CN108486494B - Production method of vanadium microalloyed 1300MPa grade high-strength hot-rolled steel sheet and cold-rolled dual-phase steel sheet - Google Patents
Production method of vanadium microalloyed 1300MPa grade high-strength hot-rolled steel sheet and cold-rolled dual-phase steel sheet Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 67
- 239000010959 steel Substances 0.000 title claims abstract description 67
- 229910052720 vanadium Inorganic materials 0.000 title claims abstract description 21
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 title claims abstract description 19
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 17
- 238000001816 cooling Methods 0.000 claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 31
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 17
- 239000010960 cold rolled steel Substances 0.000 claims abstract description 15
- 238000003723 Smelting Methods 0.000 claims abstract description 9
- 238000005554 pickling Methods 0.000 claims abstract description 6
- 238000001556 precipitation Methods 0.000 claims abstract description 6
- 238000007711 solidification Methods 0.000 claims abstract description 6
- 230000008023 solidification Effects 0.000 claims abstract description 6
- 238000005728 strengthening Methods 0.000 claims abstract 3
- 238000005096 rolling process Methods 0.000 claims description 22
- 238000000137 annealing Methods 0.000 claims description 21
- 238000005097 cold rolling Methods 0.000 claims description 18
- 230000008569 process Effects 0.000 claims description 11
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 claims description 7
- 229910001566 austenite Inorganic materials 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 7
- 229910052796 boron Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- 229910001563 bainite Inorganic materials 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims 2
- 239000000203 mixture Substances 0.000 claims 2
- 238000004512 die casting Methods 0.000 claims 1
- 238000005098 hot rolling Methods 0.000 abstract description 13
- 238000005266 casting Methods 0.000 abstract description 8
- 239000002245 particle Substances 0.000 abstract description 7
- 238000002360 preparation method Methods 0.000 abstract description 7
- 230000009466 transformation Effects 0.000 abstract 1
- 229910000859 α-Fe Inorganic materials 0.000 description 10
- 238000005275 alloying Methods 0.000 description 8
- 238000004321 preservation Methods 0.000 description 8
- 230000015572 biosynthetic process Effects 0.000 description 5
- 230000009977 dual effect Effects 0.000 description 5
- 238000002791 soaking Methods 0.000 description 5
- 238000001000 micrograph Methods 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 239000004615 ingredient Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 238000010583 slow cooling Methods 0.000 description 2
- 206010054949 Metaplasia Diseases 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000000635 electron micrograph Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 239000003344 environmental pollutant Substances 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000015689 metaplastic ossification Effects 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 231100000719 pollutant Toxicity 0.000 description 1
- 235000015170 shellfish Nutrition 0.000 description 1
- 239000002689 soil Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005482 strain hardening 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
-
- 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
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
本发明公开了一种钒微合金化1300MPa级别高强热轧钢板和冷轧双相钢板的生产方法，用于解决现有方法制备的双相钢板强度不足的技术问题。技术方案是通过钢的冶炼与凝固、铸坯或铸锭开坯后的热连轧和控制冷却获得1300MPa级别高强热轧钢板，以及在热连轧某温度卷取后，经酸洗和室温冷轧至1‑3mm厚，然后在720‑780℃两相区某一温度短时保温立即淬火，制得钒微合金化1300MPa级别高强双相冷轧钢板。该制备工艺将纳米碳化钒粒子析出强化与马氏体相变强化相结合，显著提高了现有双相钢的强度，同时还保证了较高的生产效率。
The invention discloses a production method of vanadium microalloyed 1300MPa grade high-strength hot-rolled steel sheet and cold-rolled dual-phase steel sheet, which is used to solve the technical problem of insufficient strength of the dual-phase steel sheet prepared by the existing method. The technical solution is to obtain a 1300MPa high-strength hot-rolled steel sheet through smelting and solidification of steel, hot rolling and controlled cooling after casting or ingot opening, and after hot rolling at a certain temperature, pickling and room temperature cooling. Rolled to a thickness of 1-3mm, and then quenched immediately at a temperature of 720-780°C in the two-phase region for a short time to obtain a vanadium microalloyed 1300MPa grade high-strength dual-phase cold-rolled steel plate. The preparation process combines the precipitation strengthening of the nano-vanadium carbide particles with the martensitic transformation strengthening, which significantly improves the strength of the existing dual-phase steel and also ensures high production efficiency.
