CN104726768A - High strength hot rolled steel sheet having excellent surface property and method for manufacturing the same - Google Patents
High strength hot rolled steel sheet having excellent surface property and method for manufacturing the same Download PDFInfo
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- CN104726768A CN104726768A CN201410815940.6A CN201410815940A CN104726768A CN 104726768 A CN104726768 A CN 104726768A CN 201410815940 A CN201410815940 A CN 201410815940A CN 104726768 A CN104726768 A CN 104726768A
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- rolled steel
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 121
- 239000010959 steel Substances 0.000 title claims abstract description 121
- 238000000034 method Methods 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 34
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 17
- 229910052796 boron Inorganic materials 0.000 claims abstract description 16
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 15
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052718 tin Inorganic materials 0.000 claims abstract description 7
- 238000005096 rolling process Methods 0.000 claims description 47
- 230000014509 gene expression Effects 0.000 claims description 20
- 229910000859 α-Fe Inorganic materials 0.000 claims description 18
- 238000009749 continuous casting Methods 0.000 claims description 12
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 7
- 229910001567 cementite Inorganic materials 0.000 claims description 6
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 6
- 238000007747 plating Methods 0.000 claims description 5
- 239000011701 zinc Substances 0.000 claims description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- 238000009825 accumulation Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 235000019362 perlite Nutrition 0.000 claims description 4
- 239000010451 perlite Substances 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 238000005516 engineering process Methods 0.000 description 20
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 14
- 238000005266 casting Methods 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 230000000694 effects Effects 0.000 description 9
- 230000007547 defect Effects 0.000 description 8
- 239000011572 manganese Substances 0.000 description 8
- 238000005275 alloying Methods 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 238000005098 hot rolling Methods 0.000 description 7
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 6
- 239000005864 Sulphur Substances 0.000 description 6
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 5
- 239000004411 aluminium Substances 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 239000011248 coating agent Substances 0.000 description 5
- 238000000576 coating method Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 239000011574 phosphorus Substances 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 208000037656 Respiratory Sounds Diseases 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 238000004140 cleaning Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 239000002253 acid Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229920001296 polysiloxane Polymers 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 241000219307 Atriplex rosea Species 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000002932 luster Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000004064 recycling Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- 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
- C22C38/008—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
- C22C38/06—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- 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
- 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
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
-
- 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
- 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
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
-
- 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
- C21D2211/003—Cementite
-
- 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
-
- 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
- C21D2211/009—Pearlite
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- Chemical & Material Sciences (AREA)
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- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
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- Chemical Kinetics & Catalysis (AREA)
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a high strength hot rolled steel sheet having excellent surface property, yield strength and moldability, a method for manufacturing the same. The hot rolled steel sheet comprises, by weight, 0.02-0.06% of C, 0.1-1.0% of Mn, 0.001-0.5% of Si, 0,01-0.04% of Al, 0.001-0.05% of P, 0.001-0.006% of S, 0.0001-0.002% of B, 0.001-0.015% of N, and 0.0001-0.18% of more than one element selected from Cu, Cr, Ni, Mo and Sn, the residual is Fe and unavoidable impurities, wherein C, B, N and P satisfy 5<=[(B/N)*(C/P)*100]<=300, wherein B, N,C and P are values respectively by dividing weight percentage by atomic weight.
Description
Technical field
The present invention relates to a kind of high tensile hot rolled steel sheet and the manufacture method thereof that can be used for the surface quality excellence of building board, office appliance, pipe or square tube, car inner plate parts etc.
Background technology
In recent years along with the development of hot rolling technique, the thickness of hot-rolled steel sheet is more and more thinner, is even thinned to and cold-rolled steel sheet condition of equivalent thickness.In order to improve plasticity or the processibility of this Thin Specs (thin-gauge) hot-rolled steel sheet, attempting various method.
