CN101454470A - DR steel sheet and process for manufacturing the same - Google Patents
DR steel sheet and process for manufacturing the same Download PDFInfo
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- CN101454470A CN101454470A CNA2007800198222A CN200780019822A CN101454470A CN 101454470 A CN101454470 A CN 101454470A CN A2007800198222 A CNA2007800198222 A CN A2007800198222A CN 200780019822 A CN200780019822 A CN 200780019822A CN 101454470 A CN101454470 A CN 101454470A
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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
- 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
- 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
- C21D8/0226—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
- C21D8/0221—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
- 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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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
A DR steel sheet comprising, by mass, 0.02 to 0.06% C, 0.03% or less Si, 0.05 to 0.5% Mn, 0.02% or less P, 0.02% or less S, 0.02 to 0.10% Al, 0.008 to 0.015% N and the balance iron and unavoidable impurities, which DR steel sheet exhibits a solid solution N content in steel sheet (Ntotal-NasAlN) of 0.006% or higher, a total elongation value in rolling direction after aging treatment of 10% or greater, a total elongation value in sheet width direction after aging treatment of 5% or greater and an average Lankford value after aging treatment of 1.0 or below.
Description
Technical field
The present invention relates to a kind of EOE (Easy Open End: easy-open lid; Hereinafter to be referred as EOE) DR of usefulness (Double Reduced: secondary calendering; Hereinafter to be referred as DR) steel plate and manufacture method thereof, this EOE is, by staff can be easily with a part of opening of the cover that in beverages can or normal food jar and other extensive uses, uses.
The application serves as the basis application with Japanese Patent Application 2006-219066 number, and introduces its content.
Background technology
Cover with easy-to-draw function is widely used the cover as metal tin.This cover is roughly divided into: the part open-type cover that is mainly used in beverages can; With the open-shed cover that is mainly used in food cans.Which kind of type all is extensive use of following cover of pop can:, make the peristome fracture on the panel that is formed on cover and open jar by rivet mechanism fixed corbel back slab ( Block) by pull-up.
On the main body of cover of pop can, be formed with unexistent rivet of the lid that does not possess easy-to-draw function and opening guide channel.
The opening guide channel is following formation, uses the machining tool of the point of a knife shape projection with the peristome profile that has formed regulation, exert pressure with high loading from the face side of cover, and be the opening guide channel of cover thickness more than 1/2 so that form the degree of depth.
Combination by protruding shaping of drum and pull and stretch processing forms rivet.And, the rivet that forms is inserted in the hole that is arranged on the corbel back slab, and forms rivet mechanism by carrying out caulking moulding.
The material of the cover of pop can of this pull-up corbel back slab and the type opened jar, adopting and handling steel plate with tin plate and electrolysis chromic acid is the surface treated steel plate and the aluminium sheet of representative.Though according to the difference of content, for example in fruit jar etc., use the tin plate of no application, generally use the material of application.
As tank body or cover develop come like that, in recent years, in cover of pop can in order to realize reducing the use that expense of raw materials also begins to inquire into thin mechanically resistant material.For example, have following patent documentation 1 proposed invention, if be defined as more than the 0.15mm thickness of slab and not enough 0.23mm, a jar property is opened in bending resistance when then reducing the pop can opening and raising.And, also there are following patent documentation 2 proposed inventions, compare preferred soft steel as composition with ultra-low carbon steel, if it is implemented packing annealing method and high draft 2～10%, then open a jar property raising.
In these documents, though a part has been mentioned rivet processing, main purpose is to improve to open a jar property, has the more weak problem of consideration to the system property covered.The easness that the system of considering is at the same time covered is opened in the following patent documentation 3 of jar property with improving, and utilizes the B oxide compound.The starting point of (ボ イ De) becomes easily jar to have the space in the steel plate by making, and eliminates the deterioration of rivet formability by limiting B oxide compound size.Yet,, therefore may be able to not deal with problems in itself because the impurity such as oxide compound that exist in the steel can become the destructive starting point of processing.Though carried out this motion, in fact, because thin mechanically resistant material produces the crack in the rivet molding procedure, so impracticable.On the other hand, as following patent documentation 4 is put down in writing, proposed the following protruding moulding of compound drum, making operation quantity is the above multistages in 3 stages, and has utilized the crooked processing of returning.Combination by protruding moulding of this multistage compound drum and thin mechanically resistant material has realized the practicality of thin mechanically resistant material gradually.
