CN104726768B - The excellent high tensile hot rolled steel sheet of surface quality and its manufacture method - Google Patents
The excellent high tensile hot rolled steel sheet of surface quality and its manufacture method Download PDFInfo
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- CN104726768B CN104726768B CN201410815940.6A CN201410815940A CN104726768B CN 104726768 B CN104726768 B CN 104726768B CN 201410815940 A CN201410815940 A CN 201410815940A CN 104726768 B CN104726768 B CN 104726768B
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- rolled steel
- hot rolled
- steel plate
- surface quality
- high tensile
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 117
- 239000010959 steel Substances 0.000 title claims abstract description 117
- 238000000034 method Methods 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 32
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 22
- 229910052796 boron Inorganic materials 0.000 claims abstract description 21
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 20
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052717 sulfur 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 45
- 229910000859 α-Fe Inorganic materials 0.000 claims description 19
- 238000005266 casting Methods 0.000 claims description 12
- 229910001562 pearlite 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 6
- 238000009825 accumulation Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 239000011701 zinc Substances 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 14
- 238000009749 continuous casting Methods 0.000 description 12
- 239000011572 manganese Substances 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 230000007547 defect Effects 0.000 description 9
- 238000005516 engineering process Methods 0.000 description 9
- 238000005098 hot rolling Methods 0.000 description 9
- 229910001566 austenite Inorganic materials 0.000 description 8
- 239000013078 crystal Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 6
- 238000005275 alloying Methods 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
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-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
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000011574 phosphorus Substances 0.000 description 5
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 4
- 208000037656 Respiratory Sounds Diseases 0.000 description 4
- 239000005864 Sulphur Substances 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 239000002253 acid Substances 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000010438 heat treatment Methods 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
- 239000010703 silicon Substances 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000010586 diagram Methods 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
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 241000219307 Atriplex rosea Species 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 235000019628 coolness Nutrition 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000002932 luster Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000010813 municipal solid waste Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000000717 retained effect Effects 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
- 238000003466 welding Methods 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
Abstract
With yield strength and formability and there is the hot rolled steel plate and its manufacture method of excellent surface quality the present invention relates to a kind of.The hot rolled steel plate is by weight percentage comprising 0.02~0.06% C, 0.1~1.0% Mn, 0.0001~0.5% Si, 0.01~0.04% Al, 0.001~0.05% P, 0.001~0.006% S, 0.0001~0.002% B, 0.001~0.015% N, and comprising 0.0001~0.18% selected from Cu, Cr, Ni, one or more of Mo and Sn element, balance of Fe and inevitable impurity, wherein, the C, B, N and P meets 5≤[(B/N) * (C/P) * 100]≤300, wherein B, N, C and P are value of the respective percentage by weight divided by respective atomic weight.
Description
Technical field
The present invention relates to a kind of surface that can be used for building board, office appliance, pipe or square tube, car inner plate part etc.
The high tensile hot rolled steel sheet and its manufacture method of good quality.
Background technology
Recently as the development of hot rolling technique, the thickness more and more thinner of hot rolled steel plate, in addition it is thin to same with cold-rolled steel sheet
Equal thickness.In order to improve the formability or processability of this Thin Specs (thin-gauge) hot rolled steel plate, various sides are try to
Method.
Patent document 1 is the first technology about improving thin format hot rolled steel plate processability.Patent document 1 is related to a kind of profit
The hot rolled steel plate manufacturing technology of high intensity and high ductibility is ensured with mild steel, by the mild steel to 0.02~0.04wt%
Middle addition B so that form uniform tissue and thick ferrite along the width of steel plate, using ensures high elongation rate.Separately
One first technology is patent document 2.Patent Document 2 discloses the B and Cr, Mo element of a kind of 8~33ppm of addition, and by temperature
Degree is reduced to the method rolled below the Ar3 temperature of steel plate.
However, the thin format hot rolled steel plate disclosed in the first technology is because elongation is high and yield strength is low, therefore
It is difficult to be applied to the technical field for requiring the high-yield strength with more than 260MPa.