Patent documentation 1 be relevant improve thin format hot rolled steel plate processibility in first technology.Patent documentation 1 relates to a kind of soft steel that utilizes to guarantee the hot-rolled steel sheet manufacturing technology of high strength and high ductibility, by adding B in the soft steel of 0.02 ~ 0.04wt%, make the width along steel plate form uniform tissue and thick ferrite, use and guarantee high elongation rate.Another is patent documentation 2 in first technology.Patent Document 2 discloses B and Cr, the Mo element of a kind of interpolation 8 ~ 33ppm, and temperature is reduced to the method that below the Ar3 temperature of steel plate is rolled.
But, described disclosed in first technology thin format hot rolled steel plate because elongation is high and yield strength is low, be therefore difficult to the technical field being applicable to the high-yield strength requiring to have more than 260MPa.
In addition, various trial was carried out as the technology manufacturing thin format hot rolled steel plate, what wherein receive publicity is substitute mill scale (mill) in the past with scrap iron (scrap) to manufacture molten steel in electric furnace, and recycling casting and rolling process carries out casting and the small-sized rolling technology (mini mill process) of rolling continuously.Patent Document 3 discloses a kind of method being improved soft steel ductility by described small-sized rolling technology.
In described patent documentation 3, the B adding more than 20ppm in the steel containing external (Tramp) element improves the Ar3 temperature of steel plate, and demonstrates the elongation of more than 40%.In addition, there is the content of adding Nb in described patent documentation 3, but add the manufacturing cost that Nb can increase hot-rolled steel sheet.
Therefore, also do not have a kind of technology to be disclosed in so far and utilize scrap iron to manufacture molten steel and manufacture in the small-sized rolling technology of hot-rolled steel sheet with this by casting and rolling process, there is high strength and guarantee excellent plasticity, there is the hot-rolled steel sheet of the characteristic of surface quality excellence simultaneously.
Patent documentation 1: No. 1999-0072735th, Korean Patent Laid
Patent documentation 2: No. 2002-0040436th, Korean Patent Laid
Patent documentation 3: No. 2001-0083963rd, Korean Patent Laid
Summary of the invention
The invention provides and a kind of there is high yield strength and plasticity, and there is hot-rolled steel sheet and the manufacture method thereof of excellent surface quality.
The high tensile hot rolled steel sheet of surface quality excellence of the present invention, it comprises the C of 0.02 ~ 0.06%, Mn, the Si of 0.0001 ~ 0.5%, Al, the P of 0.001 ~ 0.05%, S, the B of 0.0001 ~ 0.002%, the N of 0.001 ~ 0.015% of 0.001 ~ 0.006% of 0.01 ~ 0.04% of 0.1 ~ 1.0% by weight percentage, and comprise more than one elements be selected from Cu, Cr, Ni, Mo and Sn of 0.0001 ~ 0.18%, surplus is Fe and inevitable impurity, and described C, B, N and P meet following relational expression 1.
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are the respective weight percent value divided by respective nucleidic mass.
The manufacture method of the high tensile hot rolled steel sheet of surface quality excellence of the present invention, comprises the following steps:
Preparation meets the molten steel of described component and relational expression 1;
Described molten steel is become thin slab with the speed continuous casting of more than 4.5mpm;
Roughing is carried out to described thin slab, to obtain batten (bar plate);
At the temperature of 780 ~ 880 DEG C, finish rolling is carried out, to obtain hot-rolled steel sheet with the speed of 200 ~ 600mpm to described batten;
Described hot-rolled steel sheet is cooled to 500 ~ 650 DEG C; And
Batch the hot-rolled steel sheet of described cooling.
The present invention can provide a kind of thin format hot rolled steel plate, one especially can be provided to have high-yield strength and high elongation rate that is high formability, and have the hot-rolled steel sheet of excellent surface quality.