Patent documentation 1: Japanese kokai publication sho 63-109121 communique
Patent documentation 2: Japanese kokai publication sho 64-015326 communique
Patent documentation 3: Japanese kokai publication hei 10-251799 communique
Patent documentation 4:FR9004264 communique
As mentioned above, under the situation of using thin mechanically resistant material, in the protruding moulding of drum of common rivet molding procedure, easily produce the crack.This can infer what the extension deficiency of material caused, in order to remedy this situation, and need be based on having utilized multistage bending-bending to return the rivet moulding of the protruding moulding of compound drum of processing.By multistage ground carry out the being improved effect of Limit Drawing ratio, return the effect that processing can obtain extending material by crooked, the result thinks can moulding.
Yet, in production unit in the past, only possessing the processing space in 2 stages, in order to carry out 3 multistage processing more than the stage, stamping machine and mould all need be reset, there is the problem of the investment that needs wholesale.
Summary of the invention
The present invention In view of the foregoing carries out, its problem provides the production unit of the rivet molding procedure in a kind of 2 stages that can be by in the past and processes DR steel plate EOE, that the rivet processibility is good, and the manufacture method of making this DR steel plate at an easy rate.
The inventor, the result who conscientiously studies in order to solve above-mentioned problem, improve and a kind ofly limit composition of steel, guarantee the rolling direction after the ageing treatment and the general extension value of plate width, and suppressed the DR steel plate and the inexpensive method of manufacturing thereof of the cheapness of average blue gram Ford (the ラ Application Network Off オ-De) value after the ageing treatment.Its main contents are as follows.
(1) DR steel plate of the present invention is, contain C:0.02%～0.06% as its composition of steel with mass%, below the Si:0.03%, Mn:0.05%～0.5%, below the P:0.02%, below the S:0.02%, Al:0.02%～0.10%, N:0.008%～0.015%, and the amount of the solid solution N in the steel plate that is made of balance iron and unavoidable impurities (Ntotal-NasAIN) is more than 0.006%, the general extension value of the rolling direction after the ageing treatment is more than 10%, the general extension value of the plate width after the ageing treatment (aging process) is more than 5%, and the average Lankford value after the ageing treatment is below 1.0.
In addition,,, solid solution N is preferably more than 0.008% so measuring because the many more Lankford values of solid solution N amount are more little, and more preferably more than 0.009%.
(2) manufacture method of DR steel plate of the present invention is for making the method for following DR steel: contain C:0.02%～0.06% as composition of steel with mass%, below the Si:0.03%, Mn:0.05%～0.5%, below the P:0.02%, below the S:0.02%, Al:0.02%～0.10%, N:0.008%～0.015%, and the amount of the solid solution N in the steel plate that is made of balance iron and unavoidable impurities (Ntotal-NasAIN) is more than 0.006%, the general extension value of the rolling direction after the ageing treatment is more than 10%, the general extension value of the plate width after the ageing treatment is more than 5%, and the average Lankford value after the ageing treatment is below 1.0.In this manufacture method, be heated to steel disc more than 1200 ℃ and forge and carry out hot rolling under the temperature at the end more than the Ar3 transformation temperature; At coiling temperature is to become below 600 ℃ to batch hot-rolled steel sheet; After the pickling, to implement the calendering rate be cold rolling more than 80%; The enforcement recrystallization temperature is above, the annealing of not enough Ac1 transformation temperature; And, implement modified calendering rate and be 6%～15% DR calendering.
