CN108660369A - Quenching partition cold-rolled steel plate with tensile strength of more than 1180MPa and production method thereof - Google Patents
Quenching partition cold-rolled steel plate with tensile strength of more than 1180MPa and production method thereof Download PDFInfo
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- 238000005192 partition Methods 0.000 title claims abstract description 26
- 238000010791 quenching Methods 0.000 title claims abstract description 25
- 230000000171 quenching effect Effects 0.000 title claims abstract description 25
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 13
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 46
- 239000010959 steel Substances 0.000 claims abstract description 46
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 39
- 238000001816 cooling Methods 0.000 claims abstract description 20
- 238000000137 annealing Methods 0.000 claims abstract description 18
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 16
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 9
- 238000010583 slow cooling Methods 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 238000005097 cold rolling Methods 0.000 claims description 13
- 238000005098 hot rolling Methods 0.000 claims description 9
- 238000005554 pickling Methods 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 claims description 5
- 238000005266 casting Methods 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 230000003111 delayed effect Effects 0.000 claims 1
- 239000000126 substance Substances 0.000 abstract description 4
- 238000004886 process control Methods 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 12
- 239000011572 manganese Substances 0.000 description 10
- 238000000034 method Methods 0.000 description 9
- 229910052742 iron Inorganic materials 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 241000196324 Embryophyta Species 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 1
- 235000019082 Osmanthus Nutrition 0.000 description 1
- 241000333181 Osmanthus Species 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 229910000720 Silicomanganese Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000000638 solvent extraction Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—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
- C22C38/12—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
- C21D2211/001—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
- C21D2211/005—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
The invention relates to a quenching partition cold-rolled steel plate with tensile strength of more than 1180MPa and a production method thereof, wherein a steel plate is partially austenitized during annealing and heating to realize the enrichment of carbon in an austenite structure; adopting slow cooling in a dual-phase area, adjusting the volume fraction of two phases of austenite and ferrite, and further enriching carbon in austenite; then rapidly cooling at a cooling speed of 30-40 ℃/s to convert the austenite part into martensite; and then heating and preserving heat, and finally air-cooling to room temperature to obtain a multi-phase structure of ferrite, martensite and metastable austenite. The advantages are that: the quenching partition cold-rolled steel plate with the tensile strength of more than 1180MPa is produced in batches, the chemical components are simple, trace Nb elements are not added except C, Si and Mn or are only added, the smelting cost is low, and the process control is simple and convenient; the continuous annealing is heating in a dual-phase region, the cooling speed required by fast cooling is low, the requirement on the equipment capacity of a continuous annealing unit is low, and the production method is simple.
Description
Technical field
The invention belongs to the cold rollings that cold rolled automobile steel making field more particularly to a kind of tensile strength are more than 1180MPa
Automobile superhigh intensity quenching partition steel plate and production method.
Background technology
In recent years, along with the increasingly raising of quality of life, auto industry is persistently grown rapidly, and vehicle population increases year by year
Add.This trend also brings huge burden while causing severe pressure to communications and transportation to the energy and ecological environment.
Statistics indicate that vehicle weight often declines 10%, energy consumption 3%~7% can be saved；Vehicle can be more steady because of the reduction of chassis quality
It is fixed；Lightweighting materials absorb crash energy, can improve crashworthiness.Therefore, automotive light weight technology becomes inexorable trend.
Advanced high-strength steel is the important effective means of automobile lightweight, and Recent Progresses In The Development becomes iron and steel enterprise and automobile
The emphasis that industry is concerned about.Quenching partition steel, also referred to as QP (Quenching and Partitioning) steel, it is advanced as the third generation
One of Representative Cultivars of high-strength steel have excellent mechanical property, thinned, the city particularly suitable for automobile structure, reinforcer
Field has a extensive future.Compared with the dual phase steel of equal tensile strength, it has higher elongation percentage；With the phase transformation of equal tensile strength
Inducing plasticity steel is compared, it has lower carbon equivalent.
