CN103409706B - Steel sheet for high-strength container - Google Patents
Steel sheet for high-strength container Download PDFInfo
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- CN103409706B CN103409706B CN201310296022.2A CN201310296022A CN103409706B CN 103409706 B CN103409706 B CN 103409706B CN 201310296022 A CN201310296022 A CN 201310296022A CN 103409706 B CN103409706 B CN 103409706B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
- 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
- C21D8/0273—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—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
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
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- Materials Engineering (AREA)
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- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The hardness with more than 500MPa is provided, and the steel plate for container of excellent processability and manufacture method thereof.Be (Ar in finishing temperature
3phase point temperature-30) DEG C more than, coiling temperature is carry out hot rolling to steel at 400 ~ 750 DEG C, and carrying out pickling, after cold rolling, carry out the continuous annealing comprising Wetted constructures, then, rolling rate with 20 ~ 50% carry out the 2nd time cold rolling, obtaining tensile strength is thus more than 500MPa, the endurance difference of plate width direction and rolling direction is the steel sheet for high-strength container of below 20MPa, described steel in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.100%, surplus is made up of Fe and inevitable impurity.
Description
The application is the applying date is on April 10th, 2009, application number be 200980112785.9(international application no is PCT/JP2009/057717), denomination of invention is the divisional application of the application for a patent for invention of " steel sheet for high-strength container and manufacture method thereof ".
Technical field
The present invention relates to the steel sheet for high-strength container and the manufacture method thereof that reduce or expand the former material of container processed that are suitable as after welding waits three processing or DI etc. two to process, carry out diameter profile.
Background technology
In recent years, in order to reduce costs, and utilize material to reduce and alleviate carrying capacity of environment, carrying out for making as the thinning goods exploitation of the goods thickness of slab of the steel (steel plate) of former material.
In addition, if owing to making goods thickness of slab thinning, rigidity reduces, and therefore reducing to make up this rigidity, also needing the high strength seeking steel.But, when seeking the high strength of steel, due to hardening, therefore there is the problem cracked in flange processing or necking down processing.
For above-mentioned situation, be currently suggested various manufacture method.
Such as, following method is proposed in patent documentation 1: by Composition Control in steel within the specific limits, and at (Ar
3transformation temperature-30 DEG C) more than terminate hot rolling, then carry out pickling, cold rolling after, carry out continuous annealing, then carry out 2 times cold rolling.
But, in the method for patent documentation 1, owing to making P below 0.02 % by weight to not make flange processibility, necking down processibility and erosion resistance be deteriorated, and make 2 cold rolling rolling rates be 15 ~ 30%, therefore be difficult to effectively process thin goods, thus be difficult to produce, and there is the problem that bad order easily occurs.And also there are the following problems: sometimes crack on steel billet top layer, and the reason that the yield rate becoming goods reduces.And, be difficult to stably manufacture, thus need to improve.
In addition, as the representational manufacture method of the steel plate for container of hard, propose following method, can according to annealing kind suitably choice for use (such as non-patent literature 1).
Hot rolling → pickling → cold rolling → bell-type annealing (BAF) → 2nd time cold rolling (rolling rate: 20 ~ 50%)
Hot rolling → pickling → cold rolling → continuous annealing (CAF) → 2nd time cold rolling (rolling rate: 20 ~ 50%)
But, in the above-mentioned methods, owing to employing the high various ROLLING OIL of viscosity in order to oilness when improving rolling, therefore there is the problem of being adhered to bad order after the rolling caused by the concentration deviation of ROLLING OIL, part oil.And when rolling rate is high, steel plate is stretched due to rolling, therefore the width of steel plate and the endurance difference of rolling direction increase.
To this, the method suppressing lower by the 2nd cold rolling rolling rate can be considered.But, when reducing rolling rate, be difficult to obtain required endurance.
Patent documentation 1: Japanese Patent No. 3108615 publication
Non-patent literature 1: " わ Ga state To お け Ru narrow-necked earthen jar surface treatment Steel plate skill Intraoperative history ", Nippon Steel association, Heisei distribution on October 30th, 10, p.188
As mentioned above, when hope obtains the steel plate for container of sheet thickness, do not have the manufacture method that simultaneously can meet intensity, processibility and productivity, thus present situation expects such manufacture method.
