CN102712974A - Cold-rolled steel plate having excellent post-aging moldability and shape retention - Google Patents

Cold-rolled steel plate having excellent post-aging moldability and shape retention Download PDF

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CN102712974A
CN102712974A CN2011800061156A CN201180006115A CN102712974A CN 102712974 A CN102712974 A CN 102712974A CN 2011800061156 A CN2011800061156 A CN 2011800061156A CN 201180006115 A CN201180006115 A CN 201180006115A CN 102712974 A CN102712974 A CN 102712974A
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cold
timeliness
temperature
rolling
elongation
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CN102712974B (en
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木津太郎
安原英子
花泽和浩
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/34—Pretreatment of metallic surfaces to be electroplated
    • C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
    • 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
    • C21D2211/005—Ferrite

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  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Electroplating Methods And Accessories (AREA)
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Abstract

Provided are a cold-rolled steel plate having excellent post-aging moldability and shape retention, and a method for producing same. The steel plate has a ferrite-phase based structure comprising 0.01 to 0.05% C, no more than 0.05% Si, 0.1 to 0.5% Mn, no more than 0.05% P, no more than 0.02% S, 0.02 to 0.10% Al, no more than 0.005% N, with the remainder being made up of iron and inevitable impurities. The average particle size of said ferrite phase is 10 to 20[mu]m, and the standard deviation sigma A of the natural logarithm of the value obtained by dividing individual ferrite particle sizes by the average value is at least 0.30. In order to obtain the steel plate, when carrying out annealing after cold rolling, heating from 600 DEG C to the range of the holding temperature at an average heating rate of 1 to 30 DEG C/s; holding is carried out at a holding temperature of 800 to 900 DEG C for a holding time of 30 to 200s; cooling from the holding temperature to the range of 550 DEG C is carried out at an average cooling rate of 3 to 30 DEG C/s; after which the steel plate is maintained at a temperature of 500 to 300 DEG C for at least 30s, and strain is applied to give an elongation of 0.5 to 2.0% at room temperature.

Description

Cold-rolled steel sheet that plasticity after the timeliness and shape freezing property are good and method of manufacture thereof
Technical field
The present invention relates to plasticity and good cold-rolled steel sheet and the method for manufacture thereof of shape freezing property after the timeliness, said cold-rolled steel sheet is suitable as the member that backlight chassis of large-scale LCD TV etc. is processed the parts of large flat shape most.
Background technology
In slim liquid crystal TV and OA equipment etc., how uses through with bending, expansion forming the flat-shaped part that processes shape as main body.And, when manufacturing is used for the member (tole) of these parts,, in temper rolling, carries out elongation and be about several percentile saddening systems for the shape or the elimination elongation at yield point of rectification plate.But, behind the temper rolling,, can cause that elongation at yield point takes place once more or ductility reduction etc. is called as the deterioration in characteristics of so-called strain aging along with time lapse.Particularly in recent years, in order to reduce cost, output coiled material and the situation of carrying out punch process abroad becomes very many needs spended time owing to be fabricated onto punch process from coiled material, therefore can not avoid strain aging.In addition,, in the process of circulation of coiled material, also need spended time, perhaps under situation about coiled material being held as the stock etc., also can cause steel plate generation strain aging even at home.Like this, when causing the deterioration in characteristics of steel plate in that strain aging takes place, need liquidate press strip spare and mould etc. are adjusted again, thereby become the one of the main reasons that cost increases.
And recently, for cutting down cost, the usage quantity of steel plate is cut down the thickness of slab attenuate of member in strong request.During with the thickness of slab attenuate, be easy to generate following problem: add the shape freezing property variation in man-hour, perhaps be easy to generate man-hour such as crackle etc. adding.And then; Reduce in order to remedy the parts inflexible of following thin-walled property and coming; Sometimes also change component shape, for example append stiffening web or make it with the closed section structure proximate etc., thereby make the processing conditions more and more harshness that becomes through bending machining etc.; As a result, crackle and the shape defect during punching press becomes serious.Particularly, when bending machining, produce the shape defect that is called the crest line warpage, thus problems such as production part warpage.In addition, add man-hour at bulging, produce following problem: the bulging height cracks when big, produces fold etc. when perhaps pressure-pad-force is weak.
For such crest line warpage, it is favourable reducing the r value.But, reduces the r value and can cause elongation to reduce, thereby processing produces detrimental action to bulging.And then, if owing to strain aging causes that elongation at yield point takes place once more or ductility reduces, then can not deal with crackle and fold etc. through changing punching press condition etc.