The basic principle of quenching partition steel was put forward for the first time by American scholar Speer professors in 2003, i.e., by quenching-matching
Division technique realizes diffusion of the C element from martensite to retained austenite, obtains the metastable Ovshinsky of certain volume score at room temperature
TRIP effects occur in deformation process for body, metastable austenite, to obtain good intensity and plasticity cooperation.However, due to
The technique needs to reheat after quenching, and the cooling and aging section heating Capability Requirement to annealing furnace are higher, therefore for many years to this
The research of new steel grade rests on always theoretical research and laboratory stage.Since 2012, Baosteel and Anshan iron and steel plant are successively completed and are quenched
Fire matches the Industry trial-production of steel splitting, realizes the conversion of theory into action, excellent product performance.Wherein, Baosteel utilizes its high-strength steel
Special producing line production, using stringent quenching partition technique, i.e. austenite one phase area is heated；The special producing line of Anshan iron and steel plant high-strength steel is
In establishing, therefore according to existence conditions, the quenching partition technique of coexistence region heating is used to be successfully realized in traditional producing line for the first time
The industrialized production of the product.
In existing open source literature：The quenching-of Wang Chenglin, Li Wei, a kind of new-type high silicon hot forming steel that study of the Chinese classic army delivers are matched
Divide processing and its performance [J] material heat treatment journals, 2015 (05)；Wan Decheng, Feng Yunli, the isothermal temperature pair that Li Jie delivers
Influence [J] heat processing techniques of direct quenching partition super-high strength steel structure property, 2015 (10)；Zhou Yedong, Zhou Shu, Ding Chen,
Big, Li Hetian is built, research [J] plastic engineering journals of the tough brittleness energy of the QP980 steel low temperature that Fang Jian is delivered, 2015 (03)；Zuo Dun
Osmanthus, Yan Qi, Wang Li, the strong QP980 steel laser welded seam tissues of superelevation and performance study [J] intermetallic composite coatings (hot-working), 2015
(04)；Zheng Debing, Liu Yifan, Wu Chunming, the remaining high-strength steel QP980 punching presses of the 3rd generation stability study [J] mould industries celebrated joyously,
2015(02)；After the hardening heat of Chen Liansheng, Zhao Yuan, Tian Yaqiang, Song Jinying, Yang Dong are to silico-manganese steel coexistence region heat preservation+Q＆P processing
Structure property influences [J] steel vanadium titaniums, 2014 (05)；Bring up Xinhua, Tian Zhihong, Cui Guibin are remained in the Q＆P steel of Meng Yang, Cai Ning
Stability [J] material heat treatment journals of austenite, 2014 (10)；And in the prior art, number of patent application
201110154471.4 a kind of quenching partition production method of disclosed cold-rolled transformation induced plasticity, above-mentioned technical proposal master
It is most of to be used for experiment for the prior art if the steel for producing 980MPa ranks, and batch is not implemented and stablizes life
Production, for tensile strength 980MPa ranks, Anshan iron and steel plant product yield tensile ratio is relatively low, and elongation percentage is higher, and formability is more preferable.
So far, the only above-mentioned Liang Jia iron and steel enterprises in the whole world can realize the volume shipment of quenching partition steel, and all exist
Carry out the development of higher intensity rank and hot dip zinc product.
Invention content
In order to overcome the deficiencies of the prior art, the object of the present invention is to provide the quenchings that a kind of tensile strength is more than 1180MPa
Partition cold-rolled steel sheet and production method, using coexistence region mode of heating continuous annealing, production method is simple, is produced using conventional anneal
Line can be realized.
To achieve the above object, the invention is realized by the following technical scheme：
A kind of tensile strength is more than the quenching partition cold-rolled steel sheet of 1180MPa, and composition by weight percent content is：
C：0.20%-0.30%, Si：1.5%-2.0%, Mn：2.0%-3.0%, P：≤ 0.02%, S：≤ 0.01%,
Nb：0-0.03%, surplus are Fe and inevitable impurity.