The present invention completes in view of the foregoing, its object is to, and provides and has the intensity that tensile strength TS is more than 500MPa, and the endurance of plate width direction and rolling direction difference is below 20MPa, and the steel plate for container of excellent processability and manufacture method thereof.
Summary of the invention
The present inventor has carried out wholwe-hearted research in order to solve the problem.Its result obtains following opinion.
Contriver finds, by adjustment as the P content becoming to be grouped into, and the rate of being rolled is cold rollingly carry out high strength 20 ~ 50% the 2nd time, and then carry out Wetted constructures when continuous annealing, carbide is separated out equably, and is used as making the site of the stress dispersion adding man-hour by this carbide, not only outward appearance discomfort reduces thus, and the endurance difference of width and rolling direction diminishes, and can guarantee the material of high strength.But also find, by specifying particle diameter, density, the ratio of above-mentioned carbide, the steel plate for container that processibility is more excellent can be obtained.
As mentioned above, in the present invention, by based on above-mentioned opinion control composition, high-strength metal sheet for use in cans is completed.
The present invention is based on above opinion to complete, its purport is as follows.
[1] a kind of steel sheet for high-strength container, it in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.100%, surplus is made up of Fe and inevitable impurity, tensile strength TS is more than 500MPa, and the endurance of plate width direction and rolling direction difference is below 20MPa.
[2] a kind of steel sheet for high-strength container, it in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.020%, surplus is made up of Fe and inevitable impurity, tensile strength TS is more than 500MPa, and the endurance of plate width direction and rolling direction difference is below 20MPa.
[3] manufacture method for steel sheet for high-strength container, is characterized in that, is (Ar in finishing temperature
3phase point temperature-30) DEG C more than, coiling temperature is carry out hot rolling to steel at 400 ~ 750 DEG C, and having carried out pickling, cold rolling after, carry out the continuous annealing comprising Wetted constructures, then, rolling rate with 20 ~ 50% carry out the 2nd time cold rolling, described steel in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.100%, surplus is made up of Fe and inevitable impurity.
[4] manufacture method for steel sheet for high-strength container, is characterized in that, is (Ar in finishing temperature
3phase point temperature-30) DEG C more than, coiling temperature is carry out hot rolling to steel at 400 ~ 750 DEG C, and having carried out pickling, cold rolling after, carry out the continuous annealing comprising Wetted constructures, then, rolling rate with 20 ~ 50% carry out the 2nd time cold rolling, described steel in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.020%, surplus is made up of Fe and inevitable impurity.
In addition, in this manual, represent that the % of the composition of steel is quality %.And in the present invention, " steel sheet for high-strength container " refers to the steel plate for container that tensile strength TS (following, to be sometimes called for short TS) is more than 500MPa.
And, steel sheet for high-strength container of the present invention with the former material of container, tank with former material for object.No matter with or without surface treatment, all can implement zinc-plated, nickel plating tin, chromium plating (plating of so-called Wuxi) or organic coating etc., can be applied in the purposes of extremely wide scope.
And although be not particularly limited thickness of slab, from the view point of maximally utilising the present invention to obtain effect, thickness of slab is preferably below 0.30mm, more preferably below 0.20mm.Be particularly preferably below 0.170mm.
Embodiment
Below, the present invention is described in detail.
The steel sheet for high-strength container that the endurance difference of steel plate for container of the present invention to be TS be more than 500MPa, plate width direction and rolling direction is below 20MPa.And in the present invention, by adjustment P content, and rolling rate when making the 2nd time cold rolling (following, sometimes cold rolling also referred to as 2 times) is 20 ~ 50%, can provide the steel plate for container of high strength.
The one-tenth of steel plate for container of the present invention is grouped into and is described.
C：0.01～0.05%
If C composition make at most 2 times cold rolling after steel plate hardening to need more than, tank processed, necking down processibility are deteriorated.And, become and add because of the significant hardening of weld part the element making man-hour HAZ crack at flange.If C is more than 0.05%, then these impacts become remarkable, therefore make C be less than 0.05%.On the other hand, if C composition becomes extremely low, then needing to implement the secondary cold-rolling of high rolling rate to maintain the intensity of container, therefore making C be more than 0.01%, be preferably more than 0.02% and less than 0.04%, more preferably more than 0.02% and less than 0.03%.