Additionally, various trials were carried out as the technology of manufacture thin format hot rolled steel plate, wherein what is attracted attention is to use useless
Iron (scrap) substitutes conventional mill scale (mill) and molten steel is manufactured in electric furnace, recycles casting and rolling process to be carried out continuously casting
And the small-sized rolling mill practice (mini mill process) of rolling.Patent Document 3 discloses one kind by the small-sized rolling
The method of process improving mild steel ductility.
In the patent document 3, steel plate is improved to the B of more than 20ppm is added in the steel containing external (Tramp) element
Ar3 temperature, and show more than 40% elongation.In addition, occur the content of addition Nb in the patent document 3, but
Addition Nb can increase the manufacturing cost of hot rolled steel plate.
Therefore, also it is disclosed in without a kind of technology so far and manufacture molten steel using scrap iron and continuous casting and rolling technology is passed through with this
In the small-sized rolling mill practice of skill manufacture hot rolled steel plate, with high intensity and excellent formability is ensured, while having surface quality
The hot rolled steel plate of excellent characteristic.
Patent document 1：Korean Patent Laid the 1999-0072735th
Patent document 2：Korean Patent Laid the 2002-0040436th
Patent document 3：Korean Patent Laid the 2001-0083963rd
The content of the invention
The present invention provides a kind of with yield strength and formability high, and with the hot-rolled steel of excellent surface quality
Plate and its manufacture method.
The excellent high tensile hot rolled steel sheet of surface quality of the invention, it includes 0.02~0.06% by weight percentage
C, 0.1~1.0% Mn, 0.0001~0.5% Si, 0.01~0.04% Al, 0.001~0.05% P, 0.001
~0.006% S, 0.0001~0.002% B, 0.001~0.015% N, and comprising 0.0001~0.18% choosing
From one or more of Cu, Cr, Ni, Mo and Sn element, balance of Fe and inevitable impurity, described C, B, N and P meet with
Lower relational expression 1.
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are value of the respective percentage by weight divided by respective atomic weight.
The manufacture method of the excellent high tensile hot rolled steel sheet of surface quality of the invention, comprises the following steps：
Preparation meets the molten steel of the component and relational expression 1；
The molten steel is casting continuously to form thin slab with the speed of more than 4.5mpm；
Roughing is carried out to the thin slab, to obtain batten (bar plate)；
Finish rolling is carried out with the speed of 200~600mpm and at a temperature of 780~880 DEG C to the batten, to obtain heat
Rolled steel plate；
The hot rolled steel plate is cooled to 500~650 DEG C；And
Batch the hot rolled steel plate of the cooling.
The present invention can provide a kind of thin format hot rolled steel plate, can especially provide a kind of with high-yield strength and high elongation rate
That is, high formability, and with the hot rolled steel plate of excellent surface quality.
Particularly, the present invention provides a kind of electric furnace molten steel manufactured using scrap iron containing extraneous element and high content nitrogen,
So as to manufacture the technology of hot rolled steel plate, therefore resource reutilization rate, productivity ratio and energy saving can be improved.
Brief description of the drawings
Fig. 1 is the schematic diagram for illustrating hot rolled steel plate manufacture method of the invention.
Fig. 2 is the distribution map of the microstructure grain size distribution for showing example 1 in the embodiment of the present invention.
In figure：10th, conticaster 20, roughing mill 30, sensing heater 40, Coil Box (can omit) 50, finishing mill 60,
Runout table 70, coiling machine.
Specific embodiment
Below, the present invention is described in detail.First, component (weight %) of the invention is described in detail.
Hot rolled steel plate of the invention by weight percentage comprising 0.02~0.06% C, 0.1~1.0% Mn,
0.0001~0.5% Si, 0.01~0.04% Al, 0.001~0.05% P, 0.001~0.006% S, 0.0001
~0.002% B, 0.001~0.015% N, and comprising 0.0001~0.18% selected from Cu, Cr, Ni, Mo and Sn
More than one elements.