The known strained timeliness causes by the C, the N that are solid-solubilized in the steel plate, and carbonitride generting element such as known interpolation Ti, Nb and be the steel plate that is difficult for causing strain aging with the IF steel of the form fix of precipitate with this C, N.But the manufacturing cost of existing IF steel is high, and r value height, thereby is disadvantageous for the situation that comprises bending forming.
Based on above situation, being contemplated to be of the member (tole) of and elongation at yield point little and elongation high cheapness low for r value after the timeliness is very large.
The steel plate low as the r value and shape freezing property is good for example discloses in the patent documentation 1 like lower steel plate: in the finish to gauge in hot rolling, make Ar 3～(Ar 3+ 100) rolling rate is more than 25% and makes the frictional coefficient when rolling is at Ar under the condition below 0.2 3More than finish finish to gauge, perhaps, make Ar 3Below rolling rate be more than 25% and to make the frictional coefficient when rolling be to carry out finish to gauge under the condition below 0.2, control texture thus, and to make in the r value of rolling direction or rolling right angle orientation at least one be below 0.7.
Disclose in the patent documentation 2 that parallel with the plate face { the 100} face is with { ratio of 111} face is that the good automobile of shape freezing property more than 1.0 is used the ferritic series tole.
In the patent documentation 3; In order to obtain the good ferritic series tole of shape freezing property; Following scheme is disclosed: control 100}＜011＞~ intensity of 223}＜110＞orientation group and 112}＜110＞, 554}＜225＞, 111}＜112＞, intensity of 111}＜110＞each orientation, and make rolling direction r value and and the r value of the rectangular direction of rolling direction at least one be below 0.7.
The prior art document
Patent documentation
Patent documentation 1: No. 3532138 communique of Japanese Patent
Patent documentation 2: TOHKEMY 2008-255491 communique
Patent documentation 3: TOHKEMY 2003-55739 communique
Summary of the invention
Invent problem to be solved
Yet the steel plate of record produces problems such as punching press crackle in the reduction of timeliness post-treatment property in the patent documentation 1 ~ 3.
In view of the foregoing, the object of the present invention is to provide plasticity and good cold-rolled steel sheet and the method for manufacture thereof of shape freezing property after the timeliness.
The method that is used to deal with problems
In order to address the above problem, the contriver has carried out deep research repeatedly.
The result finds; Through the average r value that makes rolling direction, rolling 45 ° of directions, rolling right angle orientation be below 1.2, make elongation after the timeliness be more than 40% and make timeliness after elongation at yield point be below 1.0%, even can access at timeliness postforming property and the also good cold-rolled steel sheet of shape freezing property.Need to prove, at this, average r value (r m) be made as r respectively in r value with rolling direction, rolling 45 ° of directions, rolling right angle orientation L, r D, r CThe time, r m=(r L+ 2r D+ r C)/4.
In addition, think can guarantee plasticity and shape freezing property after the timeliness through the present invention mechanism as follows.Usually, in order to eliminate elongation at yield point, adopt the method that mobile dislocation is introduced in strain that at room temperature applies.But, under the few situation of dependent variable, fixed by C, N owing to timeliness makes mobile dislocation, thereby cause that elongation at yield point takes place once more.On the other hand, if increase the dependent variable under the room temperature, then yield-point increases and the elongation reduction, so plasticity reduces.Therefore, in the present invention, be conceived to the distribution of ferritic particle diameter.Through increasing the distribution of ferritic particle diameter, even dependent variable is few, it is inhomogeneous and make strain concentrating also can to make strained introduce the position.As a result, even after timeliness, also can suppress the generation of elongation at yield point.In addition, for few crystal grain was introduced in strain, the sclerosis that is caused by timeliness was also few, therefore also can suppress elongation and reduce.And the inhomogeneous introducing of such strained can realize through the standard deviation that increases the ferritic size distribution.
In addition; Aforesaid r value is that the elongation below 1.2, after the timeliness is more than 40% and the elongation at yield point after the timeliness is that cold-rolled steel sheet below 1.0% can obtain as follows: in hot rolling; Finishing finish to gauge at ferrite area also batches at low temperatures; Thus at hot rolling stage non-recrystallization, in annealing, through controlling the dependent variable after thermal history is controlled ferritic particle diameter and size distribution and controlled chilling.
The present invention is based on above opinion and accomplish, its purport is following.
[1] plasticity after a kind of timeliness and the good cold-rolled steel sheet of shape freezing property; It is characterized in that; Have following composition: in quality %, below C:0.01 ~ 0.05%, Si:0.05%, Mn:0.1 ~ 0.5%, below the P:0.05%, below the S:0.02%, Al:0.02 ~ 0.10%, below the N:0.005%, surplus is iron and unavoidable impurities; And have with the ferritic phase is the tissue of main body; And the median size of this ferritic phase is 10 ~ 20 μ m, is made as σ at the standard deviation of the natural logarithm of the value that each ferritic particle diameter is obtained divided by MV AThe time, σ A>=0.30.