Effect of the present invention:
Thin continuous annealing DR steel plate in the past, need above rivet molding procedure of 3 stages, relative therewith, DR steel plate of the present invention, become to be grouped into and manufacture method by studying its steel plate, and the Lankford value after the rolling direction after the regulation ageing treatment and the elongation of width and the ageing treatment can carry out the rivet moulding in 2 stages.
As a result, bring into play useful unusual effect on the following industry: the material that use can economize on resources, save energy ground is made, do not need to carry out the facility investment of new wholesale, in the manufacturing process of EOE, also can realize energy-conservationization etc.
Description of drawings
Fig. 1 is the sectional view after the 1st stage of rivet moulding.
Fig. 2 is the sectional view after the 2nd stage of rivet moulding.
Fig. 3 is that sectional view, the symbol t after the caulking processing of rivet is that corbel back slab, symbol d are rivet diameter.
Fig. 4 is the graphic representation of the relation of expression solid solution N and Lankford value.
Embodiment
Below to DR steel plate of the present invention with and the embodiment of manufacture method describe.
In addition, the present invention relates to a kind ofly to limit composition of steel, guarantee the rolling direction after the ageing treatment and the general extension value of plate width, and suppressed the average Lankford value after the ageing treatment cheapness the DR steel plate with and inexpensive method of manufacturing
(about mechanical characteristics)
The present invention is shaped to prerequisite to carry out rivet 2 stages.The profile status of molding procedure is as follows.Fig. 1 represents the sectional view after the protruding moulding of the drum in the 1st stage, Fig. 2 represent the 2nd stage based on the sectional view after the rivet moulding of drawing and forming, Fig. 3 represents the sectional view of the rivet mechanism that obtains by the caulking moulding of carrying out with corbel back slab after the rivet moulding.
At first, in the rivet moulding, require in order to follow the trail of the characteristic of processing.The contriver finds: if the general extension value of the rolling direction after the ageing treatment is the general extension value of the plate width more than 10% and after the ageing treatment is more than 5%, then can follow the trail of the rivet moulding.Though compare with rolling direction, the general extension value of plate width is less, and do not know to follow the trail of the reason of rivet moulding.But, can think as its reason, in the rivet moulding, include drawing and forming, be the effect of Lankford value.That is, known in the such average Lankford value of the present invention is steel plate below 1.0, compare with rolling direction, the Lankford value of plate width becomes big.Therefore, in the processing of plate width, general extension may act on Lankford value mutually additionally and have identical ductility with rolling direction.On the other hand, the general extension value of the plate width after the general extension value of the rolling direction after the ageing treatment is less than 10% and ageing treatment is under the situation of less than 5%, the fracture that produces material when rousing protruding moulding or carrying out drawing and forming in the 2nd stage in the 1st stage.
And, with the caulking moulding of corbel back slab in, rivet diameter is very important.Under the little situation of rivet diameter, the problem that corbel back slab comes off takes place.The characteristic that the inventor has carried out the steel plate that corbel back slab come off by caulking steel plate and corbel back slab relatively found that the average Lankford value after both ageing treatment is different.Surpass 1.0 o'clock rivet diameter at average Lankford value and diminish, 1.0 become big and corbel back slab can not come off with next rivet diameter if be.Though do not know its reason, but be speculated as, under average Lankford value is situation below 1.0, it is big that the Lankford value of the plate width that the Lankford value of the rolling direction that the general extension value is big diminishes, the general extension value is little becomes, and that the plastic fluidity of steel plate becomes is equal, can obtain even and big rivet diameter thus.The mensuration of the Lankford value of thin hard steel plate, only can obtain average Lankford value according to the modulus in tension calculating of steel plate, therefore the deduction of the Lankford value of rolling direction and plate width is rule of thumb carried out, but has carried out the present invention according to above situation.
In addition, generally with 180～220 (200～210) ℃ * carried out ageing treatment in 7～30 minutes, but the condition of the ageing treatment of evaluation test is 210 ℃, 30 minutes.
Afterwards, be in the continuous annealing DR steel plate in the method for making thin steel plate materials at an easy rate, find that the method for above-mentioned physicals is important, below its composition of steel of explanation, manufacture method.
