impurities constitute, and obtains steel billet through continuous metal cast process.Then, resulting steel billet is carried out reheat under 1250 ℃, then, under the condition shown in the table 2, implement hot rolling, once cold rolling, continuous annealing, secondary cold-rolling, thereby process the thickness of slab of 0.14～0.15mm.After hot rolling, implement pickling.Two surfaces of the steel plate of making as above operating implement to plate Sn continuously, and obtaining single face Sn adhesion amount is 2.8g/m
2Tinplate.
The coated steel sheet (tinplate) that as above obtains is equivalent to 210 ℃, 20 minutes application agglomerating thermal treatment, then, carries out tension test.The tension test sheet of JIS5 size is used in tension test, according to JIS Z2241, the tensile strength (breaking tenacity) and the elongation at break of rolling right angle orientation is measured.
In addition, use and implemented to be equivalent to the heat treated steel plate of application agglomerating, through the can body shaping of seam weldering carrying out external diameter 52.8mm; Undergauge is carried out in the end be machined to external diameter 50.4mm; Then, carry out flange and be machined to external diameter 55.4mm, estimate having or not the flange crackle to produce.The average evaluation that will crack in the flange processing portion for *, the average evaluation that will not crack is zero.
Can body is shaped is set at the size of 190g beverages can, and welds along the steel plate rolling direction.Undergauge processing is carried out through mould undergauge mode, and flange processing and utilization spinning flange mode is carried out.
Evaluating test estimates tank intensity.Carry out the crimping of above-mentioned processing and lid and bottom and make hollow vessel, in closed chamber, apply the external pressure of pressing, the pressure when the mensuration tank body damages by pressure from air.To damage pressure by pressure and be lower than 1.7kg/cm
2Average evaluation be *, will be at 1.7kg/cm
2Above average evaluation is zero.This benchmark is to set with the intensity that can bear the common distillation pressure when handling.Need to prove,, the can body central part is implemented 15 reinforcing steel processing in the undergauge first being processed.Reinforcing steel be spaced apart 4mm, the degree of depth is 0.5mm.
The result who as above obtains is shown in Table 3.
According to table 3, the good strength of the present invention example No.1～7, and reach the required above rolling right angle orientation tensile strength of 400MPa of thin-walled property of percentum of the can body of Three piece Can.The elongation at break of rolling right angle orientation also reaches more than 15%.In addition, processibility is also good, also can not crack man-hour even add at flange.Tank intensity behind the system jar is also abundant.
On the other hand, the C content of comparative example No.8 is too much, and therefore, because secondary cold-rolling, ductility suffers damage, and the processibility variation.
In addition, comparative example No.9 does not contain B, and therefore, welding heat affected zone is softization to heavens, thereby in flange processing, cracks.
Comparative example No.10,11 secondary cold-rolling rate are excessive, so processibility is not enough.Comparative example No.12,13 secondary cold-rolling rate are too small, so undercapacity.In addition, the intensity difference of hardened weld part and mother metal is bigger owing to weld, and therefore, in flange processing, cracks.
Utilizability on the industry
Three welding steel plate for tanks of the present invention have high working property and flange excellent processability, therefore, are preferred for the beverages can of coffee for example etc. etc.And, can obtain the high working property steel plate for tanks with thin thickness of slab, thereby realize the significantly thin-walled property of Three piece Can.
Claims (2)
1. three of high working properties weld steel plate for tanks; It is characterized in that; In quality %; Contain C: greater than 0.0015% and below 0.0030%, below the Si:0.10%, more than the Mn:0.20% and below 0.80%, more than the P:0.001% and below 0.020%, more than the S:0.001% and below 0.020%, Al: greater than 0.040% and below 0.100%, below the N:0.030%, more than the B:0.0002% and below 0.0050%; Surplus is made up of Fe and unavoidable impurities, and the tensile strength of rolling right angle orientation is more than the 400MPa and the elongation at break of rolling right angle orientation is more than 15%.