Below Si:0.04%
Add Si if a large amount of, produce the variation of surface texture, the variation of erosion resistance.Therefore, Si is made to be less than 0.04%.
Mn：0.1～1.2%
Mn is the effective element of hot tearing to preventing from being caused by S.And, by adding according to S amount, the effect preventing crackle can be obtained.And, also there is the effect making crystal grain miniaturization.In order to play these effects, need the Mn at least adding more than 0.1%.On the other hand, if add in a large number, then demonstrate the tendency that erosion resistance is deteriorated, and make more than steel plate hardening to needs, thus flange processibility, necking down processibility are deteriorated, therefore make its upper limit be 1.2%.Be preferably less than 0.35%.
P：0.0020～0.100%
P is the composition making steel hardening, in the present invention, contains the P of predetermined amount according to required intensity.If be less than 0.0020%, then can not obtain the TS of more than 500MPa, therefore make P content be more than 0.0020%.On the other hand, time above to needs containing excessive P composition, erosion resistance is deteriorated.And, flange processibility, necking down processibility are deteriorated.If P content is more than 0.100%, then the problems referred to above become remarkable, therefore make its upper limit be 0.100%.When P content is 0.0020 ~ 0.020%, the suitable intensity brought by interpolation P and the effect of secondary cold-rolling described later, can obtain higher intensity, therefore preferably.
Below S:0.10%
S exists with the form of inclusion in steel, is the element making the ductility of steel plate reduce and then erosion resistance is deteriorated.Therefore, less than 0.10% is.Be preferably less than 0.030%.
Al：0.001～0.100%
Al is the necessary element of deoxidation of steel.If its amount is less than 0.001%, deoxidation is insufficient, the variation of the flange processibility causing inclusion to cause, the variation of necking down processibility.Therefore, more than 0.001% is.On the other hand, Al and N composition combine, solid solution N is reduced, if but solid solution N excessively reduce, required intensity can not be obtained.Therefore, Al content is made to be less than 0.100%.Be preferably 0.035 ~ 0.075%.
Below N:0.10%
N can not cause the hardness of weld part to rise and the element useful to raising intensity.But if content crosses the remarkable hardening of steel plate at most, the danger former material of rolling (steel billet) cracking defect enlarges markedly, otherwise flange processibility, necking down processibility is then made to be deteriorated.Therefore, N is made to be less than 0.10%.Preferably be less than 0.05%.And, from the view point of preventing crackle of steel billet, more preferably make N be less than 0.01%.More preferably less than 0.005%.As mentioned above, by reducing N, can crackle of steel billet be reduced, thus steel billet can not be needed to repair and yield rate is improved.
Surplus is Fe and inevitable impurity.
Surplus beyond mentioned component is Fe and inevitable impurity.In addition, as inevitable impurity, such as, below Sn:0.01% can be allowed.
Steel plate for container of the present invention has above-mentioned composition, and has the TS of more than 500MPa, and the endurance difference of plate width direction and rolling direction is below 20MPa.Owing to having the TS of more than 500MPa, even if therefore the thinning rigidity of thickness of slab does not still reduce.And owing to making the endurance difference of plate width direction and rolling direction for below 20MPa, therefore flange processing, necking down add and can not crack man-hour.
Below, the manufacture method of steel sheet for high-strength container of the present invention is described.
By employing the generally well-known melting method of converter etc. by the molten steel of above-mentioned composition, then, make the former material of rolling (steel billet) by generally well-known castmethods such as continuous metal cast processs.Then, use the former material of these rollings, make hot-rolled sheet by hot rolling.
Temperature extracted out by steel billet: 1050 ~ 1300 DEG C (optimum condition)
If make the extraction temperature of steel billet be more than 1050 DEG C, then, in the hot rolling of subsequent processing, fully can guarantee high hot rolling end temp.On the other hand, if make extraction temperature be less than 1300 DEG C, then the surface texture of steel plate is not finally deteriorated.Therefore, steel billet is extracted temperature out and is preferably more than 1050 DEG C and less than 1300 DEG C.
