CN101243198A - Steel sheet for galvanizing with excellent workability, and method for manufacturing the same - Google Patents

Steel sheet for galvanizing with excellent workability, and method for manufacturing the same Download PDF

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CN101243198A
CN101243198A CNA2006800305520A CN200680030552A CN101243198A CN 101243198 A CN101243198 A CN 101243198A CN A2006800305520 A CNA2006800305520 A CN A2006800305520A CN 200680030552 A CN200680030552 A CN 200680030552A CN 101243198 A CN101243198 A CN 101243198A
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steel plate
steel
surface groups
rolling
annealing
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CN101243198B (en
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孙一领
陈光根
康熙宰
金成一
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Posco Holdings Inc
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Posco Co Ltd
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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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • 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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  • Heat Treatment Of Sheet Steel (AREA)

Abstract

A high strength ductile steel sheet for extra deep drawing mainly used for interior or exterior plates of automobile bodies, and a method for manufacturing the same are disclosed. The steel sheet comprises, by weight%, C: 0.010% or less, Si: 0.1%or less, Mn: 0.06-1.5%, P: 0.15% or less, S: 0.020%or less, Sol. Al: 0.10-0.40%, N: 0.010% or less, Ti: 0.003-0.010%, Nb: 0.003-0.040%, B: 0.0002-0.0020%, Mo: 0.05% or less, one or both of Sb: 0.005-0.05% and Sn: 0.005-0.05%, a total amount of Sb and Sn being in the range of 0.005-0.1% when both of Sb and Sn are added to the steel sheet, and the balance of Fe and other unavoidable impurities. The steel sheet has surface agglomerates having an average diameter of 1 D or less, and a tensile strength of 28-50 Df/D.