A kind of production method of the quenching partition cold-rolled steel sheet of tensile strength more than 1180MPa, steel plate portion when annealing heating
Divide austenitizing, realizes enrichment of the carbon in austenite structure；Using coexistence region slow cooling, austenite, ferrite two-phase mixture are adjusted
Fraction, the further rich carbon of austenite；Then with the cooling rate rapid cooling of 30-40 DEG C/s, austenite fraction is made to be changed into martensite；With
After heat up and keep the temperature again, make carbon from martensite to the austenite diffusion not changed；It is last air-cooled to room temperature, obtain ferrite, geneva
The heterogeneous structure of body and metastable austenite, production process are：Smelting → continuous casting → hot rolling → pickling → cold rolling → continuous annealing, tool
Body includes the following steps：
1) it is casting continuously to form slab；
2) hot rolling：Slab heating temperature is 1200~1250 DEG C, keeps the temperature 180min or more；Hot rolling start rolling temperature be more than
1100 DEG C, finishing temperature is 900~1000 DEG C；Coiling temperature is 650~700 DEG C；
3) pickling and cold rolling：Hot rolled plate carries out cold rolling after conventional pickling, and cold rolling reduction ratio controls between 50~60%；
4) continuous annealing：Heating temperature be 780~820 DEG C, soaking time 150-180s, slow cooling speed be 5-10 DEG C/
S, 680~720 DEG C of slow cooling temperature, fast speed of cooling be 30-40 DEG C/s, rapid cooling temperature be 250~280 DEG C, partition temperature be 350~
400 DEG C, the partition time is 300~600s, air-cooled later to room temperature.
Wherein, C：C is intensified element most basic in steel, and improves the important element of stabilization of austenite, especially
The metastable austenite for diffuseing to form certain volume score at room temperature of C is utilized in the present invention.Phosphorus content is too low, martensite hardness
Decline, intensity cannot be satisfied requirement, while metastable austenite volume fraction declines or stability is insufficient.Carbon content is excessively high, steel plate
Plasticity decline, formability and weldability reduce.Therefore the present invention claims C contents between 0.20%-0.30%.
Si：Si is non-carbide formation element, and the intensity and cold deformation for improving steel plate by solution strengthening are hardened
Rate.In the present invention, using it, the extremely low characteristic of solubility, obstruction austenite decomposition reduce the precipitation of cementite in carbide,
Ensure the rich carbon of metastable austenite.Si contents are insufficient, and the room temperature stability of metastable austenite declines, and intensity, plasticity reduce simultaneously.
Si too high levels can reduce the surface quality of hot rolling slab, the coating performance of cold-rolled steel sheet and welding performance.Therefore in the present invention
Si contents be 1.5%-2.0%.
Mn：Mn is one of effective solution strengthening element, and quenching degree is had a significant impact, and can promote the shape of martensite
At, while Mn is also austenite stabilizer element, can reduce cementite Precipitation Temperature.Mn contents are too low, martensite forming amount
Deficiency, intensity declines, while the volume fraction and stability for the metastable austenite that can not ensure；Mn too high levels, it will cause
Serious component segregation forms banded structure, influences the mechanical property of steel plate.Therefore the Mn contents that the present invention selects are in 2.0%-
3.0% range.
P、S：P, S is relict element, and P easily causes steel plate center segregation, the serious impact flexibility for destroying steel, and there are secondary
Brittleness is processed, hot-working and the weldability of steel plate are unfavorable for；S easily forms non-metallic inclusion with Mn, makes the clod wash and expansion of steel plate
Pore performance declines, therefore both should try to control in reduced levels.That is P≤0.02%, S≤0.01%.