Finishing temperature (hot rolling end temp): (Ar
3phase point temperature-30) DEG C more than
In order to the cold-rolling property and article characteristic that make subsequent handling reach good, need to make hot rolling end temp be (Ar
3phase point temperature-30) DEG C more than.If lower than (Ar
3phase point temperature-30) DEG C, then the metal structure coarse of final goods, becomes during tank processed and easily produces uneven surface.In addition, if hot rolling end temp is low temperature, then produce muscle phenomenon, easily produce the bad order after forming process.Therefore, hot rolling end temp is made to be (Ar
3phase point temperature-30) DEG C more than.
Coiling temperature: 400 ~ 750 DEG C
If coiling temperature is too low, the shape of hot-rolled sheet is deteriorated, and then becomes the pickling of subsequent processing, the obstacle of cold rolling manipulation, is therefore set to more than 400 DEG C.On the other hand, if coiling temperature is too high, separate out at hot rolling motherboard stage aluminium nitride, thus become enough solid solution N that can not guarantee needed for strengthening.And, in hot rolling motherboard, form the tissue that carbide is assembled, the effect that the carbide that can not obtain being caused by overaging described later is evenly separated out, and this brings detrimentally affect to the erosion resistance of steel plate.And with the increase of the scale thickness that surface of steel plate produces, pickling is deteriorated.In order to avoid these problems, need to make coiling temperature be less than 750 DEG C.
Pickling, cold rolling is carried out to the hot-rolled sheet as above manufactured, makes cold-reduced sheet.As long as pickling is according to acid removing surface scales such as well-established law hydrochloric acid, sulfuric acid.
The rolling rate that (after pickling) is cold rolling: more than 80% (optimum condition)
If rolling rate is less than 80%, then sometimes can not obtain the abundant grain refined of tissue after annealing, therefore be preferably more than 80%.In addition, in the steel plate of the former material that the present invention is such, in order to realize the abundant miniaturization of tissue, rolling rate is more preferably more than 85%.On the other hand, do not need to be particularly limited the upper limit of rolling rate, the suitably setting such as ability of hot rolling, cold rolling equipment group can be considered.
Annealing temperature: the recrystallization temperature (optimum condition) of less than 800 DEG C
If remaining non-recrystallization tissue in steel plate, then cause that plasticity during tank processed is bad, bad order etc., therefore need to implement recrystallize process by continuous annealing.But, if excessively improve annealing temperature, then produce the defect such as thermal flexure or plate fracture when continuous annealing.And because the crystal grain of exception grows, the danger causing appearance characteristics to be deteriorated increases.Therefore, preferably carry out within the scope of the recrystallization temperature that annealing temperature is less than 800 DEG C.
And, as long as in this temperature range, just do not need specially to keep constant temp.From the stability of operation, more than 5s and the soaking equivalent time of below 60s are fully.If the soaking time of more than 5s, then formed and make the precipitation of the carbide in the site of the stress dispersion adding man-hour become abundant, therefore preferably.
Wetted constructures
In order to make the carbide of being separated out by above-mentioned annealing disperse equably further and effectively form stress dispersion site, need to carry out Wetted constructures.Wetted constructures, preferably after above-mentioned annealing, is cooled to the temperature range of 300 ~ 500 DEG C with the speed of cooling of 10 DEG C/more than s, and keeps more than 5s the temperature range of 300 ~ 500 DEG C.By being cooled to the temperature range of 300 ~ 500 DEG C with the speed of cooling of 10 DEG C/more than s, carbide becomes easy precipitation, if keep more than 5s in the temperature range of 300 ~ 500 DEG C, then can guarantee the precipitation of uniform carbide.And, by carrying out such Wetted constructures, though carry out under the rolling rate of 20 ~ 50% shown below 2nd time cold rolling, the endurance difference that still can make plate width direction and rolling direction is below 20MPa.By carrying out Wetted constructures in such a situa-tion, particle diameter can be made to be that less than 1.5 μm and particle diameter are greater than 1.5 μm and the density of carbide below 3.0 μm and ratio are preferable range described later.