Description

Be used for galvanized steel plate and manufacture method thereof with excellent workability
Technical field
The present invention relates generally to the interior steel plate that is used for car body etc. or the high strength steel plate and the manufacture method thereof that are used for profound punching press (extradeep drawing) of outer steel plate.More particularly, the present invention relates to a kind of galvanized steel plate and manufacture method thereof that be used for excellent workability, the tensile strength of this steel plate is 28-50 f/, and it has the fatigue property and the surface quality of excellent formability, secondary processing brittleness resistance, welding node.
Background technology
Recent years, along with the shape of car body assembly becomes increasingly complex and is integrated into single component, the steel plate that also requires to be used for car body has the formability of further raising.In addition, also require the steel plate of car body under the working conditions of automobile, to have the excellent secondary processing brittleness and the fatigue property of welding node, and have attracting plate surface.
Usually, by being added to, Si, Mn, Ti, Al etc. produce the formability with raising and the steel plate of intensity in the highly purified steel (in the steel content of impurity reduce to minimum).
After the rolled sheet material of heat is cold rolling, anneal 700 ℃ or higher temperature, so that the structure recrystallization of work hardening.But because the element of most of above-mentioned adding is higher than avidity to Fe to the avidity of oxygen, therefore the element that is added grows into the surface groups polymers (agglomerate) of single form or complex form in cold annealing process, as MnO, SiO 2, Al 2O 3, TiO etc.
Along with the amount of surface groups polymers constantly increases, the wettability variation of plating bath, the alloying reaction in the hot-galvanizing is disturbed further, thereby produces surface imperfection as plating area not etc.
In addition, the alligatoring meeting of surface groups polymers adheres to the surface groups polymers of alligatoring and the furnace rolls (hearthroll) of continuous furnace, produces trickle indenture on the surface of electroplating steel plate, thus the influence that the surface quality of steel plate is produced significant adverse.
For problem JP2002-146477, JP2001-64750 and the JP2002-155317 that solves above-mentioned plating defective aspect discloses by element-specific such as Cr, Sb etc. are added in the steel plate so that the technology of plate property to be provided; JP2001-288550 then discloses the technology that the roll coil of strip by pre-oxidation heat before cold rolling suppresses the formation of surperficial agglomerate during the cold annealing.
But,, obtainablely be used for hot rolling, cold rolling and continous way annealed device realization at present nor can use, so these technology do not come into operation commercial because these technology can not be guaranteed this effect by adding element-specific.
Summary of the invention
Technical problem
Therefore, the present invention is proposed to address the above problem.An object of the present invention is to provide a kind of galvanized steel plate that is used for, this steel plate has excellent workability, its tensile strength is 28-50 f/, and it has the fatigue property and the surface quality of excellent formability, secondary processing brittleness resistance, welding node.
Another object of the present invention provides a kind of manufacturing and is used for galvanized method with steel plate of excellent workability.
Technical scheme
According to an aspect of the present invention, realize above-mentioned and other purpose by being provided for galvanized steel plate with excellent workability, this steel plate contains in weight % 0.010% or lower C, 0.1% or lower Si, the Mn of 0.06-1.5%, 0.15% or lower P, 0.020% or lower S, the dissolving Al (Sol.Al) of 0.10-0.40%, 0.010% or lower N, the Ti of 0.003-0.010%, the Nb of 0.003-0.040%, the B of 0.0002-0.0020%, 0.05% or lower Mo, among the Sb of 0.005-0.05% and the Sn of 0.005-0.05% one or both, surplus is Fe and other unavoidable impurities, wherein when Sb and Sn are added in the steel plate, their total amount is in the scope of 0.005-0.1%, and wherein the mean diameter of the surface groups polymers of above-mentioned steel plate is 1 or lower, and tensile strength is 28-50 f/.
Preferably, for the increase of 10 ℃ of annealing temperatures, the growth of the mean diameter of surface groups polymers is suppressed 10% or lower.
Another aspect of the present invention provides a kind of manufacturing to be used for galvanized method with steel plate of excellent workability to comprise: reheat contains the steel ingot of following component: in weight % 0.010% or lower C, 0.1% or lower Si, the Mn of 0.06-1.5%, 0.15% or lower P, 0.020% or lower S, the dissolving Al of 0.10-0.40%, 0.010% or lower N, the Ti of 0.003-0.010%, the Nb of 0.003-0.040%, the B of 0.0002-0.0020%, 0.05% or lower Mo, among the Sb of 0.005-0.05% and the Sn of 0.005-0.05% one or both, surplus is Fe and other unavoidable impurities, wherein when Sb and Sn were added in the steel plate, their total amount was in the scope of 0.005-0.1%; Under the final rolling temperature of single-phase austenite region,, form steel plate, then make this hot rolled steel plate coiling rolling with this reheat steel ingot of finish rolling hot rolling; Cold rolling this hot rolled steel plate; At 700 ℃ or higher this cold rolling steel plate of temperature continuous annealing.
Advantageous effects
As can be seen from the above description, the invention provides and be used for galvanized steel plate with excellent workability, its tensile strength is 28-50 f/, and it has the fatigue property and the surface quality of excellent formability, secondary processing brittleness resistance, welding node.
The accompanying drawing summary
In conjunction with following specification sheets and following accompanying drawing, will be more readily understood aforementioned and other target of the present invention, wherein:
Fig. 1 describes at different types of steel and annealing temperature the variation diagram of the amount of surface groups polymers.
