CN109112433B - 590 MPa-grade cold-rolled dual-phase steel without surface stripe defects and production method thereof - Google Patents
590 MPa-grade cold-rolled dual-phase steel without surface stripe defects and production method thereof Download PDFInfo
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 29
- 230000007547 defect Effects 0.000 title claims abstract description 12
- 229910000885 Dual-phase steel Inorganic materials 0.000 title abstract description 9
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 79
- 239000010959 steel Substances 0.000 claims abstract description 79
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- 238000005554 pickling Methods 0.000 claims abstract description 19
- 238000000137 annealing Methods 0.000 claims abstract description 14
- 238000009749 continuous casting Methods 0.000 claims abstract description 14
- 238000001816 cooling Methods 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 13
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000002791 soaking Methods 0.000 claims description 9
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 230000033764 rhythmic process Effects 0.000 claims description 2
- 238000010583 slow cooling Methods 0.000 claims description 2
- 239000002253 acid Substances 0.000 abstract description 2
- 230000000052 comparative effect Effects 0.000 description 14
- 230000000694 effects Effects 0.000 description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 238000000034 method Methods 0.000 description 10
- 238000005097 cold rolling Methods 0.000 description 9
- 239000011248 coating agent Substances 0.000 description 7
- 238000000576 coating method Methods 0.000 description 7
- 229910000734 martensite Inorganic materials 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 7
- 229910000859 α-Fe Inorganic materials 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 238000012876 topography Methods 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007613 environmental effect Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 150000001721 carbon Chemical class 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910005331 FeSi2 Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005282 brightening Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000003034 coal gas Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000010813 municipal solid waste Substances 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 238000012802 pre-warming Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/001—Austenite
-
- 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
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
Abstract
The invention provides 590 MPa-grade cold-rolled dual-phase steel without surface stripe defects and a production method thereof, wherein the steel plate comprises the following components in percentage by weight: c: 0.050% -0.100%, Si: less than or equal to 0.25 percent, Mn: 1.20% -2.00%, P: less than or equal to 0.012%, S: less than or equal to 0.008 percent, Al: 0.05-0.10%, Sb: 0.015-0.050%, and the balance of Fe and other inevitable impurities; the production method comprises smelting, continuous casting, hot charging and heating, high-pressure water descaling and rough rolling, finish rolling, laminar cooling, coiling, hot rolled plate acid pickling cold continuous rolling, continuous annealing, air cooling and leveling coiling.
Description
Technical field
The invention belongs to cold rolling high-strength steel production fields, more particularly to 590MPa grade cold rolling of the kind without striated surface defect
Dual phase steel and its production method.
Background technique
Environment, the energy and driver and passenger's personal safety requirement, Hyundai Motor should lightweight, safety and environmental protection and low cost systems
It makes, and realizes that the major measure of this requirement is exactly largely to use advanced high-strength steel in body of a motor car manufacture.Advanced high-strength steel-
The advantages that dual phase steel (DP steel) is with its low yield strength ratio, good obdurability, has been widely used on automotive light weight technology white body.Mesh
Before, cold-rolled biphase steel covers 450MPa~1180MPa intensity rank range, the mainly 980MPa of commercial steady production
Grade and following intensity rank, wherein use ratio of the 590MPa grades of cold-rolled biphase steels in automobile manufacture is maximum, is mainly used in
The reinforcer and structural member of automobile.On the anneling production line of CAL (air cooling line) type of cooling, the 590MPa grade cold rolling of production is double
It needs to add a certain amount of Si alloying element in phase composition of steel, to guarantee the solid solution strengthening effect and elongation after fracture of steel plate, however
When Si content is higher in steel, slab is easy to generate FeSi2O4 during heating between iron scale and matrix, and iron sheet is secured
It being sticky on matrix, the de-scaling difficulty before increasing roughing and finish rolling is easy to be pressed into steel matrix during subsequent hot rolled, thus
Cause surface of steel plate after pickling and cold-rolling linear strip flaw occur, influences steel plate phosphatization effect, weaken the durable of components coating
Property, corrosion resistance, reduce the service life of automobile.
Summary of the invention
A kind of 590MPa grade of no striated surface defect is provided it is an object of the invention to overcome the above problem and deficiency
Cold-rolled biphase steel and its production method improve automobile cold-rolled dual phase steel surface quality, and obtain meeting structure property and coating
It is required that 590MPa grades of cold-rolled biphase steel plates of automobile.
The object of the present invention is achieved like this:
A kind of 590MPa grades of cold-rolled biphase steels of no striated surface defect, the ingredient of the steel plate are as follows by weight percentage:
C:0.050%~0.100%, Si :≤0.25%, Mn:1.20%~2.00%, P :≤0.012%, S :≤0.008%, Al:
0.05%~0.10%, Sb:0.015~0.050%, surplus are Fe and some other inevitable impurity.