2nd cold rolling rolling rate: 20 ~ 50% (preferably 20 ~ 30%)
In order to ensure the yield strength of the compressive strength of welded tank, i.e. steel plate, need the after continuous annealing the 2nd time cold rolling (following, be sometimes referred to as 2 times cold rolling).Particularly, use the situation that have adjusted the former material of P content of the present invention if consider, then need to make 2 cold rolling rolling rates to be at least 20%.On the other hand, if rolling rate is more than 50%, then the anisotropy of material characteristic increases, and the endurance difference in plate width direction and rolling (rolling) direction is more than 20MPa.And, make the flange processibility in new plate preparation method (the plate preparation method that the rolling direction of steel plate is parallel with the direction of principal axis of can body), necking down processibility is significantly deteriorated.And due to welding during tank processed, the burst size of strain increases, and the softening of welding heat affected zone becomes remarkable, thus becomes and easily produces flange crack.Therefore, rolling rate is set to less than 50%.Be preferably more than 20% and less than 30%, but also suitably can select according to the armor plate strength being target with P content.Specifically, be preferably greater than 0.020% at P content and in high-content situation below 0.100%, be set to lower rolling rate.
In the present invention, can cold rolling at 2 times after, the surface (at least one surface) of cold-rolled steel sheet forms coating, thus makes Coated Steel.The coating formed on the surface can adopt any materials being applied to steel plate for container.As coating, zinc-plated, chromium plating, nickel plating, nickel plating chromium can be illustrated.And, after above-mentioned plating process, carry out application, stickup organic resin film etc. also without any problem.
Embodiment
By the steel melting that converter will be made up of Fe and inevitable impurity containing the composition shown in table 1, surplus, make steel billet by continuous metal cast process.Then, steel billet is extracted out, and temperature is 1200 DEG C, hot rolling finishing temperature is 900 DEG C, coiling temperature is 650 DEG C, implements hot rolling, make the hot-rolled sheet that final thickness is 2.0mm to above-mentioned steel billet.Then, the de-scale process utilizing pickling is implemented to these hot-rolled sheets, then implement rolling rate be 90% cold rolling, make the cold-reduced sheet that final thickness is 0.20mm, then, carry out soaking temperature is 750 DEG C, soaking time is 10 ~ 30s continuous annealing, Wetted constructures and 2 times cold rolling, make cold-rolled steel sheet.
In addition, Wetted constructures condition and 2 cold rolling rolling rates are as shown in table 2 and table 3.
Table 1
Utilize following method, structure observation is carried out to the steel plate as above obtained, obtain density and the ratio of carbide particle diameter.And, carry out following test, characteristic is evaluated.As above the cold-rolled steel sheet obtained is imbedded resol (bakelite), and grind cross section.Then, use mixing picric acid, sodium hydroxide and the sodium picrate solution that obtains as corrosive fluid, 80 DEG C, under the condition of 60s, implement the dip treating in corrosive fluid.Then, carbide is observed in 3 visuals field (scope of about 0.1375mm × 0.1375mm) by the opticmicroscope of 400 times.In each visual field, by visual, obtain particle diameter less than 1.5 μm, particle diameter be greater than 1.5 μm and below 3.0 μm, particle diameter is greater than the number of the carbide of 3.0 μm, and obtains the density in 3 visuals field and the mean value of ratio.Now, the particle diameter of carbide is minimum diameter, and such as, carbide shape is rectangle or oval when there is minor axis and major diameter, is particle diameter in the present invention with minimum diameter.
(i) tension test
Cut No. JIS13-B tension test sheet from the central part of the width of these cold-rolled steel sheets along rolling (L) direction, implement tension test with the rate of straining pinblock speed of 10mm/s, measure tensile strength TS and yield strength YS.In addition, tension test is implemented within 1 day after goods.Tension test sheet being set to No. JIS13-B test film is to reduce the phenomenon ruptured at gauge length outward as far as possible.
(ii) endurance of plate width direction and rolling direction is poor
Obtain obtained by the stretching test measurement of above-mentioned (i) YS, with No. JIS13-B tension test sheet cut on plate width direction is measured in the same manner as (i) to the difference between the YS obtained.