Carbon (C)：0.02~0.06%
C is to form carbide or be solid-solution in ferrite and increase the element of intensity.When carbon content is less than 0.02%, it is impossible to
Target yield strength of the invention is ensured, it is necessary to add substantial amounts of other alloying elements.When carbon content is more than 0.06%, due to logical
High-speed continuous casting manufacture steel alloy is crossed, therefore forms solidified shell in uneven thickness, so as to cause operating trouble such as casting blank defect
Or molten steel outflow.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 the stability of austenite so that low temperature phase change is easily formed, so that
Increase the intensity of steel.When manganese content is less than 0.1%, it is impossible to ensure target strength of the invention, and steel making operation can be reduced
And productivity ratio.If manganese content is more than 1.0%, processability is caused to be deteriorated beyond target strength, so as in press process complex shape
May be cracked during the part of shape.And, it is unreasonably a large amount of using expensive element manufacturing cost to be caused to rise.Cause
This, the content of manganese (Mn) is preferably 0.1~1.0%.
Silicon (Si)：0.0001~0.5%
Silicon (Si) is to suppress higher content reinforcing and carbide formation and increase stability of retained austenite, and then is increased
The element of steel plate ductility.When silicone content is less than 0.0001%, it is impossible to ensure the effect.When silicone content is more than 0.5%, may
The scale defects such as red oxidization skin (red scale) for being difficult pickling can be produced, the poor surface quality of hot rolled steel plate is caused,
Strength is needed to remove descale (descaling) for this.Therefore, the content of silicon (Si) is preferably 0.0001~0.5%.
Aluminium (Al)：0.01~0.04%
Aluminium (Al) is to be reacted with the oxygen in steel and improve the cleannes of steel and suppress the formation of carbide, so as to improve residual
The stability of austenite, thus increases the element of the ductility of steel plate.When aluminium content is less than 0.01%, it is impossible to ensure the effect
Really.When aluminium content is more than 0.04%, with steel in nitrogen (N) reaction and form AlN, therefore manufacture thin slab when can cause steel billet
Crackle, so as to reduce the quality of strand or hot rolled steel plate.Therefore, the content of aluminium (Al) should control as low as possible, preferably
0.01~0.04%.
Phosphorus (P:) 0.001~0.05%
The phosphorus (P) is the element for reducing ferrite grain size and increasing armor plate strength.Phosphorus content is less than 0.001%
When, it is impossible to ensure the reinforcing effect based on crystallite dimension refinement.If phosphorus content is more than 0.05%, in crystal boundary when continuous casting and rolling
And/or alternate grain boundaries generation segregation can cause fragility, and press formability can be made to be deteriorated.Residual carbon contains in mild steel
Amount is high, so crystal boundary fragility can be inhibited caused by segregating to ferrite grain boundaries, thus P element prior to P element.Cause
This, the content of phosphorus (P) is preferably 0.001~0.05%.
Sulphur (S)：0.001~0.006%
The sulphur (S) is that the impurity element in steel can cause surface defect of bloom and reduce ductility and the welding of steel plate
Property.However, be difficult to be controlled to sulfur content less than 0.001% in manufacturing process, when the sulfur content is more than 0.006%, in steel
Excessive MnS non-metallic inclusions can be formed, and segregation is produced during continuous casting and solidifying and is caused heat cracking, so as to drop
The ductility and weldability of low steel plate.On the other hand, in the present invention, made by endless rolling method (endless rolling)
Make and sulphur (S) content is controlled into obtain alap steel plate such that it is able to prevent that the crackle in hot rolled strip side may be produced.
Therefore, the content of sulphur (S) is preferably 0.001~0.006%.