Fig. 2 shows at different types of steel and after heat is coiled, and the surface groups polymers is on the gas cooling steel plate and the distribution plan on the steel plate of water-cooled.
Fig. 3 shows at different types of steel and different annealing temperatures the distribution plan of the surface groups polymers on the different steel.
Implement best mode of the present invention
Hereinafter preferred implementation will be described in conjunction with the accompanying drawings.
Steel plate of the present invention will be described in the mode of composition.
C plays the effect of space solid solute element in steel, and stop to form 111 structures, and this is favourable for the workability in the process that forms this structure when cold rolling and the annealing in steel plate.Excessive carbon need increase the consumption of Ti and Nb, and both are forming elements of carbide and nitride for the backs, thereby cause manufacturing cost to increase this disadvantageous result.Therefore, carbon content is preferably 0.010% or lower.
Si is that annealing the time causes tempering color, forms the element of plating area not and surfacial spalling (scale) when electroplating.Therefore, the content of silicon is preferably 0.1% or lower.
Mn is solution strengthening element and adding as an alternative, is used to guarantee the intensity of steel.But if Mn content surpasses 1.5%, the r value of steel and stretchiness be rapid variation, and if Mn content be lower than 0.06%, then steel are owing to the cause of wherein S becomes fragile.Therefore, the content of Mn is preferably 0.06-1.5%.
P also is representational solution strengthening element, and it and Mn together add in the steel, is used to gain in strength.In the time of in P being added to Ti-Nb steel of the present invention, it causes the growth of 111 structures by grain refining, grain boundary segregation etc., and this is favourable to the r value.But if P content surpasses 0.15%, the stretchiness of steel will reduce rapidly, and fragility then significantly increases.Therefore, P content is preferably 0.03-0.15%.
When production was used for the steel of deep draw, the S content in the steel was restricted to 0.005% or lower low scope usually.But according to the present invention, owing to contain Mn in the steel, therefore, S all in the steel are deposited as MnS, thus the formability variation that can avoid the solid solution owing to S to cause.
Therefore, according to the present invention, S content is preferably 0.020% or lower, this scope can break away from cause rolling during the scope of edge crack.
For the cold-rolled steel section product, the dissolving Al content of steel is controlled in the scope of 0.02-0.07% usually, and considers manufacturing cost, and dissolved oxygen then maintains enough low amount in the steel.
But according to the present invention, dissolving Al can guarantee that the deep draw performance is being stablized than low temperature thermal oxidation.
In other words, according to the present invention, if dissolving Al content is 0.10% or higher in the steel, it can significantly stop the effect of the inhibition recrystallize of P, thereby excite recrystallize, and it also help the settling alligatoring in the steel to form 111 structures.If dissolving Al content surpasses 0.40%, it will cause, and manufacturing cost increases, the deterioration of efficiency of continuous casting operation.Therefore, dissolving Al content is preferably in the scope of 0.10-0.40%.
In addition, in steel plate of the present invention, since dissolving Al content influence to as the Ti of carbide or nitride or the sedimentary formation of Nb base with this throw out of alligatoring, therefore it is crucial component, compare with the IF steel of routine, it provides more enhanced steel workability with a spot of Ti and Nb.
If N is present in the steel with the solid solution form, then it will make the workability deteriorates of steel.In addition, if excessive N remains in the steel, then need to increase the Ti that added and the amount of Nb, in steel, N is fixed as settling.Therefore, the content of N is preferably 0.010% or lower.
B is the grain-boundary strengthening element, and it can effectively increase the fatigue property of spot welding node, the crystal boundary fragility of preventing P to cause simultaneously.In order to obtain this effect by adding B, the content that need make B is 0.0002% or higher.But if the content of B surpasses 0.0020%, then the surface properties of the workability of steel and galvanized steel plate can rapid variation.Therefore, B content is preferably 0.0002-0.0020%.
Add Mo to increase the secondary processing brittleness resistance and to electroplate character.If the content of Mo surpasses 0.05%, the effect that then increases secondary processing brittleness resistance and plating character will significantly reduce, and also be disadvantageous for manufacturing cost.Therefore, Mo content is preferably 0.05% or lower.
For workability, Ti and Nb are very important elements.Consider the minimum and the optimal amount that guarantee workability (specifically being the r value) reinforced effects, Ti and Nb must be added in the steel with the amount of 0.003-0.010% and the amount of 0.003-0.040% respectively.
According to the present invention, Sb is very important element, and it significantly suppresses surface groups polymers such as MnO, SiO 2, Al 2O 3Deng generation, and in hot-work, increase and other variation suppresses the alligatoring of surface groups polymers by temperature.In order to obtain these effects, Sb content is necessary for 0.005% or higher.But,, will can not get above-mentioned effect if the Sb that adds has exceeded specific content.Therefore, the content of Sb on be limited to 0.05%.
Effect and Sb similar of Sn in steel.In order to obtain described effect, Sn content is necessary for 0.005% or higher.If but the Sn that adds surpasses specific content, will can not get above-mentioned effect.Therefore, the upper content limit of Sb is 0.05%.
When adding Sb and Sn in the steel simultaneously, their total content is preferably in the scope of 0.005-0.1%.
The method of manufacturing steel plate of the present invention hereinafter will be described.