(iii) necking down processibility
Plating Sn process (the Sn adhesion amount of one side is 2.8g/m2) is carried out to these cold-rolled steel sheets, makes Coated Steel.After application/printing/transparent varnish processing is carried out on the surface of this Coated Steel, do not use punching oil and to carry out 100 deep drawings to above-mentioned steel plate under the following conditions shaping, shaping the referring to of this deep drawing is implemented cup drawing and then is implemented 2 re-drawings processing, the production rate of the drawing fold of research eck.
Deep drawing condition of molding
Lip diameter: 200mm Φ
Lubricating condition: do not use punching oil
The drawing ratio of the 1st drawing: 1.5
The drawing ratio of the 2nd drawing: 1.2
The drawing ratio of the 3rd drawing: 1.2
The wrinkle resistant pressure of 1st ~ 3 drawing: optimum condition
Flange is processed: elongation 8%
Re-drawing modular angle radius: 0.45mm
Process velocity: 0.3m/s
(iv) resistance to flange crack
In the deep drawing of (iii) is shaping, the production rate of research flange crack.
(v) outward appearance
These cold-rolled steel sheets of visual observation, will be judged as that gloss or color distinct portions are set to bad order.If find 1 place's bad order in observed 100m unit, then this 100m is set to bad order portion, observes 10000m and obtain bad order rate.
(vi) crackle of steel billet
By the situation of the crackle of steel billet of the billet surface after visual observation continuous casting.
If find 1 place's crackle in observed 1m unit, then this 1m is set to bad order, observes 10m and obtain bad order rate.
The result of gained and condition are together shown in table 2 and table 3.
Table 2
Table 3
Can be confirmed by table 2 and table 3, the present invention's example No.8 ~ 10,13 ~ 18,26 ~ 28,31 ~ 36 have sufficient intensity, and the endurance of plate width direction and rolling direction difference is below 20MPa, such as, is enough to the performance reaching three machining needs.And good appearance, does not produce eck fold and flange crack.And known, the density of carbide, ratio be in preferable range No.8 ~ 10,13 ~ 15,26 ~ 28, the processibility of 31 ~ 33 is more excellent.
On the other hand, do not carry out the comparative example No.1 of Wetted constructures, 2,19, the rolling rate of the secondary cold-rolling of 20 is low, can not obtain intensity.No.3 ~ 5,21 ~ 23 the rolling rate of secondary cold-rolling be more than 20%, intensity increases, but the endurance difference in L direction and C direction is more than 20MPa, and the generation of eck fold, flange crack is remarkable.And, produce bad order.
In addition, the No.6,7,11,12,24,25,29,30 that the rolling rate of secondary cold-rolling is less than 20% can not obtain intensity.
And, about density, the ratio of carbide, obtain following opinion.Steel sheet for high-strength container of the present invention, from the view point of processibility, preferable particle size is that the density of the carbide of less than 1.5 μm is greater than 102/10000 μm
2, and particle diameter is greater than 1.5 μm and the density of carbide below 3.0 μm is greater than 63/10000 μm
2.And preferable particle size is that the carbide number of less than 1.5 μm is greater than 52% relative to the ratio of the total number of carbide, and particle diameter is that the carbide number of less than 3.0 μm is greater than 85% relative to the ratio of the total number of carbide.
Particle diameter is that the density of the carbide of less than 1.5 μm is greater than 102/10000 μm
2, and particle diameter is greater than 1.5 μm and the density of carbide below 3.0 μm is greater than 63/10000 μm
2, can guarantee thus enough to add man-hour plays function carbide as stress dispersion site, processibility becomes more excellent.It is further preferred that the density that particle diameter is the carbide of less than 1.5 μm is 130/10000 μm
2above, particle diameter is greater than 1.5 μm and the density of carbide below 3.0 μm is 80/10000 μm
2above.
And, if the carbide number that particle diameter is less than 1.5 μm is greater than 52% relative to the ratio of the total number of carbide, and, particle diameter is that the carbide number of less than 3.0 μm is greater than 85% relative to the ratio of the total number of carbide, the effect then playing the carbide of function as stress dispersion site improves further, and processibility is further improved.It is further preferred that the carbide number that particle diameter is less than 1.5 μm is more than 55% relative to the ratio of the total number of carbide, and particle diameter is the carbide number of less than 3.0 μm is more than 90% relative to the ratio of the total number of carbide.