Boron (B)：0.0001~0.002%
The boron (Β) is that the austenite grain boundary for segregating to steel suppresses austenite recrystallization and suppresses ferrite crystal grain
Nucleus growth and form thick ferritic structure, and then increase steel plate ductility element.When Boron contents are less than 0.0001%,
The increased effect of ductility cannot be obtained.When Boron contents are more than 0.002%, the quenching degree of steel can be increased, so as to steel can be caused
Ductility reduction.And, if B element is excessively added, the edge of strand or batten can be produced in continuous casting and/or the operation of rolling
Austenite grain boundary can be segregated to when being rolled under crackle, and low temperature and increase the anti-deformation behavior of steel plate, can become ultra-thin gauge rolling
Obtain difficult.Therefore, the content of boron (B) is preferably 0.0001~0.002%.
Nitrogen (N)：0.001%~0.015%
The nitrogen (N) is to stablize austenite and form the element of nitride.When nitrogen content is less than 0.001%, it is difficult to
To the effect.When nitrogen content is more than 0.015%, can with Al element reactions present in electric steel and form precipitate so that
Strand crack defect can be caused.Therefore, the content of nitrogen (N) is preferably 0.001~0.015%.
The present invention includes one or more of extraneous element Cu, Cr, Ni, Mo and Sn element, and its total content is preferably 0.001
~0.18%.External (Tramp) element is the impurity element from the waste material for being used as raw material in process for making, therefore preferably
The content of these elements is reduced as far as possible.When the total content of these elements is more than 0.18%, can cause steel billet produce face crack with
And reduce the surface quality of hot rolled steel plate.
Cu is to increase the corrosion proof element of steel plate in the extraneous element, can also specially be added sometimes, to improve hot rolling acid
Wash the corrosion resistance of steel plate.
In the present invention, described C, B, N and P preferably meet relationship below 1.
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In the relational expression 1, C, B, N and P represent value of the respective content (weight %) divided by respective atomic weight.
It is to ensure the component relation that the target yield strength and yield tensile ratio of steel should meet that the relational expression 1 is derived.Institute
The value for stating relational expression 1 is represented by individually addition P element or compound addition P+B elements less than 5, it can be ensured that more than 260MPa's
Yield strength.The value of the relational expression 1 represents the average crystal grain for individually adding B element and having more than 12 μm beyond 300, it is impossible to
Ensure the yield strength of 260MPa, and with more than 40% elongation, be also represented by due to by endless rolling technique low
The rolled steel strip at a temperature of 880 DEG C, although the structural homogenity that the Ar3 temperature of steel is reduced and caused can be increased, but due to heat
The anti-deformation behavior of steel plate increases when rolling, therefore rolling property can be deteriorated.
The present invention can further include less than 0.01% Ca in addition to the component.The Ca is non-with the affinity of oxygen
Chang Gao, thus exist with oxide or sulphided form, so as to control non-metallic inclusion form and distribution, contribute to field trash
Spheroidizing, and effectively prevent crackle, also form Cr-Ca miscible precipitates, thus be conducive to corrosion resistance.
Balance of Fe and inevitable impurity.This is represented in addition to mentioned component, without departing from skill of the present invention
Other alloying components can be further added in the range of art thought.
The microscopic structure of hot rolled steel plate of the invention is present in the cementite of ferrite grain boundaries with ferrite as principal phase
And/or the area fraction of pearlite is less than 5%.In the present invention, the ferrite average grain size be preferably 12 μm with
Under.
As described above, by ensuring the ferritic structure with fine-grain, can manufacture and be provided simultaneously with intensity and extension
Property, the steel band that material deviation is small.Simply, if the ferrite grain size is more than 12 μm, be difficult to ensure that target strength and
Ductility, therefore the ferrite grain size is preferably less than 12 μm.
If additionally, forming over 5% cementite and/or pearlite, pliability may be deteriorated.Therefore, it is described
Cementite and/or pearlitic structrure preferably have less than 5% area fraction, do not form the pearlite more preferably.Do not formed
When the cementite and/or pearlite, hot rolled steel plate of the invention can have ferrite homogeneous structure.