Preferably, the ingredient of the steel plate is as follows by weight percentage: C:0.075%~0.095%, Si :≤
0.15%, Mn:1.50%~1.90%, P :≤0.010%, S :≤0.006%, Al:0.070%~0.085%, Sb:
0.025~0.035%, surplus is Fe and some other inevitable impurity.
It is as follows that present component designs reason:
C: being most effective intensified element, is the essential element to form martensite, directly affects two-phase after the processing of critical zone
Carbon content in steel in Martensite Volume Fraction and martensite.To guarantee that steel has the intensity applied and good elongation, this
Carbon content control is 0.050%~0.100%, more preferable 0.075%~0.095% in invention.
Si: being the element of reinforced ferrite, promotes carbon to austenite segregation, has removing and purification to carbon is dissolved in ferrite
Effect, the generation of coarse carbide, helps to improve the ductility of dual phase steel, but to keep away when to avoid gap solution strengthening and cooling
Exempting from Si too high levels causes surface of steel plate to generate red rust, and excessive FeSi2O4 is generated after preventing slab from heating, and reduces steel plate de-scaling
Effect.Si control of the present invention is 0.25% hereinafter, more preferably no more than 0.15%.
Mn: belonging to the element for expanding austenite phase field, can effectively improve the harden ability of austenite, can reduce martensite and turn
The critical cooling rate of change, and play the role of solution strengthening and fining ferrite grains.High Mn content easily cause cementite,
Banded structure based on pearlite and bainite influences the coating and service performance of steel plate.Mn content control of the present invention exists
1.20%~2.00%, more preferable 1.50%~1.90%.
P, S: for the harmful element in steel.Segregation causes embrittlement to P easily on crystal boundary, makes deterioration of impact resistance, and to spot welding
It is unfavorable.S easily forms the field trashes such as MnS in steel, thermally-induced hot-short, and P in the present invention, S content is controlled respectively in 0.012% He
0.008% hereinafter, more preferable 0.010% and 0.006% or less.
Effect of the Al:Al played in dual phase steel is similar to Si, while Al can also form AlN precipitation, play certain
Grain refinement.Since silicone content is low in steel of the present invention, the presence of a small amount of aluminium can mention under the premise of proof strength
The ductility of high dual phase steel, while Al is main deoxidier, it is unsuitable too low, but excessive tufted aluminium oxide inclusion increases, and makes
The ductility of steel is deteriorated, and will affect steel-making and continuous casting, and Al content control is more excellent 0.05%~0.10% in the present invention
Select 0.070%~0.085%.
Sb: being a kind of low melting point element, can improve molten steel flow, hinders carbon atom diffusion, hence it is evident that promotes and stablize pearl
Body of light is formed, and improves matrix hardness, while steel matrix can be inhibited to be corroded, and enrichment of the Sb on MnS field trash is precipitated, energy
The formation for promoting Intragranular Acicular Ferrite in steel is conducive to the plasticity for improving dual phase steel.Sb content of the present invention control 0.015~
0.050%, more preferable 0.025~0.035%.
A kind of production method of no 590MPa grades of cold-rolled biphase steels of striated surface defect, including smelting, continuous casting, hot charging add
Heat high-pressure water descaling and roughing, finish rolling, section cooling, is batched, hot rolled plate pickling cold continuous rolling, continuous annealing, air-cooled, smooth volume
It takes,
(1) hot charging is heated: by the continuous casting billet direct hot charging hot sending to heating furnace of 170mm thickness, steel slab temperature is greater than
850 DEG C, 900~1000 DEG C of preheating section furnace gas temperature, 20~30min of preheating time, carry out high temperature rapidly pre-warming；Bringing-up section temperature
Degree is 1230~1270 DEG C, 15~25min of heating time, and soaking section temperature is 1230~1270 DEG C, soaking zone soaking time 70
~90min ensure that slab in FeSi2O4It more than melting temperature comes out of the stove, guarantees good scale removal effect.Continuous casting billet preheating time
It is amounted between 105~145min with soaking zone heat preservation, furnace pressure is in slight positive pressure state always in dynamic, is effectively reduced
Oxidization burning loss and oxidated layer thickness, while coal gas and power consumption are also saved, reduce manufacturing cost；
(2) high-pressure water descaling and roughing: after continuous casting billet exports burner hearth, rolling rhythm control rolls one block of steel in 1~2min
Base, high-pressure water descaling 4-6 passage, increases the de-scaling time, ensure that high-pressure water descaling rate per pass, and nozzle exit pressure is
19MPa~21MPa；Enhance scale removal effect；
Slab rough rolling fixed width side pressure 2-3 times, effectively mechanical scale breading effect is played, lateral pressure amount total amount is 250~300mm, is entered
Intermediate base with a thickness of 55~65mm before finish rolling；Prevent the iron scale for floating on billet surface and individual leakages except point iron scale
Too deep roll compacting is to steel matrix, and scale removal effect again before being conducive to finish rolling ensure that the surface quality of steel plate.