And the density of above-mentioned carbide and ratio, can by carrying out anneal to the steel plate after cold rolling and control under predetermined circumstances.Specifically, in the continuous annealing operation after cold rolling, the thermal history of steel plate is adjusted to after in pre-determined range and carries out Wetted constructures.
And, table 3 be make N content be 0.0065%, 0.0043%, namely in the embodiment of preferable range being less than 0.01%.As shown in Table 3, by making N content be less than 0.01%, not finding crackle of steel billet completely, preventing crackle of steel billet to produce.
According to the present invention, can obtain the TS with more than 500MPa, the endurance difference of plate width direction and rolling direction is below 20MPa, and adds the steel sheet for high-strength container of the excellent processability do not cracked man-hour in flange processing and necking down.
And, in the present invention, by adjustment P content, and make the 2nd cold rolling rolling rate be 20 ~ 50% to carry out high strength, solve the problem of the endurance difference of the problem of appearance after rolling, width and rolling direction.
In addition, by making N composition be less than 0.01% preferable range, can crackle of steel billet be prevented, suppress goods yield rate reduce.
Industry utilizes possibility
Steel plate for container of the present invention, do not crack and excellent intensity can be obtained in necking down processing or flange processing, therefore, it is possible to be suitable as such as with electronic units such as the non-food containers such as food product containers, purolator, battery such as tank etc. for the container of representative uses with former material.
Claims (2)
1. a steel sheet for high-strength container, it in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.100%, surplus by Fe and inevitably impurity form, in steel plate, particle diameter is that the density of the carbide of less than 1.5 μm is greater than 102/10000 μm
2, particle diameter is greater than 1.5 μm and the density of carbide below 3.0 μm is greater than 63/10000 μm
2, tensile strength TS is more than 500MPa, and the endurance of plate width direction and rolling direction difference is below 20MPa.
2. a steel sheet for high-strength container, it in mass %, containing C:0.01 ~ 0.05%, below Si:0.04%, Mn:0.1 ~ 1.2%, below S:0.10%, Al:0.001 ~ 0.100%, below N:0.10%, P:0.0020 ~ 0.020%, surplus by Fe and inevitably impurity form, in steel plate, particle diameter is that the density of the carbide of less than 1.5 μm is greater than 102/10000 μm
2, particle diameter is greater than 1.5 μm and the density of carbide below 3.0 μm is greater than 63/10000 μm
2, tensile strength TS is more than 500MPa, and the endurance of plate width direction and rolling direction difference is below 20MPa.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008-103303 | 2008-04-11 | ||
| JP2008103303 | 2008-04-11 | ||
| JP2008-185660 | 2008-07-17 | ||
| JP2008185660 | 2008-07-17 | ||
| CN2009801127859A CN101999009B (en) | 2008-04-11 | 2009-04-10 | Steel sheet for high-strength container, and method for manufacturing therefor |
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| CN2009801127859A Division CN101999009B (en) | 2008-04-11 | 2009-04-10 | Steel sheet for high-strength container, and method for manufacturing therefor |
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| CN103409706A CN103409706A (en) | 2013-11-27 |
| CN103409706B true CN103409706B (en) | 2015-12-02 |
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| CN2009801127859A Active CN101999009B (en) | 2008-04-11 | 2009-04-10 | Steel sheet for high-strength container, and method for manufacturing therefor |
| CN201310296022.2A Active CN103409706B (en) | 2008-04-11 | 2009-04-10 | Steel sheet for high-strength container |