Additionally, the deviation of the ferrite grain size is preferably less than 7 μm.Hot rolled steel plate of the invention is almost non-shape
Into cementite and the ferrite homogeneous structure of pearlite.Generally, hot rolled steel plate is with the ferrite with uneven grain size
Mutually constitute, the deviation of crystallite dimension is smaller to be made up of microscopic structure the crystal grain of almost identical size, and is able to ensure that
Even intensity and processability.Therefore, in the present invention preferably by deviation control below 7 μm.
Hot rolled steel plate of the invention has the yield strength of more than 260MPa, and ensures more than 30% elongation, so that
Excellent intensity and ductility is ensured, while having the excellent feature of surface quality.
Below, manufacture method of the invention is described.Manufacture method of the invention is using based on thin slab casting and rolling process
Endless rolling method by small-sized rolling mill practice, intensity, ductility and the excellent hot rolled steel plate of surface quality can be manufactured.Figure
1 is the schematic diagram for illustrating hot rolled steel plate manufacture method of the invention.Hereinafter, reference picture 1 is described in further detail.
As shown in Figure 1, it is adaptable to which small-sized rolling mill practice of the invention includes continuous casting, roughing, finish rolling, cools down and batch, institute
State each technique and be carried out continuously and will not be interrupted.Hot rolled steel plate manufacture method of the invention is characterised by, in control each technique
While condition, the actuating speed (mass flow) of roughing-finish rolling-batch is controlled into it is identical, such that it is able to realize at the uniform velocity rolling
System, produce material and thickness deviation it is excellent and without plating stripping hot rolled steel plate.
First, the steel billet a that thickness is 30~150mm is manufactured in conticaster 10.This conticaster with existing rolling mill practice
The thickness of middle production is compared for the steel billet of more than 200mm, with relatively thin thickness, this steel billet is referred to as into thin slab (Thin
slab).The thin slab is delivered directly to roughing mill 20 and is rolled as a continuous process, therefore can directly utilize steel billet certainly
The heat of body, such that it is able to energy saving, and by these processes, the formation that can occur in continuous casting and rough rolling process is micro-
The transition process of tissue and precipitate becomes different in existing rolling mill practice, and final obtained steel plate mechanical property can change.Separately
On the one hand, difference of the thickness of the thin slab with existing rolling mill practice if more than 150mm diminishes, and is cast if less than 30mm
Base temperature can drastically decline, it is difficult to form uniform tissue.To solve the problem, firing equipment, but this meeting can be set in addition
Cause production cost to rise, therefore preferably do not use as far as possible.
In addition, thin slab is rolled into desired final thickness in roughing mill 20 and finishing mill 50, and by runout table
(R0T) after 60 coolings, batched with uniform temperature in coiling machine 70, so as to be manufactured into steel plate.The present invention is as described above, its feature exists
It is identical in the actuating speed of roughing mill 20- finishing mill 50- coiling machines 70 is controlled into, so as at the uniform velocity be rolled, when continuous casting speed
When degree and mill speed have differences, to compensate the difference, Coil Box (coil box) 40 can be set before finishing mill 50,
Thus batten (bar plate) b by sensing heater 30 is once batched.
Firstly, for obtain the continuous casting step of the thin slab, after the molten steel for meeting the alloy component is prepared, will
Casting speed is set as more than 4.5mpm (miter per minute), is preferably set to 4.5~7.5mpm.Because casting
It is carried out continuously with the operation of rolling, to ensure that target rolling temperature then needs the casting speed more than to a certain degree, is cast for this
Speed is preferably in more than 4.5mpm.But, during more than 7.5mpm, operation success rate can be reduced because the liquid level of molten steel is unstable,
Therefore the casting speed is preferably in the range of 4.5~7.5mpm.