(3) finish rolling start rolling temperature is 1050~1150 DEG C, and finishing temperature is 890~950 DEG C, using leading portion section cooling,
600~650 DEG C of coiling temperature, hot rolled plate with a thickness of 2.5mm~5.0mm after rolling；
(4) hot rolled plate pickling cold continuous rolling: using turbulent chlorohydric acid pickling, concentration of hydrochloric acid is 15%~25%, and pickling temperature is
90 DEG C~95 DEG C, strip straightening and the speed of service are 50~70m/min, chill plate with a thickness of 0.8~2.3mm after rolling；Have
Effect improves strip pickling speed and effect, straightening strip to Mechanical Crushing oxide layer, strip speed control 50~
Between 70m/min, the pickling effect of strip is further increased.
(5) continuous annealing: steel band is 770~830 DEG C in the soaking temperature of annealing furnace, and slow cooling temperature is 650-700 DEG C, fastly
After cold and overaging temperature is 260~290 DEG C；It is air-cooled after timeliness, smooth to batch, ensure that steel plate finally organize as ferrite and
Martensite, for martensite with island Dispersed precipitate on ferrite matrix, the mechanical property of steel plate reaches 590MPa grades of cold rolling two-phases
The standard requirements of steel.
The present invention is directed to utilize medium thin slab continuous casting and rolling production line, pass through technological parameter in heating of plate blank and hot rolling stage
Effective control and cold-rolling pickling process control and pickling solution proportion change, meanwhile, by adding Sb using low Si to composition of steel
Processing improves slab quality, realizes the grade cold-rolled biphase steel surface 590MPa produced on CAL annealed wire without strip flaw, steel
Plate surface is bright, improves with the phosphatization effect of its auto parts and components manufacture and coating adhesion, extends automobile and use year
Limit.
The beneficial effects of the present invention are: using the present invention in medium thin slab continuous casting and rolling production line and the CAL type of cooling
Continuous annealing production line on, the 590MPa grade cold-rolled biphase steel surface-brightening of production, no strip flaw, and have it is good resistance to
Corrosion energy and coating adhesion, the good mechanical performance of steel plate, meeting Hyundai Motor should lightweight, safety and environmental protection and low cost
Manufacture requires.
Detailed description of the invention
Fig. 1 is the surface topography after 1 hot rolled plate pickling of embodiment.
Fig. 2 is the surface topography compared after 1 hot rolled plate pickling.
Fig. 3 is the surface topography of 1 continuous annealing production board of embodiment.
Fig. 4 is the surface topography of 1 continuous annealing production board of comparative example.
Specific embodiment
Below by embodiment, the present invention is further illustrated.
The embodiment of the present invention is smelted, continuous casting, hot charging heating, high-pressure water descaling according to the component proportion of technical solution
And it roughing, finish rolling, section cooling, batches, hot rolled plate pickling cold continuous rolling, continuous annealing.The ingredient of steel of the embodiment of the present invention is shown in Table
1.The heating technique parameter of the embodiment of the present invention and comparative example steel is shown in Table 2.The de-scaling of the embodiment of the present invention and comparative example steel and thick
Roll process parameter is shown in Table 3.The embodiment of the present invention and the finish rolling of comparative example steel and pickling continuous cold rolling process parameter are shown in Table 4.The present invention is real
It applies example and comparative example steel continuous annealing process parameter is shown in Table 5.Performance, the surface quality of the embodiment of the present invention and comparative example steel steel plate
It is shown in Table 6.
The ingredient (wt%) of 1 steel of the embodiment of the present invention of table
| Embodiment | C | Si | Mn | P | S | Al | Sb |
| Example 1 | 0.095 | 0.20 | 1.85 | 0.010 | 0.006 | 0.087 | 0.045 |
| Example 2 | 0.085 | 0.18 | 1.70 | 0.009 | 0.005 | 0.070 | 0.030 |
| Example 3 | 0.060 | 0.12 | 1.50 | 0.007 | 0.006 | 0.080 | 0.020 |
| Comparative example 1 | 0.080 | 0.50 | 1.75 | 0.010 | 0.006 | 0.085 | — |
| Comparative example 2 | 0.070 | 0.60 | 1.65 | 0.008 | 0.005 | 0.080 | — |
Note: surplus is Fe and inevitable trace impurity
The heating technique parameter of table 2 embodiment of the present invention and comparative example steel
The de-scaling of 3 embodiment of the present invention of table and comparative example steel and roughing technological parameter
4 embodiment of the present invention of table and the finish rolling of comparative example steel and pickling continuous cold rolling process parameter
5 embodiment of the present invention of table and comparative example steel continuous annealing process parameter
Performance, the surface quality of 6 embodiment of the present invention of table and comparative example steel steel plate
By a kind of production method production of the 590MPa grade cold-rolled biphase steel of no striated surface defect provided by the invention
Comparative example 2, surface of steel plate strip flaw is substantially reduced, and surface of steel plate is dim, and the structure property index of steel plate reaches standard
It is required that.Without the 590MPa grade cold-rolled biphase steel obtained using production method provided by the invention, i.e. embodiment 1, surface has not
With the strip flaw of degree, surface of steel plate is light bright or dim, influences the phosphatization effect and coating adhesion of steel plate, and steel plate makes
It is poor with performance.