Particularly, the invention provides a kind of electric furnace molten steel utilizing scrap iron to manufacture containing extraneous element and high content nitrogen, thus manufacture the technology of hot-rolled steel sheet, therefore can improve resource reutilization rate, productivity and save energy.
Accompanying drawing explanation
Fig. 1 is the schematic diagram for illustration of hot-rolled steel sheet manufacture method one example of the present invention.
Fig. 2 is the distribution plan of the microstructure grain size distribution of example 1 in the display embodiment of the present invention.
In figure: 10, continuous caster 20, roughing mill 30, induction heater 40, Coil Box (can omit) 50, finishing mill 60, runoff table 70, reeling machine.
Embodiment
Below, the present invention is described in detail.First, component of the present invention (% by weight) is described in detail.
Hot-rolled steel sheet of the present invention comprises the C of 0.02 ~ 0.06%, Mn, the Si of 0.0001 ~ 0.5%, Al, the P of 0.001 ~ 0.05%, S, the B of 0.0001 ~ 0.002%, the N of 0.001 ~ 0.015% of 0.001 ~ 0.006% of 0.01 ~ 0.04% of 0.1 ~ 1.0% by weight percentage, and comprises more than one elements be selected from Cu, Cr, Ni, Mo and Sn of 0.0001 ~ 0.18%.
Carbon (C): 0.02 ~ 0.06%
C is the element forming carbide or be solid-solution in ferrite and gain in strength.Carbon content lower than 0.02% time, target yield strength of the present invention cannot be guaranteed, need to add a large amount of other alloying elements.When carbon content is more than 0.06%, due to by high-speed continuous casting alloying steel, therefore form solidified shell in uneven thickness, thus cause operating troubles such as casting blank defect or molten steel to flow out.Therefore, the content of carbon (C) is preferably 0.02 ~ 0.06%.
Manganese (Mn): 0.1 ~ 1.0%
Manganese (Mn) suppresses ferritic formation and increases austenitic stability, and low temperature phase change is easily formed, thus increases the intensity of steel.Fe content lower than 0.1% time, target strength of the present invention cannot be guaranteed, and steel making operation and productivity can be reduced.If Fe content is more than 1.0%, then exceeds target strength and cause processibility to be deteriorated, thus may crack when the parts of press process complicated shape.And a large amount of element of costliness that uses can cause manufacturing cost to rise unreasonably.Therefore, the content of manganese (Mn) is preferably 0.1 ~ 1.0%.
Silicon (Si): 0.0001 ~ 0.5%
Silicon (Si) suppresses higher content strengthening and carbide are formed and increase stability of retained austenite, and then increase the element of steel plate ductility.Silicone content lower than 0.0001% time, described effect cannot be guaranteed.When silicone content is more than 0.5%, the scale defects that may produce not easily pickling, as red oxidization skin (redscale), causes the poor surface quality of hot-rolled steel sheet, needs powerful except descaling (descaling) for this reason.Therefore, the content of silicon (Si) is preferably 0.0001 ~ 0.5%.
Aluminium (Al): 0.01 ~ 0.04%
Aluminium (Al) reacts with the oxygen in steel and improves the degree of cleaning of steel and suppress the formation of carbide, thus improve the stability of retained austenite, increases the element of the ductility of steel plate thus.Aluminium content lower than 0.01% time, described effect cannot be guaranteed.When aluminium content is more than 0.04%, reacts with the nitrogen (N) in steel and form AlN, therefore can cause crackle of steel billet when manufacturing thin slab, thus reducing the quality of strand or hot-rolled steel sheet.Therefore, the content of aluminium (Al) should control low as far as possible, is preferably 0.01 ~ 0.04%.