Nb：Nb exists to replace in the form of solute atoms in steel, plays solution strengthening effect.It can significantly be carried when dissolving in austenite
The quenching degree of high steel plate；In the presence of in the form of carbide or oxide fine particle, crystal grain thinning simultaneously reduces quenching degree.In the present invention,
The effect of Nb mainly improves the recrystallization temperature of austenite, and crystal grain thinning is more stablized, tiny metastable austenite,
The hole expansibility and cold-bending property of steel plate are improved simultaneously.Micro Nb is enough that steel plate can be made to obtain excellent comprehensive performance, extra
Nb is no longer apparent to the contribution of Strengthening and Toughening, and cost of alloy is caused to improve, thus the present invention claims Nb contents 0-0.03% it
Between.
Compared with prior art, the beneficial effects of the invention are as follows：
1) for the present invention to produce the quenching partition cold-rolled steel sheet that tensile strength is more than 1180MPa in batches, chemical composition is simple
It is single, it is not added in addition to C, Si, Mn or is only added to micro Nb elements, smelting cost is cheap, and technology controlling and process is easy.
2) continuous annealing is heated for coexistence region, and the cooling velocity that rapid cooling requires is only 30-40 DEG C/s, is set to continuous annealing unit
Standby Capability Requirement is relatively low, and production method is simple, and industrialization can be realized in conventional anneal producing line.
3) heterogeneous structure of ferrite, martensite and metastable austenite is obtained at room temperature, and steel plate tensile strength is more than
1180MPa, while there is good plasticity, it can be used for cold forming, ideal lightweighting materials provided for automobile industry.
4) finally obtained mechanical property of steel plate is Rp0.2：600-945MPa；Rm：1185-1255MPa；A：13.0-
16.5%.
Specific implementation mode
The present invention is described in detail below, it should be noted that the implementation embodiment party not limited to the following of the present invention
Formula.
Tensile strength is more than the quenching partition cold-rolled steel sheet of 1180MPa, and composition by weight percent content is：
C：0.20%-0.30%, Si：1.5%-2.0%, Mn：2.0%-3.0%, P：≤ 0.02%, S：≤ 0.01%,
Nb：0-0.03%, surplus are Fe and inevitable impurity.
Tensile strength is more than the quenching partition cold-rolled steel sheet and production method of 1180MPa, and sheet steel sections are difficult to understand when annealing heating
Family name's body realizes enrichment of the carbon in austenite structure；Using coexistence region slow cooling, austenite, ferrite two-phase mixture integral are adjusted
Number, the further rich carbon of austenite；Then with the cooling rate rapid cooling of 30-40 DEG C/s, austenite fraction is made to be changed into martensite；Then rise
Temperature is kept the temperature again, and carbon is made to be spread from martensite to the austenite not changed；It is last air-cooled to room temperature, obtain ferrite, martensite and
The heterogeneous structure of metastable austenite, production process are：Smelting → continuous casting → hot rolling → pickling → cold rolling → continuous annealing, it is specific to wrap
Include following steps：
1) it is casting continuously to form slab；
2) hot rolling：Slab heating temperature is 1200~1250 DEG C, keeps the temperature 180min or more；Hot rolling start rolling temperature be more than
1100 DEG C, finishing temperature is 900~1000 DEG C；Coiling temperature is 650~700 DEG C；
3) pickling and cold rolling：Hot rolled plate carries out cold rolling after conventional pickling, the control of cold rolling total reduction 50~60% it
Between；
4) continuous annealing：Heating temperature be 780~820 DEG C, soaking time 150-180s, slow cooling speed be 5-10 DEG C/
S, 680~720 DEG C of slow cooling temperature, fast speed of cooling be 30-40 DEG C/s, rapid cooling temperature be 250~280 DEG C, partition temperature be 350~