[2] like plasticity after above-mentioned [1] described timeliness and the good cold-rolled steel sheet of shape freezing property, it is characterized in that, also contain more than in Ti:0.005 ~ 0.02%, B:0.0003 ~ 0.0030% any one in quality %.
Like plasticity after above-mentioned [1] or [2] described timeliness and the good cold-rolled steel sheet of shape freezing property, it is characterized in that [3] having zinc at surface of steel plate is coating.
The method of manufacture of the cold-rolled steel sheet that [4] plasticity after a kind of timeliness and shape freezing property are good is characterized in that, is (Ar with the steel billet of above-mentioned [1] or above-mentioned [2] said composition in the final outlet side temperature of finish to gauge 3-100 ℃) ~ Ar 3℃, coiling temperature is lower than under 550 ℃ the condition and carries out hot rolling; Then carry out pickling, carry out with 40 ~ 80% rolling rate cold rolling, then; When annealing; Heating in the average rate of heating with 1 ~ 30 ℃/second in 600 ℃ of TRs till the soaking temperature, is that 800 ~ 900 ℃, soaking time are to carry out equal thermal treatment under 30 ~ 200 seconds the condition in said soaking temperature, and the average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from said soaking temperature cools off; Keep down more than 30 seconds at 500 ~ 300 ℃, at room temperature apply elongation and be 0.5 ~ 2.0% strain.
[5] like the method for manufacture of the good cold-rolled steel sheet of the plasticity after above-mentioned [4] described timeliness and shape freezing property; It is characterized in that; After the said equal thermal treatment; Average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from said soaking temperature cools off, and continues to be cooled in the TR below 500 ℃, and then is heated to 500 ~ 550 ℃ TR; Keep down more than 30 seconds at 500 ~ 300 ℃ afterwards, at room temperature apply elongation and be 0.5 ~ 2.0% strain.
Need to prove that in this manual, the % of the composition of expression steel all is quality %.In addition, also comprise as the cold-rolled steel sheet of object of the present invention cold-rolled steel sheet is implemented zinc-plated processing (for example electro-galvanizing is handled, pot galvanize is handled, alloyed zinc hot dip galvanized processing) and the steel plate that obtains.And, also comprise the steel plate that has tunicle through chemical conversion processing etc.
In addition, steel plate of the present invention panel, air-conditioner outdoor unit etc. that can be widely used in backlight chassis, the refrigerator of large-scale TV have planar portions and have implemented the general member of the household electrical appliances purposes of bending, bulging, slight deep-draw processing etc.And then, if use the present invention, for example then can utilize thickness of slab to make the backlight chassis more than about 650mm * about 500mm (32V type) for the steel plate of 0.8mm.
The invention effect
According to the present invention, can access plasticity and the good cold-rolled steel sheet of shape freezing property after the timeliness.Thus, the desired writing board shape of large component can be guaranteed, thereby the members such as backlight chassis of large-scale LCD TV can be made.
Description of drawings
Fig. 1 is expression σ AGive the figure of the influence that elongation at yield rate (YP-El) and elongation (El) after the timeliness bring.
Fig. 2 is expression (final outlet side temperature (the FT)-Ar of finish to gauge 3) to σ AThe figure of the influence that brings.
Fig. 3 is that expression coiling temperature (CT) is given σ AThe figure of the influence that brings.
Embodiment
Chemical ingredients to steel plate of the present invention describes.Need to prove that in following explanation, the content % of composition element all representes quality %.
C：0.01~0.05%
C forms cementite and reduces solid solution C, thereby can reduce ys.C after a little while, the generation of cementite is suppressed, solid solution C increases, thus; Age hardening takes place easily, and in hot rolling, in the finish to gauge frame when austenite phase transformation is ferritic; The two-phase region is less, so resistance to deformation sharply reduces, and rollingly becomes unstable thereby make.Therefore, need make C is more than 0.01%.On the other hand, when C increased, grain growing was suppressed and grain refined, therefore, and steel plate hardization and elongation is reduced.Therefore, need make C is below 0.05%.
Below the Si:0.05%
During the Si heavy addition,, generate the Si oxide compound during perhaps owing to annealing plating property is suppressed owing to hardization makes the plasticity variation.Therefore, need make Si is below 0.05%.