Phosphorus (P :) 0.001 ~ 0.05%
Described phosphorus (P) is the element reducing ferrite grain size and increase armor plate strength.Phosphorus content lower than 0.001% time, the strengthening effect based on grain-size refinement cannot be guaranteed.If phosphorus content is more than 0.05%, then producing segregation at crystal boundary and/or alternate grain boundaries when continuous casting and rolling can cause fragility, and press formability can be made to be deteriorated.In soft steel, the content of residual carbon is high, so have precedence over P element to segregate to ferrite grain boundaries, the crystal boundary fragility that thus P element causes can be inhibited.Therefore, the content of phosphorus (P) is preferably 0.001 ~ 0.05%.
Sulphur (S): 0.001 ~ 0.006%
Described sulphur (S) is that the impurity element in steel can cause surface defect of bloom and reduce ductility and the weldability of steel plate.But, manufacturing process being difficult to sulphur content controlled is lower than 0.001%, when described sulphur content is more than 0.006%, can form excessive MnS non-metallic inclusion in steel, and in continuous casting and solidifying process, produce segregation and cause heat cracking, thus reduce ductility and the weldability of steel plate.On the other hand, in the present invention, by endless rolling method (endless rolling) manufacture, sulphur (S) content is controlled to obtain alap steel plate, thus can prevent from producing the crackle in hot rolled strip side.Therefore, the content of sulphur (S) is preferably 0.001 ~ 0.006%.
Boron (B): 0.0001 ~ 0.002%
Described boron (Β) is that the austenite grain boundary segregating to steel suppresses austenite recrystallization and suppresses the nucleus growth of ferrite crystal grain and form thick ferritic structure, and then increases the element of steel plate ductility.Boron contents lower than 0.0001% time, cannot obtain ductility increase effect.When Boron contents is more than 0.002%, the hardening capacity of steel can be increased, thus the ductility of steel can be caused to reduce.And if excessive interpolation B element, the edge of strand or batten can crack in continuous casting and/or the operation of rolling, and can austenite grain boundary be segregated to during rolling under low temperature and increase the anti-deformation behavior of steel plate, ultra-thin gauge rolling can be made to become difficulty.Therefore, the content of boron (B) is preferably 0.0001 ~ 0.002%.
Nitrogen (N): 0.001% ~ 0.015%
Described nitrogen (N) is element austenite being stablized and forms nitride.Nitrogen content lower than 0.001% time, be difficult to obtain described effect.When nitrogen content is more than 0.015%, can with the Al element reaction that exists in electric steel and form precipitate, thus strand crack defect can be caused.Therefore, the content of nitrogen (N) is preferably 0.001 ~ 0.015%.
The present invention comprises more than one elements in extraneous element Cu, Cr, Ni, Mo and Sn, and its total content is preferably 0.001 ~ 0.18%.Described external (Tramp) element is the impurity element from the waste material being used as raw material in process for making, therefore preferably reduces the content of these elements as far as possible.When the total content of these elements is more than 0.18%, steel billet can be caused to produce surface crack and reduce the surface quality of hot-rolled steel sheet.
In described extraneous element, Cu increases the corrosion proof element of steel plate, sometimes also can specially add, to improve the solidity to corrosion of hot rolling acid-cleaning steel plate.
In the present invention, described C, B, N and P preferably meet following relational expression 1.
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In described relational expression 1, C, B, N and P represent respective content (% by weight) value divided by respective nucleidic mass.
The target yield strength that what described relational expression 1 derived is for guaranteeing steel and the component relation that yield tensile ratio should meet.The value of described relational expression 1 is less than 5 expressions by adding separately P element or compound interpolation P+B element, can guarantee the yield strength of more than 260MPa.The value of described relational expression 1 exceeds 300 expressions and adds B element separately and have the average crystal grain of more than 12 μm, the yield strength of 260MPa can not be guaranteed, and there is the elongation of more than 40%, also represent due to by endless rolling technique rolled steel strip at lower than the temperature of 880 DEG C, although the homogeneity of structure that the Ar3 temperature that can increase steel reduces and causes, but because the anti-deformation behavior of steel plate during hot rolling increases, therefore rolling can be deteriorated.