400 DEG C, the partition time is 300~600s, air-cooled later to room temperature.
Embodiment：
Embodiment chemical composition is as shown in table 1：
1 chemical composition of table (wt%)
Embodiment rolling technological parameter is as shown in table 2：
2 rolling technological parameter of table
Embodiment continuous annealing process parameter is as shown in table 3：
3 continuous annealing process parameter of table
The mechanical property of embodiment steel plate is as shown in table 4：
The mechanical property of 4 steel plate of table
Claims (2)
1. a kind of tensile strength is more than the quenching partition cold-rolled steel sheet of 1180MPa, which is characterized in that composition by weight percent content
For：
C：0.20%-0.30%, Si：1.5%-2.0%, Mn：2.0%-3.0%, P：≤ 0.02%, S：≤ 0.01%, Nb：0-
0.03%, surplus is Fe and inevitable impurity.
2. a kind of production method of quenching partition cold-rolled steel sheet of tensile strength according to claim 1 more than 1180MPa,
It is characterized in that, sheet steel sections austenitizing when annealing heating, realizes enrichment of the carbon in austenite structure；It is slow using coexistence region
It is cold, adjust austenite, ferrite two-phase volume fraction, the further rich carbon of austenite；Then with the cooling rate rapid cooling of 30-40 DEG C/s,
Austenite fraction is set to be changed into martensite；Then heating is kept the temperature again, and carbon is made to be spread from martensite to the austenite not changed；Finally
Air-cooled to obtain the heterogeneous structure of ferrite, martensite and metastable austenite to room temperature, production process is：Smelting → continuous casting → heat
→ pickling → cold rolling → continuous annealing is rolled, following steps are specifically included：
1) it is casting continuously to form slab；
2) hot rolling：Slab heating temperature is 1200~1250 DEG C, keeps the temperature 180min or more；Hot rolling start rolling temperature is more than 1100
DEG C, finishing temperature is 900~1000 DEG C；Coiling temperature is 650~700 DEG C；
3) pickling and cold rolling：Hot rolled plate carries out cold rolling after conventional pickling, and cold rolling reduction ratio controls between 50~60%；
4) continuous annealing：Heating temperature is 780~820 DEG C, soaking time 150-180s, and slow cooling speed is 5-10 DEG C/s, is delayed
680~720 DEG C of cold temperature, fast speed of cooling are 30-40 DEG C/s, and rapid cooling temperature is 250~280 DEG C, and partition temperature is 350~400
DEG C, the partition time is 300~600s, air-cooled later to room temperature.
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| CN109898018A (en) * | 2019-03-01 | 2019-06-18 | 鞍钢股份有限公司 | Cold-rolled 1300 MPa-grade martensitic steel and production method thereof |
| CN109930079A (en) * | 2019-03-29 | 2019-06-25 | 本钢板材股份有限公司 | A kind of 980MPa grades of inexpensive cold rolling quenching partition steel and preparation method thereof |
| CN110093552A (en) * | 2019-05-30 | 2019-08-06 | 安徽工业大学 | A kind of high strength and ductility Q&P steel plate and preparation method thereof that welding performance is excellent |
| CN110093564A (en) * | 2019-05-06 | 2019-08-06 | 东北大学 | A kind of 1180MPa grade super strength low cost cold rolling quenching partition steel and its manufacturing method |
| CN110129673A (en) * | 2019-05-21 | 2019-08-16 | 安徽工业大学 | A kind of 800MPa grades of high strength and ductility Q&P steel plate and preparation method thereof |
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| CN114606449A (en) * | 2022-03-24 | 2022-06-10 | 华南理工大学 | High-strength-ductility low-yield-ratio DP980 cold-rolled dual-phase steel and production method thereof |
| CN114606449B (en) * | 2022-03-24 | 2023-09-26 | 华南理工大学 | DP980 cold-rolled dual-phase steel with high strength and elongation product and low yield ratio and production method thereof |
| CN115198176B (en) * | 2022-06-16 | 2023-09-15 | 首钢集团有限公司 | Martensitic steel for ultrahigh-strength carriage and preparation method thereof |
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