Mn：0.1~0.5%
Mn makes that deleterious S forms MnS and makes it innoxious in the steel, and therefore need make Mn is more than 0.1%.On the other hand, a large amount of Mn can be owing to solution strengthening makes the plasticity variation with the caused hardization of low temperature phase change generation mutually.In addition, Mn reduces transformation temperature, and rolling being difficult at ferrite area carried out.And then, when annealing, suppress ferritic recrystallize, make thus and organize grain refined.Therefore, Mn below 0.5%, is preferably below 0.3%.
Below the P:0.05%
P makes ductility and toughness variation at grain boundary segregation, and therefore, need make P is below 0.05%.Be preferably below 0.03%.
Below the S:0.02%
Ductility when S makes hot rolling significantly reduces, and brings out hot tearing thus and makes the remarkable variation of surface texture.And then S does not only almost have help to improving intensity, and forms thick MnS as impurity element, and ductility is reduced.These problems surpass at 0.02% o'clock in the S amount and become significantly, thereby preferably reduce as much as possible.Therefore, need make the S amount is below 0.02%.
Al：0.02~0.10%
Al makes N form nitride and is fixed, and can suppress the age hardening that produces because of solid solution N thus.In order to obtain such effect, need make Al is more than 0.02%.On the other hand, a large amount of Al adds not only to be made the intensity rising and plasticity is reduced, but also is accompanied by the rising of cost.Therefore, need make Al is below 0.10%.
Below the N:0.005%
N contains sometimes in a large number, in hot rolling, might follow crackle of steel billet and produces surface imperfection.In addition, when existing with the form of solid solution N, can cause age hardening in cold rolling, annealing back.Therefore, need make N is below 0.005%.
On the basis of above-mentioned element, in the present invention,, can contain among Ti, the B more than one in the scope of Ti:0.005 ~ 0.02%, B:0.0003 ~ 0.0030% in order to improve ageing and shape freezing property.
Ti：0.005~0.02%
Ti at high temperature combines with N to form nitride and solid solution N is reduced, and can improve ageing thus.In order to obtain such effect, need make Ti is more than 0.005%.On the other hand, the content of Ti further combines with C and generates carbide and carbonitride for a long time, and therefore, intensity raises and plasticity is reduced.Therefore, when containing Ti, be more than 0.005% and below 0.02%.
B：0.0003~0.0030%
B at high temperature combines with N to form nitride and solid solution N is reduced, and can improve ageing thus.And then, suppress ferritic grain growing in the annealing process of B after cold rolling, and control r value, shape freezing property can be improved thus.In order to obtain such effect, need make B is more than 0.0003%.On the other hand, when B existed in a large number, therefore ferritic recrystallize in the time of can suppressing to anneal made and organizes grain refined.Therefore, when containing B, be more than 0.0003% and below 0.0030%.
Composition beyond above-mentioned is made up of iron and unavoidable impurities.As unavoidable impurities, for example can enumerate: the Cu below 0.05%, the Cr that sneak into easily, and the Sn below 0.01% in addition, Mo, W, V, Nb, Ni etc. from waste material.
The tissue of steel plate of the present invention is main body with the ferritic phase.In addition, the median size of ferritic phase is 10 ~ 20 μ m.And then, be made as σ at the standard deviation of the natural logarithm of the value that each ferritic particle diameter is obtained divided by MV AThe time, σ A>=0.30.
In order to ensure plasticity, be the main body with soft ferritic phase.Alleged here " is main body with the ferritic phase " is meant that ferritic phase counts the situation more than 95% with respect to the ratio of whole tissues with area occupation ratio.Through being main body with the ferritic structure, the elongation after the timeliness is reached more than 40%.Ferritic structure is 100% o'clock, and elongation improves, and is therefore preferred.Beyond the principal phase second is that cementite phase, perlite equate mutually, can contain in the scope of counting below 5% with area occupation ratio.If increase to surpassing 5%, then ductility significantly reduces.Need to prove that the area occupation ratio of ferritic phase can be through utilizing structure observation with ferritic phase and distinguishing out mutually and carry out picture processing and obtain in addition.
In order to ensure plasticity, making median size is more than the 10 μ m.On the other hand, when particle diameter became big, except when being shaped, producing orange peel etc. the bad order, size distribution also diminished, therefore, make median size on be limited to 20 μ m.Need to prove that median size is measured through shearing method and calculated through 2/ [(1/Ll)+(1/Lc)] by average slice length Ll, the Lc of rolling direction and thickness of slab direction.
Among the present invention, through increasing the distribution of ferritic particle diameter, even dependent variable is few, it is inhomogeneous and make strain concentrating also can to make strained introduce the position, thereby even after timeliness, also can suppress the generation of elongation at yield point.In addition, for few crystal grain was introduced in strain, the sclerosis that is caused by timeliness was also few, therefore also can suppress elongation and reduce.Therefore, the standard deviation in the natural logarithm of the value that each ferritic particle diameter is obtained divided by MV is made as σ AThe time, need be σ A>=0.30.Below, describe for this point.