2. the method for manufacture of three welding of high working property steel plate for tanks is characterized in that, steel is processed steel billet through continuous casting, is Ar in finishing temperature
3Transformation temperature above and below 960 ℃, coiling temperature is more than 560 ℃ and under the condition below 750 ℃ said steel billet to be carried out hot rolling; Then; With more than 89% and 93% below rolling rate carry out once cold rolling; Implementing anneal more than 600 ℃ and under the temperature below 790 ℃; Then, with greater than 6.0% and implement secondary cold-rolling, wherein less than 10.0% rolling rate; Said steel has following composition; In quality %, contain C: greater than 0.0015% and below 0.0030%, below the Si:0.10%, more than the Mn:0.20% and below 0.80%, more than the P:0.001% and below 0.020%, more than the S:0.001% and below 0.020%, Al: greater than 0.040% and below 0.100%, below the N:0.030%, more than the B:0.0002% and below 0.0050%, surplus is made up of Fe and unavoidable impurities.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2009-189970 | 2009-08-19 | ||
| JP2009189970A JP5018843B2 (en) | 2009-08-19 | 2009-08-19 | Steel plate for high workability 3-piece welded can and manufacturing method thereof |
| PCT/JP2010/063951 WO2011021646A1 (en) | 2009-08-19 | 2010-08-12 | Highly processable steel sheet for three-piece welded can and method for producing same |
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| CN102482748A true CN102482748A (en) | 2012-05-30 |
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| Country | Link |
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| EP (1) | EP2468909B1 (en) |
| JP (1) | JP5018843B2 (en) |
| KR (1) | KR101390263B1 (en) |
| CN (1) | CN102482748A (en) |
| WO (1) | WO2011021646A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103045937A (en) * | 2012-12-14 | 2013-04-17 | 宝山钢铁股份有限公司 | Secondary cold rolled steel and production method thereof |
| CN104781437A (en) * | 2012-11-07 | 2015-07-15 | 杰富意钢铁株式会社 | Steel sheet for three-piece can and manufacturing process therefor |
| CN106133167A (en) * | 2014-03-28 | 2016-11-16 | 杰富意钢铁株式会社 | Steel plate for tanks and manufacture method thereof |
| CN107109559A (en) * | 2014-11-28 | 2017-08-29 | 杰富意钢铁株式会社 | Bottle cap steel plate and its manufacture method and bottle cap |
| CN109440004A (en) * | 2014-05-30 | 2019-03-08 | 杰富意钢铁株式会社 | Steel plate for tanks and its manufacturing method |
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| JP5424506B2 (en) | 2011-02-28 | 2014-02-26 | 株式会社タニタ | Determination method of 8-isoplastane |
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| JP5810714B2 (en) * | 2011-07-29 | 2015-11-11 | Ｊｆｅスチール株式会社 | High-strength, high-formability steel plate for cans and method for producing the same |
| MY174356A (en) | 2015-02-26 | 2020-04-09 | Jfe Steel Corp | Steel sheet for crown cap, method for manufacturing steel sheet for crown cap, and crown cap |
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- 2010-08-12 WO PCT/JP2010/063951 patent/WO2011021646A1/en active Application Filing
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| JPH10245655A (en) * | 1997-03-04 | 1998-09-14 | Kawasaki Steel Corp | Steel sheet for deformed three piece can and its production |
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| CN104781437A (en) * | 2012-11-07 | 2015-07-15 | 杰富意钢铁株式会社 | Steel sheet for three-piece can and manufacturing process therefor |
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| CN106133167B (en) * | 2014-03-28 | 2018-11-16 | 杰富意钢铁株式会社 | Steel plate for tanks and its manufacturing method |
| US10851434B2 (en) | 2014-03-28 | 2020-12-01 | Jfe Steel Corporation | Steel sheet for can and method for manufacturing the same |
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| CN107109559A (en) * | 2014-11-28 | 2017-08-29 | 杰富意钢铁株式会社 | Bottle cap steel plate and its manufacture method and bottle cap |
| CN107109559B (en) * | 2014-11-28 | 2018-11-06 | 杰富意钢铁株式会社 | Bottle cap steel plate and its manufacturing method and bottle cap |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2468909B1 (en) | 2016-11-23 |
| JP5018843B2 (en) | 2012-09-05 |
| JP2011042816A (en) | 2011-03-03 |
| WO2011021646A1 (en) | 2011-02-24 |
| EP2468909A1 (en) | 2012-06-27 |
| KR20120031509A (en) | 2012-04-03 |
| EP2468909A4 (en) | 2013-05-29 |
| KR101390263B1 (en) | 2014-04-29 |
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