The present invention, except described component, can comprise the Ca of less than 0.01% further.The avidity of described Ca and oxygen is very high, thus exists with oxide compound or sulphided form, thus controls non-metallic inclusion form and distribution, contribute to the balling of inclusion, and effectively prevent crackle, also form Cr-Ca miscible precipitate, be thus conducive to solidity to corrosion.
Surplus is Fe and inevitable impurity.This represents except mentioned component, can add other alloying constituents further in the scope not exceeding the technology of the present invention thought.
The microstructure of hot-rolled steel sheet of the present invention is principal phase with ferrite, and is present in the cementite of ferrite grain boundaries and/or pearlitic area fraction is less than 5%.In the present invention, described ferrite average grain size is preferably less than 12 μm.
As mentioned above, by guaranteeing the ferritic structure with fine-grain, that simultaneously possess intensity and ductility, that material deviation is little steel band can be manufactured.Just, if described ferrite grain size is more than 12 μm, be then difficult to guarantee target strength and ductility, therefore described ferrite grain size is preferably less than 12 μm.
In addition, if the cementite formed more than 5% and/or perlite, then snappiness may be deteriorated.Therefore, described cementite and/or pearlitic structure preferably have the area fraction of less than 5%, more preferably do not form described perlite.When not forming described cementite and/or perlite, hot-rolled steel sheet of the present invention can have ferrite single phase structure.
In addition, the deviation of described ferrite grain size is preferably less than 7 μm.Hot-rolled steel sheet of the present invention does not almost form cementite and pearlitic ferrite single phase structure.Usually, hot-rolled steel sheet is that the ferritic phase with uneven grain size is formed, and the deviation of grain-size is less forms microstructure by the crystal grain of almost identical size, and can guarantee uniform intensity and processibility.For this reason, in the present invention preferred by described deviation control below 7 μm.
Hot-rolled steel sheet of the present invention has the yield strength of more than 260MPa, and guarantees the elongation of more than 30%, thus guarantees excellent intensity and ductility, has the feature of surface quality excellence simultaneously.
Below, manufacture method of the present invention is described.Manufacture method of the present invention utilizes the endless rolling method based on thin slab casting and rolling process to pass through small-sized rolling technology, can manufacture the hot-rolled steel sheet of intensity, ductility and surface quality excellence.Fig. 1 is the schematic diagram for illustration of hot-rolled steel sheet manufacture method one example of the present invention.Below, describe in further detail with reference to Fig. 1.
As shown in Figure 1, be applicable to small-sized rolling technology of the present invention and comprise continuous casting, roughing, finish rolling, cool and batch, described each technique carries out being interrupted continuously.The feature of hot-rolled steel sheet manufacture method of the present invention is, while the described each processing condition of control, the actuating speed (mass rate) of roughing-finish rolling-batch is controlled to identical, thus at the uniform velocity rolling can be realized, produce material and thickness deviation excellent and do not electroplate the hot-rolled steel sheet of stripping.
First, in continuous caster 10, the steel billet a that thickness is 30 ~ 150mm is manufactured.Compared with this is the steel billet of more than 200mm with the thickness produced in the continuous caster of existing rolling technology, there is quite thin thickness, this steel billet is called thin slab (Thin slab).Described thin slab is delivered directly to roughing mill 20 with continuous print process and is rolled, therefore the heat of steel billet self can directly be utilized, thus can save energy, and by these processes, the formation microstructure that can occur in continuous casting and rough rolling process and the transition process of precipitate become different in existing rolling technology, and final obtained steel plate mechanical characteristics can change.On the other hand, if the thickness of described thin slab is more than 150mm, diminish with the difference of existing rolling technology, if be less than 30mm, strand temperature can sharply decline, and is difficult to form uniform tissue.For solving this problem, heating installation can be set in addition, but this can cause production cost to rise, therefore preferably not adopting as far as possible.