Use if consider actual steel plate, then think as the time of prescription room temperature (20 ℃) under be 6 months promptly enough.Fig. 1 is expression σ AThe figure of the influence that elongation at yield rate (YP-El) when carrying out 6 months timeliness under giving 20 ℃ and elongation (El) bring.In addition; Fig. 1 measures and obtains through using following various steel plates and these steel plates being processed into JIS5 tension test sheet; Said steel plate has below following composition: C:0.01 ~ 0.05%, Si:0.05%, Mn:0.1 ~ 0.5%, below the P:0.05%, below the S:0.02%, Al:0.02 ~ 0.10%, below the N:0.005%, surplus is iron and unavoidable impurities, and; The ratio of ferritic phase is counted more than 95% with area occupation ratio, and the median size of ferritic phase is 10 ~ 20 μ m.At this, be below 1.0% through making the elongation at yield rate after the timeliness, can eliminate the fold after the shaping or be suppressed to almost can't be through the visual level of distinguishing.In addition, be more than 40% through making the elongation after the timeliness, can be under situation about not cracking wall angle during with expansion forming be configured as about 45 °, thereby can tackle most drawing.As shown in Figure 1, through making σ ABe more than 0.30, the elongation at yield rate is reduced to below 1.0%, and elongation is increased to more than 40%.Therefore, make σ ABe more than 0.30.
Then, creating conditions of steel plate of the present invention described.The steel billet that in the present invention, will have an above-mentioned composition is (Ar in the final outlet side temperature of finish to gauge 3-100 ℃) ~ Ar 3℃, coiling temperature is lower than under 550 ℃ the condition and carries out hot rolling; Then carry out pickling, carry out with 40 ~ 80% rolling rate cold rolling, then; When annealing; Heating in the average rate of heating with 1 ~ 30 ℃/second in 600 ℃ of TRs till the soaking temperature, is that 800 ~ 900 ℃, soaking time are to carry out equal thermal treatment under 30 ~ 200 seconds the condition in soaking temperature, and the average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from said soaking temperature cools off; Keep more than 30 seconds down at 500 ~ 300 ℃; At room temperature apply 0.5 ~ 2.0% strain, can increase the distribution of ferritic particle diameter thus, thereby can access the low-yield intensity after the timeliness, low r value and good elongation.
Finish to gauge end temp: (Ar 3-100 ℃) ~ Ar 3
Through finishing the finish to gauge in the hot rolling, in ferritic structure, accumulate strain, and recover to carry out unevenly according to crystalline orientation at ferrite area.As a result, strained is accumulated and is become inhomogeneous, can increase the ferritic size distribution after the annealing.In addition, by the inhomogeneous flourishing randomization that makes texture of crystalline orientation generation, thereby can reduce the r value and raising shape freezing property.Therefore, need make the outlet temperature of finish to gauge is Ar 3Below.More preferably be lower than Ar 3Temperature.At Ar 3Amount of rolling when following does not have special stipulation, is preferably more than 10%, more preferably more than 20%.On the other hand, when the finish to gauge end temp reduces, introduced the strained crystalline and recovered not carry out, strain is accumulated and can not be become inhomogeneous.And then because rolling load becomes big, therefore operational difficulty is followed.Therefore, need make the finish to gauge end temp is (Ar 3-100 ℃) more than.
Need to prove Ar 3Can obtain through following formula.
Mn content＜0.4% o'clock: Ar 3=880-1000 * C content (%)
Mn content>=0.4% o'clock: Ar 3=870-1000 * C content (%)
Coiling temperature: be lower than 550 ℃
When the coiling temperature after the finish to gauge is high, can make the ferritic recrystallize, thereby can not introduce uneven strain, therefore, need make coiling temperature for being lower than 550 ℃.The lower limit of coiling temperature does not have special stipulation, but temperature crosses when low, and therefore the scroll variation of coiled material is preferably more than 300 ℃.Finishing the speed of cooling of beginning till batch from finish to gauge does not have special stipulation, is preferably more than 10 ℃/second, more preferably more than 30 ℃/second, further is preferably more than 100 ℃/second.
Rolling rate when cold rolling: 40 ~ 80%
With the rolling rate in cold rolling after the hot-rolled sheet pickling when big, strained is introduced and is become evenly, and the ferritic size distribution after the annealing reduces, and through increase the grain refined that causes in response to variable high strength, thereby plasticity is reduced.In addition, texture is also flourishing, therefore makes the r value become big and reduction shape freezing property.Therefore, need make rolling rate is below 80%.On the other hand, rolling rate hour, because the dependent variable of introducing is few, therefore, the recrystallize during annealing is suppressed and forms recovery organization, and plasticity is reduced.Therefore, need make rolling rate is more than 40%.