The thin slab obtained by the casting will be by roughing step, and the roughing to thin slab is by by 2~4
The roughing mill 20 of individual rolling machine frame composition is realized.Now, in the entrance side of the roughing mill, the surface temperature of thin slab is excellent
Elect 1000~1200 DEG C as.If the surface temperature of the thin slab is less than 1000 DEG C, roughing load can be caused to increase and thick
Can be cracked in batten edge part during rolling, this can cause the defect of hot rolled steel plate edge part.On the other hand, the thin steel
When the surface temperature of base is more than 1200 DEG C, it may occur that such as hot rolling surface matter caused by the hot rolling oxide skin (scale) of residual
Measure the problem for reducing.
In addition, when carrying out the roughing, accumulation reduction ratio is preferably 60~90%, this is conducive to conduct in the manufacture present invention
The hot rolled steel plate with excellent material deviation of target.Roughing reduction ratio gets over Gao Yueneng to be made to be formed in continuous-cast blank (thin slab)
Internal continuous casting microscopic structure and alloying component is uniformly distributed, and to realize this effect, the accumulation reduction ratio is preferably 60%
More than.But, during more than 90%, rolling deformation resistance becomes big and causes operationally to become difficult, therefore carries out the roughing
When, accumulation reduction ratio is preferably in the range of 60~90%.
In finish rolling step, the batten obtained by the roughing is rolled in the range of 200~600mpm, it is excellent
Carried out at a temperature of being selected in less than existing rolling mill practice.The rolling is preferably carried out under certain speed.As described above, by rolling
System can control into identical mass flow (mass flow) from continuous casting to coiling technique.But, if mill speed is excessively slow,
The temperature of the hot rolled steel plate of rolling is then difficult to ensure that, operating trouble such as maloperation can occur in controlled rolling if too fast leads
The broken belt of cause, it is difficult to which hot-rolled temperature is controlled into desired value.
In addition, the reasons why final rolling temperature is set below into i.e. less than 880 DEG C of existing rolling mill practice temperature is, of the invention
Strand is solidified completely in the range of casting speed, avoid rolling not solidified strand as far as possible, so as to improve endless rolling operation
Stability, and the hot rolling scale defects that can be produced when reducing high temperature finish rolling as far as possible.In addition, also have being increased by zerolling
The ratio of the austenite phase of non-recrystallization makes the effect of crystal grain refinement.But, when the hot-rolled temperature is less than 780 DEG C, it may occur that
Operating trouble such as hot rolling load sharply increases caused broken belt, therefore the hot rolling is preferably carried out at 780~880 DEG C.
Then, the hot rolled steel plate now cools down speed preferably in runout table (R0T) continuous coo1ing to target coiling temperature
In the normal ranges that degree can be in the art.The cooling is carried out to 500~650 DEG C, and in the temperature range
Batched, when the coiling temperature is less than 500 DEG C, the ferritic phase of irregular shape can be formed, thus increased microscopic structure
Inhomogeneities, and during more than 650 DEG C, because the formation of pearlite can cause bendability to be deteriorated.Therefore, the coiling temperature is preferred
In the range of 500~650 DEG C, for the stability of the microscopic structure to be obtained of the invention, preferably at 580~650 DEG C
In the range of.
The step of batching rear pickled hot steel plate described in can further including, can be removed by the step and be formed in hot rolling
The oxide skin of surface of steel plate.The acid cleaning process can be using all conventional methods in the art.
After the acid pickling step is carried out, the hot rolled steel plate is heated to 450~550 DEG C, and with continuous technique
It is introduced to molten zinc plating groove to be electroplated, constant temperature heat treatment is then carried out at 500~560 DEG C, so as to melting can also be manufactured into
Zinc-plated hot rolled steel plate.When the heating-up temperature is less than 450 DEG C, because insufficient heating can cause plating defects (spot (Tears
Mark)) frequency is produced to rise, and during more than 550 DEG C, because the shade deviation for electroplating layer surface can cause plate surface defect.Separately
Outward, constant temperature heat treatment be in order to realize alloying element be uniformly distributed and electrodeposited coating alloying, temperature is less than 500 DEG C
When, it is difficult to the effect is obtained, and electrodeposited coating surface defect such as ripple mark can occur, and during more than 560 DEG C, in substrate steel/electricity
The Fe-Zn alloyings that plating interface is neighbouring, substrate steel interface occurs can be uneven, so as to cause what electrodeposited coating color and luster had differences
Problem.