In addition, thin slab is rolled into desired final thickness in roughing mill 20 and finishing mill 50, and after being cooled by runoff table (R0T) 60, batches, thus manufacture steel plate at reeling machine 70 with certain temperature.The present invention is described above, the actuating speed of roughing mill 20-finishing mill 50-reeling machine 70 is it is characterized in that to be controlled to identical, thus carry out at the uniform velocity rolling, when casting speed and roll speed there are differences, for compensating this difference, Coil Box (coil box) 40 can be set before finishing mill 50, thus batten (bar plate) b by induction heater 30 once be batched.
First, for the continuous casting step for obtaining described thin slab, after preparation meets the molten steel of described alloy component, casting speed being set as more than 4.5mpm (miter per minute), being preferably set to 4.5 ~ 7.5mpm.This is because casting and the operation of rolling are carried out continuously, to guarantee that target rolling temperature then needs to a certain degree above casting speed, casting speed is preferably at more than 4.5mpm for this reason.But during more than 7.5mpm, because the liquid level instability of molten steel can reduce successful operation rate, therefore described casting speed is preferably in the scope of 4.5 ~ 7.5mpm.
The thin slab obtained by described casting will through roughing step, is that roughing mill 20 by being made up of 2 ~ 4 rolling machine frames realizes to the described roughing of thin slab.Now, at the inlet side of described roughing mill, the surface temperature of thin slab is preferably 1000 ~ 1200 DEG C.If the surface temperature of described thin slab is lower than 1000 DEG C, then roughing load can be caused to increase and can crack at batten edge part in rough rolling process, this can cause the defect of hot-rolled steel sheet edge part.On the other hand, when the surface temperature of described thin slab is more than 1200 DEG C, the problem of the hot rolling surface quality reduction that the heat scale (scale) as residual causes may be there is.
In addition, when carrying out described roughing, accumulation draft is preferably 60 ~ 90%, and this is conducive to manufacturing the hot-rolled steel sheet with excellent material deviation as target in the present invention.Roughing draft is got over Gao Yueneng and is made to be formed in the inner continuous casting microstructure of continuous-cast blank (thin slab) and alloying constituent is uniformly distributed, and for realizing this effect, described accumulation draft is preferably more than 60%.But during more than 90%, rolling deformation resistance becomes large and causes operationally becoming difficulty, and when therefore carrying out described roughing, accumulation draft is preferably in the scope of 60 ~ 90%.
In finish rolling step, the batten obtained by described roughing is rolled in the scope of 200 ~ 600mpm, preferably carries out at the temperature lower than existing rolling technology.Described rolling is preferably carried out under certain speed.As mentioned above, identical mass rate (mass flow) can be controlled to by rolling from continuous casting to coiling technique.But, if roll speed is excessively slow, be then difficult to the temperature of the hot-rolled steel sheet guaranteeing rolling, if too fast, the broken belt that operating troubles causes as mishandle can occur when controlled rolling, be difficult to hot-rolled temperature to be controlled to target value.
In addition, final rolling temperature is set to and lower than the existing rolling technology temperature i.e. reason of less than 880 DEG C is, within the scope of casting speed of the present invention, strand is solidified completely, avoid the not solidified strand of rolling as far as possible, thus improve the stability of endless rolling operation, and the heat scale defect that can produce when as far as possible reducing high temperature finish rolling.In addition, also be there is the effect being made grain refining by the ratio of the austenite phase of low temperature rolling increase non-recrystallization.But, when described hot-rolled temperature is lower than 780 DEG C, can occur operating troubles as hot rolling load sharply increase the broken belt that causes, therefore described hot rolling is preferably carried out at 780 ~ 880 DEG C.