Average rate of heating in 600 ℃ of TRs till the soaking temperature: 1 ~ 30 ℃/second
Carry out cold rolling after, anneal.In the present invention, control the dependent variable behind ferritic particle diameter and size distribution and the controlled chilling through the thermal history in the control annealing.Creating conditions when therefore, annealing is important condition.
Since 600 ℃ of average rate of heating till the soaking temperature hour, recover to carry out, recrystallize is suppressed.Therefore, need make average rate of heating is more than 1 ℃/second.On the other hand, when average rate of heating was big, the nucleation of the recrystallize in the heat-processed was suppressed, thus when soaking nucleation together, therefore, make the crystal grain grain refined.Therefore, need make average rate of heating is below 30 ℃/second.
Soaking temperature: 800 ~ 900 ℃, soaking time: 30 ~ 200 seconds
In the equal thermal treatment after heating, need when recrystallize is finished, increase particle diameter and plasticity is improved.Therefore, need make soaking temperature is more than 800 ℃.On the other hand, when soaking temperature is too high, carry out from ferritic to austenitic phase transformation, thus, particle diameter diminishes in cooled reverse transformation.Therefore, need make soaking temperature is below 900 ℃.
In addition, soaking time can't be accomplished recrystallize in short-term, even perhaps accomplish, time of grain growing is also short, therefore, grain refined takes place and plasticity is reduced.Therefore, the soaking time in the time of need making heating is more than 30 seconds.On the other hand, when soaking time was elongated, the growth when corroding little crystal grain of big crystal grain became big, and therefore, the distribution of ferritic particle diameter diminishes and particle diameter becomes big, thus, when drawing, produces bad orders such as orange peel.Therefore, need make soaking time is below 200 seconds.
Begin the average cooling rate in the TR till 550 ℃ from soaking temperature: 3 ~ 30 ℃/second
Equal speed of cooling after the thermal treatment hour, the growth of ferritic grain is promoted that the growth when corroding little crystal grain of big crystal grain becomes big, therefore, the distribution of ferritic particle diameter diminishes and particle diameter becomes big, thus, when drawing, produces bad orders such as orange peel.Therefore, need make the average cooling rate that begins in the TR till 550 ℃ from soaking temperature is more than 3 ℃/second.On the other hand, when speed of cooling was excessive, intensity uprised and plasticity is reduced, and therefore, need make average cooling rate is below 30 ℃/second.
Need to prove, above-mentioned begin the cooling till 550 ℃ from soaking after, during under 500 ~ 300 ℃ temperature, keeping in, as long as cooperate producing apparatus suitably to cool off.Preferably after the cooling begin from soaking temperature till, continue to cool off, promptly cool off with 3 ~ 30 ℃/second speed with identical speed of cooling scope to 550 ℃.
Hold-time under 500 ~ 300 ℃: more than 30 seconds
Solid solution C separates out with the form of cementite, can improve ageing thus.Therefore, need in separating out 300 ~ 500 ℃ TR of cementite easily, keep more than 30 seconds.The upper limit of time does not have special stipulation, but owing to keep for a long time reducing production efficiency, therefore, preferably makes the upper limit of hold-time be about 300 seconds.
Need to prove, keeping postcooling to room temperature, but above-mentioned cooling conditions does not need special stipulation, as long as cooperate producing apparatus suitably.
Strain under the room temperature applies, elongation: 0.5 ~ 2.0%
After the annealing, at room temperature apply strain, can eliminate yield-point thus.Therefore, the strain that applies under the room temperature is counted more than 0.5% with elongation.On the other hand, when elongation became big, therefore rise of yield point and plasticity is reduced, need be below 2.0%.Be preferably below 1.5%.Need to prove that strained applies and can also can carry out through stretching through rolling the carrying out that utilizes roll under the room temperature, perhaps, also can be through roll is combined to carry out with stretching.In addition, in rolling, can be lubricated, also can not be lubricated.