Below, embodiments of the invention are described in detail.But, following embodiments are merely to illustrate the present invention, are not to use
In the limitation present invention.
(embodiment)
Prepare the molten steel A~J with the component (weight %, balance of Fe and inevitable impurity) in table 1 below it
Afterwards, the thin slab that high-speed continuous casting is made 80 ㎜ is carried out with the speed of 5mpm, the roughing mill 20- finishing mills 50- shown in Fig. 1 is batched
The actuating speed of machine 70 controls into identical speed and carries out equal speed rolling.By finish rolling outlet side temperature (FDT) of appropriate table 2, volume
The method for taking temperature (CT) etc. has manufactured hot rolled steel plate.
But, the K steel grades in table 1 below and 2 are not to use endless rolling, but are reheated and hot rolling by conventional steel billet
Technique manufacture.
【Table 1】
In the table 1, Tr. is the total content of extraneous element Cu, Cr, Ni, Mo and Sn, and formula 1 is atomic molar ratio, is represented
The value of [(B/N) * (C/P) * 100].
For manufactured hot rolled steel plate, the mechanical property using ASTM sample tests, the results are shown in table 2 below.Separately
Outward, the ferrite grain size (FGS) of hot rolled steel plate is measured, and Surface Quality is evaluated, the results are shown in table 2
In.When surface quality is evaluated, after removing surface scale, surface gloss is evaluated.Zero represents surface gloss
It is that 60~70, △ represents that surface gloss is less than 60.
【Table 2】
As described shown in table 2, meeting the example of component of the invention and condition has the yield strength of more than 260MPa
And with more than 30% elongation.Furthermore, it is possible to ensure excellent surface quality.
On the other hand, its component of comparative example 1 to 4 is beyond the scope of this invention, even if meeting process conditions of the invention, table
Face quality or poor.
Comparative example 5 and 6 is component and the situation beyond the scope of this invention of relational expression 1, although crystal grain can be refined, but table
Face is of poor quality.In addition, comparative example 7 and 8 is the situation beyond the scope of this invention of relational expression 1, crystallite dimension is thick and surface matter
Amount is poor.Comparative example 9 does not meet component of the invention, yield strength not up to of the presently claimed invention and coarse grains.
Additionally, Fig. 2 is the chart of the ferrite crystal grain distribution for showing the example 1.It can be seen from Fig. 2, the invention
Its ferrite average grain size (FGS) of example 1 is less than 12 μm, and deviation is less than 7 μm.
Claims (8)
1. the excellent high tensile hot rolled steel sheet of a kind of surface quality, its by weight percentage comprising 0.02~0.06% C,
0.1~1.0% Mn, 0.0001~0.5% Si, 0.01~0.04% Al, 0.001~0.05% P, 0.001~
0.006% S, 0.0001~0.002% B, 0.001~0.015% N, and be selected from comprising 0.0001~0.18%
One or more of Cu, Cr, Ni, Mo and Sn element, balance of Fe and inevitable impurity,
Wherein, described C, B, N and P meet relationship below 1,
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are value of the respective percentage by weight divided by respective atomic weight,
The high tensile hot rolled steel sheet with ferrite as Main Tissues, and comprising one or more of cementite and pearlite, its
Area fraction is less than 5%,
And the ferrite grain size is less than 12 μm.
2. the excellent high tensile hot rolled steel sheet of surface quality according to claim 1, its thickness is 1.2~2.8 ㎜.