Steel embodiment of the present invention is through smelting continuous casting, according to the heating of plate blank of setting, de-scaling and roughing technique and finish rolling and acid
Continuous cold rolling process is washed, on the continuous annealing production line of the CAL type of cooling, the 590MPa grade with a thickness of 0.8~2.3mm of production
Cold-rolled biphase steel surface does not have strip flaw, and surface of steel plate is bright, and has good corrosion resisting property and coating adhesion, steel plate
Microscopic structure is made of ferrite and martensite, tensile strength be greater than 590MPa, elongation percentage is more than 23.5%, intensity with prolong
Property matching it is good, can apply on the reinforcer and structural member of automobile, meet Hyundai Motor should lightweight, safety and environmental protection and
Low cost manufacturing requirement.
Claims (3)
1. a kind of 590MPa grade cold-rolled biphase steel of no striated surface defect, which is characterized in that the ingredient of steel percentage by weight
It is as follows than counting: C:0.050%~0.100%, Si :≤0.25%, Mn:1.20%~2.00%, P :≤0.012%, S :≤
0.008%, Al:0.05%~0.10%, Sb:0.015~0.050%, surplus are Fe and some other inevitable impurity；
The production method of the 590MPa grade cold-rolled biphase steel of the no striated surface defect, including smelting, continuous casting, hot charging heating, high pressure
Water de-scaling and roughing, finish rolling, section cooling, batch, hot rolled plate pickling cold continuous rolling, continuous annealing, it is air-cooled, smooth batch,
(1) hot charging is heated: in the hot sending to heating furnace of continuous casting billet direct hot charging, steel slab temperature is greater than 850 DEG C, preheating section furnace gas
900 DEG C~1000 DEG C of temperature, preheating time 20min~30min, bringing-up section temperature is 1230 DEG C~1270 DEG C, heating time
15min~25min, soaking section temperature are 1230 DEG C~1270 DEG C, and soaking zone soaking time 70min~90min, furnace pressure exists
Always slight positive pressure state is in dynamic；
(2) high-pressure water descaling and roughing: after continuous casting billet exports burner hearth, rolling rhythm control rolls one block of steel in 1min~2min
Base, high-pressure water descaling 4-6 passage, nozzle exit pressure are 19MPa~21MPa；
(3) use leading portion section cooling, 600 DEG C~650 DEG C of coiling temperature, after rolling hot rolled plate with a thickness of 2.5mm~
5.0mm；
(4) hot rolled plate pickling cold continuous rolling: using turbulent chlorohydric acid pickling, concentration of hydrochloric acid is 15%~25%, and pickling temperature is 80 DEG C
~95 DEG C, strip straightening and the speed of service are 50~70m/min；
(5) continuous annealing: steel band is 770 DEG C~830 DEG C in the soaking temperature of annealing furnace, and slow cooling temperature is 650 DEG C -700 DEG C, fastly
After cold and overaging temperature is 260 DEG C~290 DEG C.
2. the 590MPa grade cold-rolled biphase steel of a kind of no striated surface defect according to claim 1, which is characterized in that the steel
Ingredient it is as follows by weight percentage: C:0.075%~0.095%, Si :≤0.15%, Mn:1.50%~1.90%, P:
≤ 0.010%, S :≤0.006%, Al:0.070%~0.085%, Sb:0.025~0.035%, surplus are Fe and other one
A little inevitable impurity.
3. the 590MPa grade cold-rolled biphase steel of a kind of no striated surface defect according to claim 1, it is characterised in that: described
(2) continuous casting billet roughing fixed width side pressure 2-3 times in, lateral pressure amount total amount are 250mm~300mm, enter intermediate base before finish rolling with a thickness of
55mm~65mm.
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| CN109576591B (en) * | 2019-02-12 | 2020-03-31 | 鞍钢股份有限公司 | 700 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
| CN109628840B (en) * | 2019-02-12 | 2020-03-31 | 鞍钢股份有限公司 | 550 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
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