When embodiment of the present invention, melting method can suitably use common converter process, electric furnace process etc.After steel after the melting is cast as steel billet, directly implements hot rolling or implement hot rolling in cooling, heating back.In hot rolling, after carrying out finish to gauge under the above-mentioned finish to gauge condition, under above-mentioned coiling temperature, batch.Then, carry out common pickling after, implement above-mentioned cold rolling.For the anneal after cold rolling, under above-mentioned condition, heat, keep, cool off.Can under about 480 ℃, carry out plating as required through pot galvanize.In addition, can also be more than reheat to 500 behind the plating ℃ and make coating alloying.Need to prove that when carrying out reheat, need make temperature is below 550 ℃, so that ferritic crystal grain is not grown.In addition, about 500 ~ 300 ℃ above-mentioned maintenance, owing to might make the cementite dissolving more than the reheat to 500 ℃, therefore, in the time of more than reheat to 500 ℃ and below 550 ℃, preferably making 500 ~ 300 ℃ hold-time behind the reheat is more than 30 seconds.Need to prove that the lower limit of plating bath temperature is about 460 ℃.That is, carry out under the situation of Alloying Treatment in the laggard capable pot galvanize of above-mentioned equal thermal treatment step of going forward side by side, as thermal history, as long as as follows.After the above-mentioned equal thermal treatment; Average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from above-mentioned soaking temperature cools off; And continue to be cooled to and carry out pot galvanize in the TR below 500 ℃; Then the TR of reheat to 500 ~ 550 ℃ and implement Alloying Treatment keeps more than 30 seconds down at 500 ~ 300 ℃ then.As the hold-time,, preferably make it be about 300 seconds based on reason same as described above.Need to prove, keep the back as long as suitable cool to room temperature.And then, carry out temper rolling with about elongation of 0.5% ~ about 2.0%.Preferred elongation is 0.5 ~ 1.5%.In addition, in annealing process, do not implement under the situation of plating,, can carry out electro-galvanizing etc. in order to improve erosion resistance.And then, can also on cold-rolled steel sheet or coated steel sheet, give tunicle through chemical conversion processing etc.
As above can obtain plasticity and the good cold-rolled steel sheet of shape freezing property after the timeliness.And, the cold-rolled steel sheet that as above obtains, the average r value of rolling direction, rolling 45 ° of directions, rolling right angle orientation is below 1.2, and the elongation after the timeliness is more than 40%, and the elongation at yield point after the timeliness is below 1.0%.Need to prove that these characteristics are average r value, elongation, the elongation at yield points after carrying out 6 months ageing treatment under 20 ℃.
The warpage that produces behind r value and the bending forming has dependency.In bending forming, the r value of bending direction uprises, and thus, obviously produces saddle type warpage along wiggle.Therefore, in order to improve the shape freezing property after the drawing through low r value, making average r value in the present invention is below 1.2.
Elongation and plasticity have good dependency, and elongation is big more, for example, can expansion forming to high more.Therefore, needed elongation is the bigger the better, and is more than 40% through making the elongation after the timeliness, can carry out the processing of deep-draw processing and bulging, thereby can guarantee the desired shape of parts.
On above-mentioned basis, making the elongation at yield point after the timeliness of steel plate of the present invention is below 1.0%.Through reducing the elongation at yield point after steel plate has just been made back and timeliness, the tension strain after can suppressing to be shaped, thereby the good molding of manufacturing appearance.
Embodiment 1
After will having the steel billet melting of the chemical constitution shown in the table 1; Carry out reheat; Under the final outlet side temperature (FT) shown in the table 1, carry out hot rolling, cool off, under the coiling temperature shown in the table 1 (CT), batch processing then with 10 ℃/second average cooling rates.Then, carry out pickling, carry out cold rollingly with the rolling rate shown in the table 1, under the condition shown in the table 1, anneal.Then, at room temperature be rolled, make and supply the examination material with the elongation shown in the table 1.
Need to prove, in table 1, will be made as HR, soaking temperature is made as AT, soaking time is made as Ht since 600 ℃ of average rate of heating till the soaking temperature 1, will be made as CR from the average cooling rate that soaking temperature begins till 550 ℃, will be made as Ht from 500 ℃ to 300 ℃ residence time 2In addition, supply to carry out plating through pot galvanize under halfway 480 ℃ of examination material No.4 and handle, make the surface form hot galvanized layer (GI).Supply under halfway 480 ℃ of examination material No.3 to carry out behind the plating reheat to 540 ℃, make the surface form alloyed zinc hot dip galvanized layer (GA) through pot galvanize.Supply examination material No.2 to carry out electroplating processes, make the surface form electrolytic coating (EG).Need to prove, except supplying examination material No4, continue to cool off till since 550 ℃ to 500 ℃ with the speed of cooling identical with the CR shown in the table 1.