Description
Technical field
The present invention relates to a kind of preparation method of dual phase sheet steel, in particular to a kind of vanadium micro-alloying 1300MPa rank is high
The production method of heat-flash rolled steel plate and cold-rolled biphase steel plate.
Background technique
High-strength and high-plasticity material is pursued by material worker always, and current automobile steel industry field is faced with product
The demand that can be promoted guarantees safety, while requiring the exploitation of body lightening and novel process to reduce energy consumption standard and reduce
Pollutant emission, and then meet corresponding energy-saving and environment-friendly social regulation.In recent years, two-phase (martensite+ferrite) steel is opened
Hair meets the performance requirement of automobile steel under the premise of low cost well, is widely applied.
All the time, the mechanical property of dual phase steel relies primarily on martensite and provides intensity, and ferrite provides plasticity, at present most
High intensity levels are the DP1180 trade mark, and tensile strength is about 1200MPa, and yield strength is about 750MPa, and breaking elongation is about
10% (data source: DP1180 dual phase steel strain hardening behavior and mechanism under high strain rate deformation condition；Acta Metallurgica Sinica；
2012 (48): 1160-1160).Melting, forging, hot rolling, cold rolling, two-phase section annealing, quenching etc. are mainly passed through in the preparation of dual phase steel
Process flow.Compared to the second generation, the advanced high-strength automobile steel of the third generation, dual phase steel is because its production cost is low and function admirable
Feature is the Typical Representative of the advanced high-strength automobile steel of the first generation.The production technology of cold-rolled biphase steel is cold continuous rolling and continuously moves back
Fire process, tensile strength are determined that the more high then tensile strength of martensite fractions is about high by the martensite fractions in annealed structure,
This requires high strength martensitic steel to need to use higher annealing temperature to form more martensite fractions, but institute can quotient at present
The dual phase steel maximum intensity grade that industry metaplasia produces is 1180MPa, i.e. 1180 steel of DP.
Summary of the invention
Dual phase sheet steel intensity in order to overcome the problems, such as existing method preparation is insufficient, and the present invention provides a kind of vanadium micro-alloying
The production method of 1300MPa grade high-strength hot rolled steel plate and cold-rolled biphase steel plate.The smelting and solidification, slab that this method passes through steel
Or the hot continuous rolling after ingot formation and control cooling obtain 1300MPa grade high-strength hot rolled steel plate, and in hot continuous rolling temperature
After batching, through pickling and cold rolling at room temperature to 1-3mm thickness, then quench immediately in a certain temperature isothermal treatment for short time of 720-780 DEG C of two-phase section
Vanadium micro-alloying 1300MPa grade high-strength two-phase cold-rolled steel sheet is made in fire.The preparation process nano vanadium carbide particle is precipitated strong
Change in conjunction with martensitic traoformation hardening constituent, significantly improve the intensity of existing dual phase steel, while also assuring higher production effect
Rate.
A kind of the technical solution adopted by the present invention to solve the technical problems: vanadium micro-alloying 1300MPa grade high-strength heat
The production method of rolled steel plate and cold-rolled biphase steel plate, its main feature is that the following steps are included:
(1) it the smelting and solidification of steel: by converter, electric furnace or induction furnace steel-smelting, is given birth to using continuous casting slab or molding
Produce ingot casting；
(2) hot continuous rolling after slab or ingot formation: slab or ingot casting are heated through 1100-1250 DEG C, by roughing mill into
Row 5-20 passes, hot rolling carry out 5-7 passes to 4-15mm, finish to gauge to 40-80mm thickness specification, then by heat even unit
Temperature is controlled at 800~850 DEG C
(3) it is divided to two kinds of types of cooling after finish to gauge, first is that it is cooled to 500-550 DEG C fastly after finish to gauge with > 4 DEG C/s cooling rate, then with
0.5-1 DEG C/s is cooled to < 150 DEG C and then low temperature batches；Second is that being cooled to 450-650 DEG C of high temperature coiling with > 4 DEG C/s, roll up great in 10
Ton.Above two hot rolled coil is finally air-cooled to room temperature, and former technique can get 1300MPa rank hot rolled steel plate.