Then, described hot-rolled steel sheet preferably at runoff table (R0T) continuous coo1ing to target coiling temperature, now speed of cooling can in normal ranges in the art.Described cooling proceeds to 500 ~ 650 DEG C, and batches in described temperature range, when described coiling temperature is lower than 500 DEG C, erose ferritic phase can be formed, increase the ununiformity of microstructure thus, and during more than 650 DEG C, because pearlitic formation can cause bendability to be deteriorated.Therefore, described coiling temperature preferably in the scope of 500 ~ 650 DEG C, in order to the stability of the microstructure that the present invention will obtain, preferably in the scope of 580 ~ 650 DEG C.
Batch the step of rear pickled hot steel plate described in can comprising further, the oxide skin being formed in hot rolled sheet metal surface can be removed by this step.Described acid cleaning process can adopt all ordinary methods in the art.
After carrying out described acid pickling step, described hot-rolled steel sheet is heated to 450 ~ 550 DEG C, and is introduced into molten zinc plating groove with continuous print technique and electroplates, then at 500 ~ 560 DEG C, carry out constant temp. heating process, thus molten zinc plating hot-rolled steel sheet can also be manufactured.When described Heating temperature is lower than 450 DEG C, rise because insufficient heating can cause plating defects (spot (Tears mark)) to produce frequency, and during more than 550 DEG C, because the shade deviation on electrolytic coating surface can cause plate surface defect.In addition, described constant temp. heating process is to realize being uniformly distributed and the alloying of electrolytic coating of alloying element, when temperature is lower than 500 DEG C, be difficult to obtain described effect, and electrolytic coating surface imperfection can be there is as ripple mark, and during more than 560 DEG C, the Fe-Zn alloying occurred at substrate steel/electrolytic coating near interface, substrate steel interface can be uneven, thus cause the problem that electrolytic coating color and luster there are differences.
Below, embodiments of the invention are described in detail.But following embodiment, only for illustration of the present invention, is not intended to limit the invention.
(embodiment)
Preparing the component (% by weight had in following table 1, surplus is Fe and inevitable impurity) molten steel A ~ J after, carry out with the speed of 5mpm the thin slab that high-speed continuous casting makes 80 ㎜, the actuating speed of the roughing mill 20-finishing mill 50-reeling machine 70 shown in Fig. 1 is controlled to identical speed and carries out equal speed rolling.Hot-rolled steel sheet has been manufactured by the method for the finish rolling outlet side temperature (FDT), coiling temperature (CT) etc. of appropriate table 2.
But the K steel grade in following table 1 and 2 is not adopt endless rolling, but to be reheated by conventional steel billet and hot rolling technology manufacture.
[table 1]
In described table 1, Tr. is the total content of extraneous element Cu, Cr, Ni, Mo and Sn, and formula 1 is atomic molar ratio, represents the value of [(B/N) * (C/P) * 100].
For manufactured hot-rolled steel sheet, utilize ASTM sample test mechanical characteristics, the results are shown in following table 2.In addition, measure the ferrite grain size (FGS) of hot-rolled steel sheet, and Surface Quality is evaluated, and the results are shown in table 2.When evaluating surface quality, after removing surface scale, effects on surface glossiness is evaluated.Zero presentation surface glossiness is 60 ~ 70, △ presentation surface glossiness is less than 60.
[table 2]
As described in shown in table 2, the example meeting component of the present invention and condition have more than 260MPa yield strength and have more than 30% elongation.And, excellent surface quality can be guaranteed.
On the other hand, its component of comparative example 1 to 4 exceeds scope of the present invention, even if meet processing condition of the present invention, and surface quality or poor.
Comparative example 5 and 6 is situations that component and relational expression 1 exceed scope of the present invention, although crystal grain can by refinement, surface quality is poor.In addition, comparative example 7 and 8 is situations that relational expression 1 exceeds scope of the present invention, and grain-size is thick and surface quality is poor.Comparative example 9 does not meet component of the present invention, does not reach yield strength of the presently claimed invention and coarse grains.