The confession that as above obtains being tried the tissue and the mechanical characteristics of material investigates.For tissue, utilize the thickness of slab cross section of observation by light microscope rolling direction, obtain the median size and the size distribution of tissue through shearing method.As a result, in the present embodiment, all ferritic phase is more than 99% in the tissue of confession examination material.In addition; From supplying the examination material to downcut with the JIS5 tension test sheet of rolling direction as draw direction; Under 20 ℃, carry out 6 months ageing treatment, carry out tension test with 10mm/ minute draw speed then, measure elongation at yield point (YP-El) and percentage of total elongation (El).In addition, for the r value, downcut JIS5 tension test sheet, measure with 15% prestrain, by the r value (r of rolling direction from all directions of the rolling direction that supplies the examination material, rolling 45 ° of directions, rolling right angle orientation L), the r value (r of rolling 45 ° of directions d), rolling right angle orientation is the r value (r of C direction C) pass through r m=(r L+ 2r D+ r CAverage r value (r is obtained in)/4 m).Resulting result is shown in Table 1 with becoming to be grouped into and create conditions in the lump.
Figure BDA00001885788100161
Can know according to table 1, the steel plate (invention steel) that has composition of the present invention and make through method of manufacture of the present invention, its ferritic median size is in the scope of 10 ~ 20 μ m, and standard deviation (σ A) be more than 0.30.As a result, the average r value that obtains rolling direction, rolling 45 ° of directions, rolling right angle orientation is that the elongation at yield point below 1.2, after the timeliness is below 1.0% and the elongation after the timeliness (Elm) is plasticity and the good cold-rolled steel sheet of shape freezing property after the timeliness more than 40%.
Relative therewith, method of manufacture is at extraneous steel plate of the present invention (comparative steel), its ferritic median size or standard deviation (σ A) outside scope, elongation at yield point and the elongation after the timeliness (El) after average r value, the timeliness are all relatively poor.
Among Fig. 2, show (FT-Ar 3) try the σ of material No.1 ~ 8 for confession AThe influence that brings among Fig. 3, shows CT and gives the σ that supplies examination material No.1 ~ 4,9 AThe influence that brings.
Can know by Fig. 2, be (Ar through making final outlet side temperature (FT) 3-100 ℃) ~ Ar 3, can make standard deviation (σ A) be more than 0.30.
Can know by Fig. 3, be lower than 550 ℃, can make standard deviation (σ through making coiling temperature (CT) A) be more than 0.30.

Claims (5)

1. plasticity and the good cold-rolled steel sheet of shape freezing property after the timeliness is characterized in that,
Have following composition: in quality %, below C:0.01 ~ 0.05%, Si:0.05%, Mn:0.1 ~ 0.5%, below the P:0.05%, below the S:0.02%, Al:0.02 ~ 0.10%, below the N:0.005%, surplus is iron and unavoidable impurities,
And having with the ferritic phase is the tissue of main body, and the median size of this ferritic phase is 10 ~ 20 μ m, is made as σ at the standard deviation of the natural logarithm of the value that each ferritic particle diameter is obtained divided by MV AThe time, σ A>=0.30.
2. plasticity after the timeliness as claimed in claim 1 and the good cold-rolled steel sheet of shape freezing property is characterized in that, also contain more than in Ti:0.005 ~ 0.02%, B:0.0003 ~ 0.0030% any one in quality %.
3. plasticity and the good cold-rolled steel sheet of shape freezing property after according to claim 1 or claim 2 the timeliness is characterized in that having zinc at surface of steel plate is coating.
4. the method for manufacture of the cold-rolled steel sheet that plasticity after the timeliness and shape freezing property are good is characterized in that, is (Ar with the steel billet of claim 1 or the said composition of claim 2 in the final outlet side temperature of finish to gauge 3-100 ℃) ~ Ar 3℃, coiling temperature is lower than under 550 ℃ the condition and carries out hot rolling; Then carry out pickling, carry out with 40 ~ 80% rolling rate cold rolling, then; When annealing; Heating in the average rate of heating with 1 ~ 30 ℃/second in 600 ℃ of TRs till the soaking temperature, is that 800 ~ 900 ℃, soaking time are to carry out equal thermal treatment under 30 ~ 200 seconds the condition in said soaking temperature, and the average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from said soaking temperature cools off; Keep down more than 30 seconds at 500 ~ 300 ℃, at room temperature apply elongation and be 0.5 ~ 2.0% strain.
5. the method for manufacture of the cold-rolled steel sheet that plasticity after the timeliness as claimed in claim 4 and shape freezing property are good; It is characterized in that; After the said equal thermal treatment; Average cooling rate with 3 ~ 30 ℃/second in the TR till beginning to 550 ℃ from said soaking temperature cools off, and continues to be cooled in the TR below 500 ℃, and then is heated to 500 ~ 550 ℃ TR; Keep down more than 30 seconds at 500 ~ 300 ℃ afterwards, at room temperature apply elongation and be 0.5 ~ 2.0% strain.
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