(4) step (3) are obtained into two kinds of hot rolled plates and passes through pickling processes, at room temperature cold continuous rolling to 0.5-3.0mm.Due to
Roll that drag is different, low temperature batches < 150 DEG C of hot rolled plate final cold rolling to thickness 1.0-3.0mm in step (3), and 450-
650 DEG C of hot rolled plates batched can be cold-rolled to 0.5-2mm.
(5) cold-rolled steel sheet obtained in step (4) is made annealing treatment.Step (3) low temperature batches < 150 DEG C of hot rolling
After plate cold rolling, 600-700 DEG C of heat preservation 3-10min is heated to the rate of heat addition of > 10 DEG C/s, is then again heated to 720-780 DEG C,
Rapid cooling after soaking time 80-150s, cooling rate > 30 DEG C/s；And for 450-650 DEG C of high temperature coiling of step (3) of hot rolled plate
It after cold rolling, is directly heated with the rate of heat addition of > 10 DEG C/s to 720-780 DEG C, rapid cooling after soaking time 20-60s, cooling rate >
30℃/s.Two kinds of techniques can get high strength cold-rolled dual phase sheet steel.
The chemical component of gained slab or ingot casting is 0.10-0.30wt%C, 1.50-4.50wt%Mn in step (1),
0.00-0.120wt%Al, 0.00-0.90wt%Si, 0.05-0.50%V, P≤0.020wt%, S≤0.02wt%, surplus are
Fe。
According to hot rolled steel plate prepared in step (3), low temperature batches the hot rolled plate tissue of (< 150 DEG C) with shellfish after finish to gauge
Based on family name's body.
It is and the residual deformation group for martensite, ferrite and vanadium carbide according to product tissue signature after step (5) annealing
It knits.
In addition, one or more of element can also be added in slab or ingot casting ingredient, performance is further increased:
Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:
0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, RE are (dilute
Soil): 0.002-0.005wt%, Ca:0.005-0.03wt%.Wherein adding Ni, Mo, Cr, B etc. can further improve quenching for steel
Permeability or low-temperature impact toughness；The refinement original austenite grain such as addition Nb, Ti leads to final structure refinement；Addition Cu, pass through analysis
Strengthen the intensity for improving steel out；It adds Si etc. and improves intensity and inhibition Carbide Precipitation etc.；Add the stabilization that [N] adjusts austenite
Property.
The beneficial effects of the present invention are: this method passes through the hot continuous rolling after the smelting of steel and solidification, slab or ingot formation
1300MPa grade high-strength hot rolled steel plate is obtained with control cooling, or after hot continuous rolling temperature is batched, through pickling and cold rolling at room temperature
It to 1-3mm thickness, is then quenched immediately in a certain temperature isothermal treatment for short time of 720-780 DEG C of two-phase section, vanadium micro-alloying 1300MPa is made
Grade high-strength two-phase cold-rolled steel sheet.The preparation process is by the precipitation strength of nano vanadium carbide particle and martensitic traoformation hardening constituent knot
It closes, significantly improves the intensity of existing dual phase steel, while also assuring higher production efficiency.
The present invention is by using vanadium micro-alloying and controlled rolling, control 1300MPa grades of high-strength hot rolled steel plates of cooling acquisition；
By the way that cold-reduced sheet deformation storage can be obtained to the tissue of nonequilibrium state, then the nanoparticle of vanadium is precipitated strong with martensitic traoformation
Change combines, and then obtains 1300MPa grades of cold-rolled steel sheets.Cold-rolled biphase steel plate obtained in the present invention is double compared to traditional cold rolling
Phase steel plate, under the premise of breaking elongation does not reduce, this index of tensile strength is promoted it is 10% even higher, yield strength this
It is even higher that one index promotes 12%.
The present invention is to redesign basis on the basis of existing dual phase steel, passes through rapid cooling shape after conventional annealing
It is improved outside intensity at martensite, the microalloying ingredient for having also combined vanadium designs, dexterously by formation austenite when annealing and carefully
The precipitated phase of the small particle containing vanadium combines, thus further improves the yield strength and tensile strength of cold-rolled steel sheet, while steel plate
Also good elongation percentage is maintained.