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| CN2009801127859A Active CN101999009B (en) | 2008-04-11 | 2009-04-10 | Steel sheet for high-strength container, and method for manufacturing therefor |
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| US (1) | US20110168303A1 (en) |
| JP (1) | JP5434212B2 (en) |
| KR (2) | KR20130083487A (en) |
| CN (2) | CN101999009B (en) |
| BR (1) | BRPI0909012A2 (en) |
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| CN103205657A (en) * | 2008-04-03 | 2013-07-17 | 杰富意钢铁株式会社 | High-strength Steel Plate For A Can And Method For Manufacturing Said High-strength Steel Plate |
| FI122143B (en) * | 2009-10-23 | 2011-09-15 | Rautaruukki Oyj | Procedure for the manufacture of a high-strength galvanized profile product and profile product |
| CN102286688A (en) * | 2010-06-21 | 2011-12-21 | 宝山钢铁股份有限公司 | Steel for high-hardness tin plating primitive plate and manufacture method thereof |
| JP5093423B2 (en) | 2010-12-06 | 2012-12-12 | 新日本製鐵株式会社 | Steel plate for aerosol can bottom cover and manufacturing method thereof |
| JP5803660B2 (en) * | 2011-12-26 | 2015-11-04 | Ｊｆｅスチール株式会社 | High-strength, high-formability steel plate for cans and method for producing the same |
| CN103917684B (en) * | 2012-04-19 | 2017-02-22 | 新日铁住金株式会社 | Steel foil and method for producing same |
| CN103290312B (en) * | 2013-06-05 | 2015-01-21 | 首钢总公司 | Production method for increasing work hardening value of 440MPa-level carbon structural steel |
| CN103757534B (en) * | 2013-12-27 | 2016-01-20 | 首钢总公司 | A kind of cold-rolled steel sheet and production method thereof with good flange welding property |
| BR112016025380B1 (en) | 2014-04-30 | 2021-03-09 | Jfe Steel Corporation | high-strength steel sheet for containers and method for producing the same |
| US11359255B2 (en) * | 2017-07-31 | 2022-06-14 | Jfe Steel Corporation | Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap |
| CN109423577B (en) | 2017-08-30 | 2021-01-12 | 宝山钢铁股份有限公司 | High-strength multi-phase steel tinning raw plate and manufacturing method thereof |
| CN110541123B (en) * | 2019-09-05 | 2021-06-15 | 首钢集团有限公司 | Cold-rolled strip steel for battery case and preparation method thereof |
| US11965224B2 (en) * | 2020-02-17 | 2024-04-23 | Nippon Steel Corporation | Steel sheet for can and manufacturing method thereof |
| CN115341155B (en) * | 2022-10-17 | 2023-02-24 | 江苏省沙钢钢铁研究院有限公司 | Tin plate and manufacturing method thereof |
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- 2009-04-09 JP JP2009094592A patent/JP5434212B2/en active Active
- 2009-04-10 CN CN2009801127859A patent/CN101999009B/en active Active
- 2009-04-10 MY MYPI2010004425A patent/MY168642A/en unknown
- 2009-04-10 CN CN201310296022.2A patent/CN103409706B/en active Active
- 2009-04-10 BR BRPI0909012A patent/BRPI0909012A2/en not_active IP Right Cessation
- 2009-04-10 KR KR1020137017399A patent/KR20130083487A/en not_active Application Discontinuation
- 2009-04-10 TW TW098111997A patent/TWI390053B/en active
- 2009-04-10 KR KR1020107022588A patent/KR20100122115A/en active Search and Examination
- 2009-04-10 WO PCT/JP2009/057717 patent/WO2009125876A1/en active Application Filing
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| CN1462316A (en) * | 2001-05-09 | 2003-12-17 | 住友金属工业株式会社 | Ferritic heat-resistant steel |
| CN1540023A (en) * | 2003-04-09 | 2004-10-27 | ������������ʽ���� | High speed tool steel and its mfg. method |
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Also Published As
| Publication number | Publication date |
|---|---|
| MY168642A (en) | 2018-11-27 |
| CN103409706A (en) | 2013-11-27 |
| TWI390053B (en) | 2013-03-21 |
| TW201000649A (en) | 2010-01-01 |
| KR20130083487A (en) | 2013-07-22 |
| CN101999009A (en) | 2011-03-30 |
| US20110168303A1 (en) | 2011-07-14 |
| CN101999009B (en) | 2013-07-17 |
| KR20100122115A (en) | 2010-11-19 |
| WO2009125876A1 (en) | 2009-10-15 |
| JP5434212B2 (en) | 2014-03-05 |
| BRPI0909012A2 (en) | 2015-09-22 |
| JP2010043349A (en) | 2010-02-25 |
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