(about composition of steel)
<C：0.02mass％～0.06mass％>
C is a factor of control grain growing, the grain growing that its addition is few more when promoting the alligatoring of crystal grain of hot-rolled steel sheet and annealing more, and the average Lankford value of steel plate (r value) uprises more.Therefore, be to need to make the following of C amount to be limited to 0.02% below 1.0 in order to make the r value.On the other hand, C amount is many more, and crystal grain is separated out many more cementites in refinement and the steel more.This close grain and cementite precipitate become the starting point that produces the space in tension test, and crackle are propagated easily and the general extension value of sheet is reduced, therefore make the C amount on be limited to 0.06%.
＜Si:0.03mass% is following 〉
When heavy addition Si, cause problems such as plating property deterioration and erosion resistance deterioration, therefore preferred its amount is less.But it is the element of sneaking into inevitably when refining, if for a small amount of then do not produce problem in the practicality, therefore make and be limited to 0.03% on it.Especially when the needs superior corrosion resistance, be preferably below 0.02%.
<Mn：0.05mass％～0.5mass％>
Mn is to fixing S and prevents the useful element of red brittleness in the hot rolling.Must add more than 2 times of S in order to bring into play this effect, when S:0.02% is following, must make the following of Mn be limited to 0.05%.On the other hand, in steel solid solution the steel plate of a large amount of Mn, the crystal grain refinement that becomes easily, and promote sclerosis and general extension reduction.In addition, when making Mn by thermal treatment, promote the erosion resistance deterioration in denseization of steel plate top layer, therefore make Mn on be limited to 0.5%.
＜P:0.02mass% is following 〉
Identical with Mn, P also has to be made steel plate sclerosis and makes general extension reduce and make the effect of erosion resistance deterioration.Particularly when P amount surpasses 0.02%, becoming to the segregation of crystal boundary significantly promotes the embrittlement of steel plate, and is difficult to obtain needed general extension value, therefore makes to be limited to 0.02% on it.
＜S:0.02mass% is following 〉
S exists as inclusion, is the harmful element that causes general extension reduction and erosion resistance deterioration, so its amount is few more good more.But it is the element of sneaking into inevitably when refining, if for a small amount of then do not produce problem in the practicality, therefore make and be limited to 0.02% on it.
<Al：0.02mass％～0.10mass％>
Al is the bioelement of the reductor during as melting, is the preferred elements that improves the purity of steel plate.Therefore, addition must enough be used for getting rid of the oxygen in the steel.When Al after a little while, deoxidation is insufficient and inclusion in the steel increases, and can cause equally with cementite and therefore to make the reduction of general extension down and to be limited to 0.02%.On the other hand, when addition for a long time, the Al of the surplus after the deoxidation and the N chemical combination in the steel and become the AlN precipitate reduce the general extension value and produce the surface imperfection that is caused by aluminium elementide (alumina cluster) etc., therefore make and are limited to 0.10%.
<N：0.008mass％～0.015mass％>
Among the present invention, N is most important manufacturing factor, steel plate is worked and brings into play effect of the present invention as solid solution N.This solid solution N is, defined by solid solution N amount=Ntotal-NasAlN, can be used as whole N amounts of containing from steel plate (=(=AlN) value obtains to deduct the N amount of separating out measured by the method for fusion of bromo-ester Ntotal).N is the sosoloid strengthening element better than P, has the advantage that does not make the erosion resistance deterioration as P.And the effect that has is, acts on structure important among the present invention and reduces the average Lankford value of sheet.But, when less than 0.006%, can not expect the effect of solid solution N, (=Ntotal) following is limited to 0.008% therefore to make whole N amounts.On the other hand, when surpassing 0.015%, significantly promote the embrittlement of steel plate and general extension reduces, and the slab crack when being easy to generate continuous casting or by producing the gas hole defect that gas causes.Therefore, make N on be limited to 0.015%, but the stability of the material in considering a series of manufacturing processes, guarantee preferably to be limited to 0.010% on it under the situation of good qualification rate etc.