The invention discloses the preparation methods of the hot rolled plate of 1300MPa intensity rank.Currently, existing hot-rolled low-alloy is high
Strong steel sheet intensity rank is no more than 1000MPa mostly, and present invention hot rolled steel plate obtained, by optimizing components design with
The combination of cold technique is controlled, the hot rolled steel plate tensile strength of acquisition is in 1300MPa or so, and elongation percentage is more than 10%, has obvious
Mechanical property advantage.
In above-mentioned technical proposal, the vanadium carbide particle of a large amount of nanoscales, cold rolling can be precipitated in high temperature coiling process after hot rolling
After can directly heat the martensite+ferrite dual phase for being achieved with vanadium carbide precipitation strength after quenching to two-phase section isothermal treatment for short time
Tissue, to effectively promote yield strength and tensile strength in the case where not losing the condition of palsticity；And low temperature after hot rolling is batched
Hot rolled plate is after cold rolling, and major part V is not yet precipitated at this time, need to be heated to allowing VC to analyse compared with heat preservation at the lower temperature of annealing temperature
Out, it then anneals again to two-phase section, which can obtain the VC particle of more small and dispersed, therefore the yield strength of steel plate is more
Height, and tensile strength and elongation percentage are then similar with previous technique.
According to hot rolled steel plate prepared in technical scheme steps (3), low temperature batches the hot rolled plate of (< 150 DEG C) after finish to gauge
Tissue based on bainite, mechanical property be tensile strength 1200-1400MPa, yield strength >=900MPa, breaking elongation >=
10%, uniform elongation >=4%.
It is martensite, ferrite and vanadium carbide according to product tissue signature after technical scheme steps (5) annealing, and remains
Deformation structure；(low temperature batches hot rolled plate cold-reduced sheet and is first heated to 600-700 DEG C of heat preservation is again heated to 720- to former annealing process
Rapid cooling after 780 DEG C of heat preservations), obtain yield strength >=950MPa of steel plate, tensile strength >=1300MPa, uniform elongation >=
5%, breaking elongation 9-15%.Under the premise of uniform elongation and breaking elongation do not reduce, compared to DP1180 steel, it will resist
This index of tensile strength promotes 10%, and yield strength improves 26%；And latter annealing process (high temperature coiling hot rolled plate cold-reduced sheet
Rapid cooling after directly heating to 720-780 DEG C of heat preservation), steel plate yield strength >=800MPa of acquisition, tensile strength >=1300MPa,
Uniform elongation >=5%, breaking elongation are 8-13% under the premise of uniform elongation and breaking elongation do not reduce, compared to
This index of tensile strength is promoted 10% by DP1180 steel, and yield strength improves 12%.The steel plate surrender that former technique obtains
Intensity is higher.
It elaborates with reference to the accompanying drawings and detailed description to the present invention.
Detailed description of the invention
Fig. 1 is the hot rolled steel plate electron scanning micrograph obtained after 1-B-3 group hot rolling in embodiment of the present invention method；
Fig. 2 is the hot rolled steel plate optical metallographic microscope photo obtained after 2-B-3 group hot rolling in embodiment of the present invention method；
Fig. 3 is the cold-rolled steel sheet scanning electron microscope obtained after the cold rolling of 1-B-3 group, annealing in embodiment of the present invention method
Photo；
Fig. 4 is the cold-rolled steel sheet scanning electron microscope obtained after the cold rolling of 2-B-3 group, annealing in embodiment of the present invention method
Photo；
Fig. 5 is the typical work that two kinds of hot rolled steel plates and two kinds of cold-rolled steel sheet stretching experiments obtain in embodiment of the present invention method
Journey load-deformation curve.