After reheat has the steel ingot of above-mentioned composition, under the final rolling temperature of single-phase austenite region with finish rolling carry out hot rolling, coil, cold rolling, thereby cold-rolled steel sheet is provided.Then, carry out continuous annealing 700 ℃ or higher temperature.
Usually, the temperature increase causes the toughness of steel and r value to increase.
But along with the increase of annealing temperature, the amount of the surface groups polymers on the steel plate (oxide compounds of the Si of single form or complex form, Al, Mn etc.) also increases, and demonstrates tangible alligatoring trend.As a result, probably produce surface imperfection, as not plating area or surface pitting.
According to the present invention, the growth of surface groups polymers can be suppressed in the annealing temperature zone, thereby guarantees that steel have excellent surface quality.
Preferably, steel ingot carries out reheat in 1100-1300 ℃ temperature range, carries out finish rolling at 830-920 ℃, coils at 500-700 ℃.
According to the present invention, after heat is coiled, can implement air-cooled or water-cooled to hot-rolled steel sheet.
In addition, reduce ratio (reduction ratio) when cold rolling and be preferably 65% or higher, to obtain 1.9 or higher high r value.
If cold-rolled steel sheet at low-down annealing temperature, then is difficult to obtain 1.9 or higher high r value.On the contrary, the problem that the character of the cause steel bar of thermal annealing can't meet the demands if cold-rolled steel sheet at very high annealing temperature, then may produce.Therefore, annealing temperature is 700 ℃ or higher, is preferably 780-860 ℃.
Preferably, for the increase of 10 ℃ of annealing temperatures in the above-mentioned annealing region, the growth of the mean diameter of particulate state surface groups polymers is suppressed 10% or lower.
At the typical method of making the steel plate that is used for profound punching press, continuous annealing cold-rolled steel sheet in 880-930 ℃ temperature range.
Like this, because continuous annealing temperature of the present invention is lower than the annealing temperature that is applied when making typical extra deep drawing compressed steel plate, the present invention is more economical, and has excellent operability.
According to the present invention, can produce and be used for galvanized steel plate with excellent workability, the mean diameter of its surface groups polymers is 1 or lower, tensile strength is 28-50 f/.
The surface groups polymers mainly contains Si, the Al of single form or complex form, the oxide compound of Mn, Ti etc.
For the increase of 10 ℃ of annealing temperatures, the growth of the mean diameter of surface groups polymers is preferable to be suppressed 10% or lower.
The invention embodiment
Hereinafter will describe the present invention in conjunction with the embodiments in detail.
Embodiment
After will having steel ingot reheat to 1200 that table 1 forms ℃, to this steel ingot finish rolling hot rolling, and air-cooled under 890 ℃ smart hot-rolled temperature.Then, with 80% minimizing ratio that this hot-rolled steel sheet is cold rolling, thus cold-rolled steel sheet is provided.
In addition, for the steel plate of steel type 4 and 5, coiling the back with 80% minimizing ratio enforcement water-cooled and air-cooled.
For the steel plate of the steel type 1-3 in the steel plate of above-mentioned production, at 780-830 ℃ temperature range and N 2-10%H 2Annealed for 86 seconds in the atmosphere.Then, measure the Mn form as the surface of steel plate aggregate and the amount of Al.Measuring result is presented among Fig. 1.
For the steel plate (having carried out air-cooled and water-cooled respectively) of steel type 4 and 5, at 860 ℃ and N 2-10%H 2Annealed for 86 seconds in the atmosphere.Then, the shape of the surface groups polymers that forms on the research steel plate, measuring result is presented among Fig. 1.
For steel type 4 of carrying out air-cooled and water-cooled and 5 steel plate, at 800-850 ℃ and N 2-10%H 2Annealed for 86 seconds in the atmosphere.Then, the shape of the surface groups polymers that forms on the research steel plate, measuring result is presented among Fig. 1.
Table 1
Steel type Form (wt%) Comment
C Si Mn P S Mo S-Al Nb Ti B Sn Sb N
1 0.0038 0.01 0.81 0.08 0.01 0.01 0.1 0.005 0.04 0.0002 - - 0.0019 CS
2 0.0037 0.01 0.82 0.08 0.01 0.01 0.1 0.005 0.04 0.0002 0.05 - 0.0022 IS
3 0.0041 0.01 0.81 0.08 0.01 0.01 0.1 0.005 0.04 0.0002 - 0.05 0.0022 IS
4 0.0019 0.06 0.87 0.08 0.01 0.09 0.115 0.007 0.021 0.0005 - - 0.0040 CS
5 0.0023 0.06 0.87 0.08 0.01 0.09 0.15 0.007 0.021 0.0006 - 0.01 0.005 IS
IS: steel of the present invention; CS: steel relatively
As can be seen from Figure 1, satisfy the steel type 2 of condition of the present invention and compare with the steel type 1 of discontented unabridged version invention condition with 3, the amount of the surface groups polymers of its Mn and Al is lower.
In addition, as can be seen from Figure 2, satisfy the steel type 5 of condition of the present invention and compare with the steel type 5 of discontented unabridged version invention condition, the amount of its surface groups polymers is lower, and size is less.
Especially, the steel plate that has carried out air-cooled steel type 4 after heat is coiled with coil after carry out the steel plate that water-cooled obtained and compare, the size of its surface groups polymers obviously increases.On the other hand, carry out surface groups polymers big or small substantially the same of steel plate of the steel type 5 of water-cooled after heat is coiled in the size of coiling the surface groups polymers on the cold steel plate of laggard sector-style.
In addition, as can be seen from Figure 3, for steel type 4, the size of surface groups polymers increases according to the increase of annealing temperature.For steel type 5, although annealing temperature increases, the size of surperficial agglomerate does not become basically.
Should be understood that above-mentioned embodiment and accompanying drawing only are illustrative, only have the right requirement restriction of scope of the present invention.In addition, those skilled in the art will recognize that, under the situation of the scope and spirit of the present invention that do not depart from claim and limited, can make various modifications, increase and replacement the present invention.