(other chemical ingredients)
As the composition of EOE of the present invention with the DR steel plate, with mass% need contain C:0.02%～0.06%, below the Si:0.03%, Mn:0.05%～0.5%, below the P:0.02%, below the S:0.02%, Al:0.02%～0.10%, N:0.008%～0.015%, but also can contain known welded tank with the DR steel plate in the general composition element that exists.For example, also can contain following composition element according to the difference of purpose, below the Cr:0.10%, below the Cu:0.20%, below the Ni:0.15%, below the Mo:0.05%, below the B:0.0020%, Ti, Nb, Zr, V etc. are below 0.3% more than a kind or 2 kinds, and perhaps Ca:0.01% is with inferior.
(about creating conditions)
Become the steel disc indefinite of rolled material, but for the macrosegregation that makes composition is an inferior limit, preferably the steel disc that obtains by Continuous casting process.This casts steel disc continuously, not necessarily needs cooling before hot rolling, preferably directly delivers to hot rolling after casting and inserts process furnace.This is the situation for fear of the minimizing of available solid solution N because steel disc cools off.Though do not know detailed mechanism, with steel disc cooling and reheat the time, the low more solid solution N of its temperature becomes few more as can be known.Therefore, when cold steel disc is carried out reheat, the Heating temperature of the process capability upper limit that the situation when preferred use and casting is approaching, and subsistence level carries out reheat under the Heating temperature more than 1200 ℃ in the present invention.
With the steel disc temperature maintenance the Ar3 transformation temperature with on carry out hot rolled and forge eventually calendering.By the calendering more than the transformation temperature, can access the hot rolling microstructure of homogeneous, refinement, and the lattice distortion that suppresses AlN causes separating out, guarantee easily to stablize in the hot rolling stage thus, a large amount of solid solution N.
After forging calendering eventually, carry out reducing separating out of AlN based on the pressure cooling of water-cooled.In the present invention, owing to need guarantee a large amount of solid solution N, therefore carry out forging eventually the cooling after the calendering as far as possible apace, and to make coiling temperature be below 600 ℃ in the hot rolling stage.This be because, the solid solution Al that is not used to deoxidation in steel, from under the Ar3 transformation temperature to surpassing in 600 ℃ the temperature range easily and N chemical combination, and promote AlN to generate and the situation of solid solution N minimizing in order to avoid, on the viewpoint that solid solution N guarantees, extremely preferably pass through this temperature range at short notice.
By pickling the hot-rolled steel sheet that so obtains is descaled, and implement cold rolling.When cold rolling rate less than 80%, in continuous annealing, produce significant grain growth sometimes and average Lankford value surpasses 1.0.Therefore, preferred cold rolling draft is high slightly more than 80%, more preferably 85%～95%.
Recrystallize after cold rolling is handled and is carried out in annealing furnace.When annealing temperature surpasses the Ac1 transformation temperature, produce significant grain growth and the average Lankford value of sheet is more than 1.0, therefore making upper annealing temperature is 700 ℃.On the other hand, when recrystallization temperature was following, cold rolling microstructure was residual and can not guarantee general extension, therefore made down to be limited to more than the recrystallization temperature.