Specific embodiment
Following embodiment referring to Fig.1-5.A kind of vanadium micro-alloying 1300MPa grade high-strength hot rolled steel plate and cold-rolled biphase steel
The production method of plate, the specific steps are as follows:
(1) it the smelting and solidification of steel: by converter, electric furnace or induction furnace steel-smelting, is given birth to using continuous casting slab or molding
Produce ingot casting；
(2) hot continuous rolling after slab or ingot formation: slab or ingot casting are heated through 1100-1250 DEG C, by roughing mill into
Row 5-20 passes, hot rolling carry out 5-7 passes to 4-15mm, finish to gauge to 40-80mm thickness specification, then by heat even unit
Temperature is controlled at 800~850 DEG C
(3) it is divided to two kinds of types of cooling after finish to gauge, first is that it is cooled to 500-550 DEG C fastly after finish to gauge with > 4 DEG C/s cooling rate, then with
0.5-1 DEG C/s is cooled to < 150 DEG C and then batches；It is batched second is that being cooled to 450-650 DEG C with > 4 DEG C/s, volume needs to be greater than 15 tons again to protect
Demonstrate,prove slow cooling rate, or in middle simulated test it is cold practical extremely slowly cooling to simulate Industrial Coil with heating furnace heat preservation and furnace
Speed.Above two hot rolled coil is finally air-cooled to room temperature and provides base-material for subsequent cold rolling.But former technique can get
1300MPa rank hot rolled steel plate.
(4) step (3) are obtained into two kinds of hot rolled plates and passes through pickling processes, at room temperature cold continuous rolling to 0.5-3.0mm.Due to
Rolling that drag is different, low temperature batches the hot rolled plate final cold rolling of (< 150 DEG C) to thickness 1.0-3.0mm in step (3), and
The 450-650 DEG C of hot rolled plate batched can be cold-rolled to 0.5-2mm.
(5) cold-rolled steel sheet obtained in step (4) is made annealing treatment.Step (3) low temperature batches the heat of (< 150 DEG C)
After rolling plate cold rolling, 600-700 DEG C of heat preservation 3-10min is heated to the rate of heat addition of > 10 DEG C/s, is then again heated to 720-780
DEG C, rapid cooling after soaking time 80-150s, cooling rate > 30 DEG C/s；And for the heat of step (3) high temperature coiling (450-650 DEG C)
It after rolling plate cold rolling, is directly heated with the rate of heat addition of > 10 DEG C/s to 720-780 DEG C, rapid cooling after soaking time 20-60s, cooling speed
Rate > 30 DEG C/s.Two kinds of techniques can get high strength dual phase cold-rolled steel sheet.
Embodiment 1:
The chemical component (wt%) of 1 invention steel of table
| Ingredient | C | Mn | Al | V | Si | P | S |
| A | 0.10 | 1.84 | 0.080 | 0.08 | 0.20 | <0.005 | <0.005 |
| B | 0.16 | 2.62 | 0.053 | 0.15 | 0.33 | <0.005 | <0.005 |
| C | 0.25 | 4.13 | 0.120 | 0.35 | 0.80 | <0.005 | <0.005 |
Using chemical component shown in table 1, casting ingot-forming after smelting, hot forging adds at the slab of 50mm thickness for the present embodiment test
Heat to 1200 DEG C keep the temperature 3 hours, then warp in try out singlestandmill be hot-rolled down to 4.7 millimeters or so acquisition hot-rolled products, finish to gauge
Temperature at 850 DEG C or so, then according to cooling technique and coiling temperature be divided into 1 and 2 two kind batch mode, be respectively labeled as 1 group
With 2 groups., wherein 1 group is be cooled to 530 DEG C or so with about 5 DEG C/s or so cooling rate after finish to gauge fastly, then with about 0.6-0.8 DEG C/s rate
It is cooled to 150 DEG C, then batches；2 groups are cooled to 550 DEG C with about 5 DEG C/s and batch, and are then placed in 550 DEG C of heat-treatment furnaces and keep the temperature 5 hours
Furnace cooling later, to simulate the Slow cooling process of industrial hot rolled coil.The hot rolled plate mechanical property of the above two type of cooling
It is shown in Table 2, it is seen that the mechanical property of steel plate that low temperature batches after former rapid cooling is up to 1300MPa.