In addition, Fig. 2 is the chart of the ferrite crystal grain distribution showing described example 1.Known see Fig. 2, its ferrite average grain size (FGS) of described example 1 is less than 12 μm, and deviation is less than 7 μm.
Claims (10)
1. the high tensile hot rolled steel sheet of a surface quality excellence, it comprises the C of 0.02 ~ 0.06%, Mn, the Si of 0.0001 ~ 0.5%, Al, the P of 0.001 ~ 0.05%, S, the B of 0.0001 ~ 0.002%, the N of 0.001 ~ 0.015% of 0.001 ~ 0.006% of 0.01 ~ 0.04% of 0.1 ~ 1.0% by weight percentage, and comprise more than one elements be selected from Cu, Cr, Ni, Mo and Sn of 0.0001 ~ 0.18%, surplus is Fe and inevitable impurity
Wherein, described C, B, N and P meet following relational expression 1,
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are the respective weight percent value divided by respective nucleidic mass.
2. the high tensile hot rolled steel sheet of surface quality excellence according to claim 1, wherein,
Take ferrite as Main Tissues,
Comprise in cementite and perlite more than one, its area fraction is less than 5%.
3. the high tensile hot rolled steel sheet of surface quality excellence according to claim 2, wherein,
Described ferrite grain size is less than 12 μm.
4. the high tensile hot rolled steel sheet of surface quality excellence according to claim 1, its thickness is 1.2 ~ 2.8 ㎜.
5. a manufacture method for the high tensile hot rolled steel sheet of surface quality excellence, comprises the following steps:
Prepare molten steel, this molten steel comprises the C of 0.02 ~ 0.06%, Mn, the Si of 0.0001 ~ 0.5%, Al, the P of 0.001 ~ 0.05%, S, the B of 0.0001 ~ 0.002%, the N of 0.001 ~ 0.015% of 0.001 ~ 0.006% of 0.01 ~ 0.04% of 0.1 ~ 1.0% by weight percentage, and comprise more than one elements be selected from Cu, Cr, Ni, Mo and Sn of 0.0001 ~ 0.18%, surplus is Fe and inevitable impurity, and described C, B, N and P meet following relational expression 1;
Described molten steel is become thin slab with the speed continuous casting of more than 4.5mpm;
Roughing is carried out to described thin slab, to obtain batten;
At the temperature of 780 ~ 880 DEG C, finish rolling is carried out, to obtain hot-rolled steel sheet with the speed of 200 ~ 600mpm to described batten;
Described hot-rolled steel sheet is cooled to 500 ~ 650 DEG C; And
Batch the hot-rolled steel sheet of described cooling,
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are the respective weight percent value divided by respective nucleidic mass.
6. the manufacture method of the high tensile hot rolled steel sheet of surface quality excellence according to claim 5, wherein,
The thickness of described thin slab is 30 ~ 150 ㎜.
7. the manufacture method of the high tensile hot rolled steel sheet of surface quality excellence according to claim 5, wherein,
The accumulation draft of described roughing is 60 ~ 90%.
8. the manufacture method of the high tensile hot rolled steel sheet of surface quality excellence according to claim 5, wherein,
During described roughing, the feeding temperature of thin slab is 1000 ~ 1200 DEG C.
9. the manufacture method of the high tensile hot rolled steel sheet of surface quality excellence according to claim 5, further comprising the steps:
Described batch after, hot-rolled steel sheet described in pickling.
10. the manufacture method of the high tensile hot rolled steel sheet of surface quality excellence according to claim 9, further comprising the steps:
After described pickling, described hot-rolled steel sheet is heated to 450 ~ 550 DEG C;
Molten zinc plating is carried out by the hot-rolled steel sheet heated to described; And
At 500 ~ 560 DEG C, constant temperature process is carried out to the hot-rolled steel sheet of described molten zinc plating.
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| KR101560944B1 (en) | 2015-10-15 |
| CN104726768B (en) | 2017-06-06 |
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