Secondary cold-rolling after the annealing is the of the present invention important manufacturing factor after solid solution N.To containing the continuous annealing steel plate of the present invention of the solid solution N more than 0.006%, implement draft 6%～15%.If under this condition, then can suppress deterioration based on the general extension value of work strengthening, and can guarantee anisotropy that steel plate extends, be that rolling direction is more than 10% and the extension of plate width more than 5%.Though do not know detailed mechanism, the solid solution N in steel is 0.006% when above, may act on the density of the dislocation that produces by calendering and moves and suppress crystal grainization.Be limited to 6% under the best draft, it is former because though the general extension change loses stable calenderability greatly in the calendering that is lower than this value, and can not guarantee application and the Flatness of making the required steel plate of lid continuously.On the other hand, when draft surpassed 15%, the anisotropy of the extension of steel plate increased and promotes the crystal grainization of dislocation and the general extension of plate width becomes less than 5%, so the draft upper limit is necessary for 15%.The steel plate that has passed through above-mentioned operation becomes end article.Therefore though the thickness of slab to end article is not particularly limited, the thick more general extension value of thickness of slab is big more, considers the tank body cost after the system jar and preferably makes and be limited to 0.20mm on it.When thickness of slab deficiency 0.14mm, the processibility of lid and the problem of undercapacity take place easily, therefore preferably make under the practicality to be limited to 0.14mm.As the surface treatment of steel plate, then there is not restriction as long as be applicable to common steel plate for tanks.That is, for zinc-plated, chromium plating, nickel plating and with these plating of making up etc. compoundly.And for application on these electroplating steel plates or the color coated steel sheet pasting organic resin film and make jar, the present invention also can be suitable for no problemly.
(embodiment)
Below, embodiments of the invention and comparative example compared one side describe on one side.Table 1 expression composition, steel plate characteristic and rivet processibility, table 2 expression is created conditions, steel plate characteristic and rivet processibility.The example of the present invention of the steel shown in the table 1 create conditions for, 1211 ℃～1248 ℃ of the Heating temperatures of steel disc, hot rolled is forged 851 ℃～896 ℃ of temperature eventually, 546 ℃～599 ℃ of coiling temperatures, cold rolling rate 88.2%～92.6%, 642 ℃～686 ℃ of continuous annealing temperature, modified calendering rate 6%～15%, the goods thickness of slab is 0.160mm～0.200mm.And the steel of the example shown in the table 2 are, use the identical steel disc manufacturing of the example put down in writing with table 12.Following the trying to achieve of Ar3 transformation temperature of example 2, in calculation formula: among the Ar3=850-660C-120Mn+1770P+400A, composition of steel C:0.041%, Mn:0.28%, P:0.012%, Al:0.059% that substitution is represented with mass%.The Ar3 transformation temperature of example 2 is 834 ℃.Comparative example 23～28 is SR (Single Reduce: single calendering; Hereinafter to be referred as SR) material, other comparative examples and embodiment are the DR steel plates of goods thickness of slab 0.168mm～0.200mm.For these steel plates, as surface treatment the electrolysis chromic acid handle or plating Sn after carry out the chemical conversion treatment reason, then according to the outside mutually face to face with inner face mutually face to face order carry out application, the baking (190 ℃, 10 minutes) of dry film thickness 10 μ m respectively.
In addition, the rivet processibility is to have made the standard-sized sheet mouth EOE of φ 301 (jar of internal diameter 74.1mm) by 2 operations of rivet moulding.Have or not the generation crack with visual the evaluation in the rivet molding procedure, and measure the rivet diameter in the caulking operation of rivet, the result of comprehensive evaluation has been carried out in table 1 and table 2 expression to the rivet processibility.And Fig. 4 is that the relation table with solid solution N and Lankford value is shown graphic representation.
Any one the rivet processibility of example that satisfies condition of the present invention is all good, has confirmed effect of the present invention.In addition, as shown in Figure 4, when the solid solution N that contains in the steel plate becomes 0.006% when above, the average Lankford value of steel plate becomes below 1.0 to acting on structure strongly, when and during with higher DR calendering rate, the reduction of Lankford value becomes greatly.
Table 1
Notes) underscore is partly represented to break away from from invention scope.
Table 2
Notes) underscore is partly represented to break away from from invention scope.
Notes) steel disc of use example 2.
Industry applications
Thin continuous annealing DR steel plate in the past needs above rivet molding procedure of 3 stages, with This is relative, and DR steel plate of the present invention becomes to be grouped into and manufacture method is studied to this steel plate, By rolling direction and the extension of width and the orchid after the Ageing Treatment after the regulation Ageing Treatment Gram Ford value can be carried out the rivet moulding in 2 stages.