The hot rolled plate of 1st group of acquisition is cold-rolled to 2mm thickness, 630-670 DEG C of heat preservation 300-600s is heated to 15 DEG C/s, so
After be again heated to different temperatures within the scope of 720-760 DEG C, in soaking time 120-150s after different time, after taking-up oil it is cold, it is cold
But rate is more than 30 DEG C/s；The hot rolled plate of 2nd group of acquisition is cold-rolled to 1.2mm thickness, is directly heated with 15 DEG C/s to 720-760 DEG C
Different temperatures in range keeps the temperature 30-60s, oily cold, cooling rate > 30 DEG C/s after taking-up.Two kinds of techniques can get high-intensitive double
Phase cold-rolled steel sheet, performance are shown in Table 3.
It is cold after 1 group of hot rolling it can be seen from Fig. 1 electron scanning micrograph by the characterization discovery to microstructure
But bainite structure is obtained.The tissue that 2 groups of hot roller repairings obtain it can be seen from Fig. 2 electron scanning micrograph is pearl
Body of light tissue, ferrite are matrix, are dispersed with cementite particle.This is mainly due to the differences of hot rolling technology to cause.It is swept by Fig. 3
Retouching electron micrograph and can be seen that final state tissue after 1 group of annealing is ferrite+martensitic structure, and along rolling to being in
Zonal distribution, original austenite grain size and ferrite grain size are at 1~3 micron.By Fig. 4 electron scanning micrograph
As can be seen that final state tissue is ferrite+martensitic structure after 2 groups of annealing, and along rolling in zonal distribution, original austenite
Crystallite dimension and ferrite grain size are at 1~3 micron.The difference side of batching it can be seen from Fig. 5 engineering stress strain curve
There are greatest differences for the tensile mechanical properties of formula acquisition hot rolled steel plate；In addition, the tensile strength of final state tissue is higher than after 1 group of annealing
1300MPa, yield strength are higher than 800MPa, and uniform elongation is higher than 6%, and breaking elongation is higher than 10%.Final state group after 2 groups of annealing
The tensile strength knitted is higher than 1300MPa, and yield strength is higher than 800MPa, and uniform elongation is higher than 6%, and breaking elongation is higher than 9%.
2 hot rolled plate mechanical property of table
Mechanical property after hot rolled plate cold rolling in 3 table 2 of table after going through different annealing
Yield strength substantially exceeds 800MPa, the yield strength of first group of hot rolling low-temperature coiling processes after cold-rolled steel sheet annealing
It is higher, more than 950MPa；In 1300MPa or more, strength and ductility product obtains the two tensile strength in 12GPa% or more, this technique
Performance be obviously improved compared to traditional DP1180, be expected to put into actual production.
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| CN111363978B (en) * | 2018-12-26 | 2021-11-16 | 宝山钢铁股份有限公司 | Welding softening resistant ferrite martensite hot-rolled dual-phase steel and manufacturing method thereof |
| CN110129670B (en) * | 2019-04-25 | 2020-12-15 | 首钢集团有限公司 | A kind of 1300MPa grade high strength and high plasticity hot stamping steel and preparation method thereof |
| CN110684932B (en) * | 2019-10-12 | 2021-06-08 | 唐山钢铁集团有限责任公司 | 1500 MPa-grade cold-formed strip steel and production method thereof |
| CN113737087B (en) | 2020-05-27 | 2022-07-19 | 宝山钢铁股份有限公司 | Ultrahigh-strength dual-phase steel and manufacturing method thereof |
| CN112795837B (en) * | 2020-11-20 | 2022-07-12 | 唐山钢铁集团有限责任公司 | A 1300Mpa grade high toughness cold-formed steel sheet and its production method |
| CN115181897B (en) * | 2021-04-02 | 2023-07-11 | 宝山钢铁股份有限公司 | 1280 MPa-level low-carbon low-alloy ultra-high strength dual-phase steel and rapid heat treatment manufacturing method |
| CN113930675B (en) * | 2021-09-16 | 2022-11-01 | 鞍钢集团北京研究院有限公司 | A kind of 2200MPa grade low carbon B-free hot forming steel and preparation method thereof |
| CN114293111B (en) * | 2021-12-08 | 2022-10-11 | 北京科技大学 | A 1.1GPa-level lamellar interphase martensite-ferrite dual-phase steel and preparation method thereof |
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