Claims (8)

1. one kind is used for galvanized steel plate with excellent workability, and in weight %, this steel plate contains:
0.010% or lower C, 0.1% or lower Si, the Mn of 0.06-1.5%, 0.15% or lower P, 0.020% or lower S, the dissolving Al of 0.10-0.40%, 0.010% or lower N, the Ti of 0.003-0.010%, the Nb of 0.003-0.040%, the B of 0.0002-0.0020%, 0.05% or lower Mo, among the Sb of 0.005-0.05% and the Sn of 0.005-0.05% one or both, surplus is Fe and other unavoidable impurities, wherein when Sb and Sn are added in the steel plate, their total amount is in the scope of 0.005-0.1%
Wherein, the mean diameter of the surface groups polymers of this steel plate is 1 or lower, and tensile strength is 28-50 f/.
2. steel plate as claimed in claim 1, wherein, for the increase of 10 ℃ of annealing temperatures, the growth of the mean diameter of described surface groups polymers is suppressed 10% or lower.
3. steel plate as claimed in claim 1 or 2 is characterized in that, described surface groups polymers contains the oxide compound of Si single form or complex form, Al, Mn and Ti.
4. a manufacturing is used for galvanized method with steel plate of excellent workability, and this method comprises:
Reheat contains the steel ingot of following component: in weight % 0.010% or lower C, 0.1% or lower Si, the Mn of 0.06-1.5%, 0.15% or lower P, 0.020% or lower S, the dissolving Al of 0.10-0.40%, 0.010% or lower N, the Ti of 0.003-0.010%, the Nb of 0.003-0.040%, the B of 0.0002-0.0020%, 0.05% or lower Mo, among the Sb of 0.005-0.05% and the Sn of 0.005-0.05% one or both, surplus is Fe and other unavoidable impurities, wherein when Sb and Sn were added in the steel plate, their total amount was in the scope of 0.005-0.1%;
Under the final rolling temperature of single-phase austenite region,, form steel plate, then make this hot rolled steel plate coiling rolling with this reheat steel ingot of finish rolling hot rolling;
Cold rolling this hot rolled steel plate; With
At 700 ℃ or higher this cold rolling steel plate of temperature continuous annealing.
5. method as claimed in claim 4 is characterized in that, carries out reheat in 1100-1300 ℃ temperature range, carry out finish rolling at 830-920 ℃, coil at 500-700 ℃, with 65% or higher minimizing ratio carry out cold rolling and anneal at 780-860 ℃.
6. as claim 4 or 5 described methods, it is characterized in that described method also comprises: coil the cold or water-cooled of the laggard sector-style of this hot-rolled steel sheet.
7. as claim 4 or 5 described methods, it is characterized in that for the increase of 10 ℃ of annealing temperatures in the annealing region, the alligatoring of surface groups polymers is suppressed 10% or still less.
8. method as claimed in claim 6 is characterized in that, for the increase of 10 ℃ of annealing region annealing temperatures, the alligatoring of surface groups polymers is suppressed 10% or still less.
CN2006800305520A 2005-08-25 2006-08-24 Steel sheet for galvanizing with excellent workability, and method for manufacturing the same Expired - Fee Related CN101243198B (en)

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KR1020050078433A KR100711356B1 (en) 2005-08-25 2005-08-25 Steel Sheet for Galvanizing with Superior Formability and Method for Manufacturing the Steel Sheet
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KR100711356B1 (en) 2007-04-27
US20110073223A1 (en) 2011-03-31
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CN101243198B (en) 2010-12-29
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