3. a kind of manufacture method of the excellent high tensile hot rolled steel sheet of surface quality, comprises the following steps：
Prepare molten steel, the molten steel by weight percentage comprising 0.02~0.06% C, 0.1~1.0% Mn, 0.0001~
0.5% Si, 0.01~0.04% Al, 0.001~0.05% P, 0.001~0.006% S, 0.0001~0.002%
B, 0.001~0.015% N, and comprising 0.0001~0.18% selected from one or more of Cu, Cr, Ni, Mo and Sn
Element, balance of Fe and inevitable impurity, described C, B, N and P meet relationship below 1；
The molten steel is casting continuously to form thin slab with the speed of more than 4.5mpm；
Roughing is carried out to the thin slab, to obtain batten；
Finish rolling is carried out with the speed of 200~600mpm and at a temperature of 780~880 DEG C to the batten, to obtain hot-rolled steel
Plate；
The hot rolled steel plate is cooled to 500~650 DEG C；And
The hot rolled steel plate of the cooling is batched,
[relational expression 1]
5≤[(B/N)*(C/P)*100]≤300
In relational expression 1, B, N, C and P are value of the respective percentage by weight divided by respective atomic weight.
4. the manufacture method of the excellent high tensile hot rolled steel sheet of surface quality according to claim 3, wherein,
The thickness of the thin slab is 30~150 ㎜.
5. the manufacture method of the excellent high tensile hot rolled steel sheet of surface quality according to claim 3, wherein,
The accumulation reduction ratio of the roughing is 60~90%.
6. the manufacture method of the excellent high tensile hot rolled steel sheet of surface quality according to claim 3, wherein,
During the roughing, the feeding temperature of thin slab is 1000~1200 DEG C.
7. the manufacture method of the excellent high tensile hot rolled steel sheet of surface quality according to claim 3, further include with
Lower step：
It is described batch after, hot rolled steel plate described in pickling.
8. the manufacture method of the excellent high tensile hot rolled steel sheet of surface quality according to claim 7, further include with
Lower step：
After the pickling, the hot rolled steel plate is heated to 450~550 DEG C；
Molten zinc plating is carried out to the heated hot rolled steel plate；And
Hot rolled steel plate to the molten zinc plating at 500~560 DEG C carries out constant temperature treatment.
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| KR101664098B1 (en) * | 2015-09-01 | 2016-10-10 | 주식회사 포스코 | Hot rolled steel sheet for pressure vessel, and the method of manufacturing the same |
| KR101767773B1 (en) * | 2015-12-23 | 2017-08-14 | 주식회사 포스코 | Utlra high strength hot-rolled steel sheet having excellent ductility and method of manufacturing the same |
| MX2019004706A (en) * | 2017-08-31 | 2019-06-06 | Nippon Steel Corp | Steel sheet for carburization, and production method for steel sheet for carburization. |
| KR102109240B1 (en) * | 2017-12-24 | 2020-05-11 | 주식회사 포스코 | Hot-rolled steel sheet for non-oriented electrical steel sheet, non-oriented electrical steel sheet and method for manufacturing the same |
| KR101999030B1 (en) * | 2017-12-26 | 2019-10-01 | 주식회사 포스코 | Ultra thin hot rolled steel sheet having excellent isotropic properties and method of manufacturing the same |
| KR102045653B1 (en) * | 2017-12-26 | 2019-11-15 | 주식회사 포스코 | Non-oriented electrical steel sheet having low deviation of mechanical property and thickness and method of manufacturing the same |
| CN110042309A (en) * | 2019-05-07 | 2019-07-23 | 南京钢铁股份有限公司 | A kind of production method improving wide surface of thin steel sheet quality |
| CN112522590A (en) * | 2019-09-19 | 2021-03-19 | 宝山钢铁股份有限公司 | High-strength and high-corrosion-resistance steel and manufacturing method thereof |
| CN114737037B (en) * | 2022-03-30 | 2023-06-27 | 马鞍山钢铁股份有限公司 | 550 MPa-grade high-plastic-toughness hot-dip galvanized steel plate based on CSP process and production method thereof |
| CN115198221B (en) * | 2022-07-22 | 2024-02-02 | 燕山大学 | Device for automatic spraying and hot rolling of composite plate strip interlayer and processing method thereof |
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