As a result, bring into play useful remarkable result on the following industry: use can economize on resources, save The material that make in the energy seedbed does not need to carry out the equipment investment of new wholesale, at the worker of EOE Also can carry out energy-saving in the order.
Claims (2)
1, a kind of DR steel plate is characterized in that,
Contain with mass% as composition of steel,
C：0.02％～0.06％，
Below the Si:0.03%,
Mn：0.05％～0.5％，
Below the P:0.02%,
Below the S:0.02%,
Al：0.02％～0.10％，
N：0.008％～0.015％，
And the amount of the solid solution N in the steel plate that is made of remainder fe and unavoidable impurities (Ntotal-NasAIN) is more than 0.006%,
The general extension value of the rolling direction after the ageing treatment is more than 10%, and the general extension value of the plate width after the ageing treatment is more than 5%, and the average Lankford value after the ageing treatment is below 1.0.
2, a kind of manufacture method of DR steel plate,
This DR steel plate is,
Contain with mass% as composition of steel,
C：0.02％～0.06％，
Below the Si:0.03%,
Mn：0.05％～0.5％，
Below the P:0.02%,
Below the S:0.02%,
Al：0.02％～0.10％，
N：0.008％～0.015％，
And the amount of the solid solution N in the steel plate that is made of remainder fe and unavoidable impurities (Ntotal-NasAIN) is more than 0.006%,
The general extension value of the rolling direction after the ageing treatment is more than 10%, and the general extension value of the plate width after the ageing treatment is more than 5%, and the average Lankford value after the ageing treatment is below 1.0;
The manufacture method of this DR steel plate is characterised in that,
Steel disc is heated to more than 1200 ℃ and to forge temperature the end more than the Ar3 transformation temperature carries out hot rolling;
Become below 600 ℃ at coiling temperature and to batch hot-rolled steel sheet;
After the pickling, implement the calendering rate and be cold rolling more than 80%;
The enforcement recrystallization temperature is above, the annealing of not enough Ac1 transformation temperature;
And, implement the DR calendering of modified calendering rate 6%～15%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP219066/2006 | 2006-08-11 | ||
| JP2006219066 | 2006-08-11 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101454470A true CN101454470A (en) | 2009-06-10 |
Family
ID=39033060
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNA2007800198222A Pending CN101454470A (en) | 2006-08-11 | 2007-08-09 | DR steel sheet and process for manufacturing the same |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US20090250147A1 (en) |
| EP (1) | EP2050834A4 (en) |
| JP (1) | JP5047970B2 (en) |
| KR (1) | KR20090007796A (en) |
| CN (1) | CN101454470A (en) |
| TW (1) | TW200827460A (en) |
| WO (1) | WO2008018531A1 (en) |
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Family Cites Families (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63109121A (en) | 1986-10-28 | 1988-05-13 | Nippon Steel Corp | Production of steel sheet for easy opening can lid |
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-
2007
- 2007-08-07 TW TW096128989A patent/TW200827460A/en unknown
- 2007-08-09 JP JP2008528868A patent/JP5047970B2/en active Active
- 2007-08-09 KR KR1020087030194A patent/KR20090007796A/en not_active Application Discontinuation
- 2007-08-09 US US12/227,505 patent/US20090250147A1/en not_active Abandoned
- 2007-08-09 EP EP07792242A patent/EP2050834A4/en not_active Withdrawn
- 2007-08-09 CN CNA2007800198222A patent/CN101454470A/en active Pending
- 2007-08-09 WO PCT/JP2007/065590 patent/WO2008018531A1/en active Application Filing
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Also Published As
| Publication number | Publication date |
|---|---|
| US20090250147A1 (en) | 2009-10-08 |
| TW200827460A (en) | 2008-07-01 |
| JPWO2008018531A1 (en) | 2010-01-07 |
| EP2050834A1 (en) | 2009-04-22 |
| JP5047970B2 (en) | 2012-10-10 |
| KR20090007796A (en) | 2009-01-20 |
| EP2050834A4 (en) | 2010-09-29 |
| WO2008018531A1 (en) | 2008-02-14 |
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