CN105274432A - 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof - Google Patents
600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof Download PDFInfo
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- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 16
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 17
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 75
- 239000010959 steel Substances 0.000 claims description 75
- 238000001816 cooling Methods 0.000 claims description 31
- 238000000137 annealing Methods 0.000 claims description 28
- 238000005097 cold rolling Methods 0.000 claims description 24
- 238000000034 method Methods 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 16
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- 238000005554 pickling Methods 0.000 claims description 8
- 238000010583 slow cooling Methods 0.000 claims description 8
- 238000009413 insulation Methods 0.000 claims description 6
- 238000003723 Smelting Methods 0.000 claims description 5
- 238000007670 refining Methods 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910001562 pearlite Inorganic materials 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 2
- 239000010955 niobium Substances 0.000 description 14
- 239000010936 titanium Substances 0.000 description 13
- 230000008569 process Effects 0.000 description 10
- 229910000734 martensite Inorganic materials 0.000 description 9
- 230000009466 transformation Effects 0.000 description 9
- 229910001563 bainite Inorganic materials 0.000 description 8
- 238000005275 alloying Methods 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910001275 Niobium-titanium Inorganic materials 0.000 description 3
- RJSRQTFBFAJJIL-UHFFFAOYSA-N niobium titanium Chemical compound [Ti].[Nb] RJSRQTFBFAJJIL-UHFFFAOYSA-N 0.000 description 3
- 235000019362 perlite Nutrition 0.000 description 3
- 239000010451 perlite Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000003351 stiffener Substances 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
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- 150000004767 nitrides Chemical class 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
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- 238000005482 strain hardening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
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- 229910052742 iron Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 208000020442 loss of weight Diseases 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention discloses a 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate which is characterized by comprising the following components in percentage by mass: 0.06% -0.12%, Si: 0.02 to 0.10%, Mn: 1.40% -2.00%, P: less than or equal to 0.015%, S: less than or equal to 0.010 percent, Al: 0.02% -0.10%, N: less than or equal to 0.0050%, Nb: 0.015-0.045%, Ti: 0.020-0.055%, and the balance of 0.035% to 0.100% of Nb + Ti, and the balance of ferrite is Fe and other inevitable impurities.
Description
Technical field
The invention belongs to automobile cold-rolled high strength thin slab technique field, provide a kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet and manufacture method thereof.
Background technology
Less energy-consumption, loss of weight and high safety have become development trend that is modern and future automobile, for adapting to automotive industry this development trend, automobile production producer and iron and steel enterprise and scientific research institutions are just actively devoted to the research and development of body of a motor car " lightweight " design and automobile high-strength steel.The automobile cold-rolled high-strength steel industrial volume production such as the two-phase of the intensity developed at present from 590MPa to 980MPa (DP) steel and phase change induction plasticity (TRIP) steel, for frame member, the automobile component such as stiffener and anti-collision energy absorption part of automobile, achieve body of a motor car " lightweight " requirement.Because the automobile structure that manufactures with these High Strength Steel Plates is shaped relatively simple, the deflection of steel plate is little, and work hardening capacity is not high, although the yield strength of baking vanish process light plate after forming increases, meets the strength and stiffness of vehicle body.But, produce the cold rolling high strength steel of these advanced persons, to the cooling section of continuous annealing furnace and aging section Capability Requirement higher, annealing process controls harsh, and production difficulty is high.For reducing cold rolling high strength steel production difficulty, and the vehicle body of guarantee high tensile steel plate manufacture has enough strength and stiffness, meet body of a motor car " lightweight ", need to add micro alloying element in the composition of cold-rolled steel sheet, and production technique is improved, make cold-rolled steel sheet have high yield tensile ratio and excellent plasticity concurrently.
CN101376944A relates to a kind of high-strength high-tensile ratio cold-rolled steel sheet and manufacture method thereof, and the yield strength of its steel plate is greater than 500MPa, and tensile strength is greater than 600MPa, and yield tensile ratio is greater than 0.80.600MPa is greater than for obtaining this intensity, the steel plate that yield tensile ratio is greater than 0.80, in annealing process, less than 200 DEG C are cooled fast to by two-part after steel plate being heated to 780-850 DEG C of insulation, this technique first paragraph easily controls from high temperature rapid cooling, and second segment is cooled fast to less than 200 DEG C from the lesser temps of 400-500 DEG C, very large to relying on the annealed wire difficulty of gas vapour cooling, do not possess actual operation.
CN101558178A provides a kind of cold-rolled steel sheet with high-yield-ratio and excellent weather resistance, Nb is added in this steel grades, Ni, the alloying elements such as Co, Cr, Cu and B, that the yield tensile ratio obtaining steel plate is greater than 0.85, and tensile strength is greater than 800MPa by the steel plate continuous annealing in 500 DEG C of temperature ranges to A1 transition point after cold rolling, be mainly used in building, track vehicle and freight container, there is no comparability with the automobile product of high yield ratio cold rolling high strength steel plate and annealing process.
The production technique of the low-alloy high-strength cold-reduced sheet of a kind of automobile high strength and ductility that CN103088255A announces, steel plate is continuous annealing after cold rolling, and annealing soak temperature is 840-860 DEG C, and slow cooling temperature is 670-700 DEG C, rapid cooling temperature is 410-430 DEG C, and completion of prescription temperature is 350-370 DEG C.Add compound in steel and with the addition of micro alloying element Ti and Nb, after annealing, the tensile strength of steel plate reaches 500MPa, and elongation reaches 30%, and strength and ductility product is 15GPa%, and yield tensile ratio reaches more than 0.80.
CN102492823A provides the continuous annealing process of the cold rolling low-alloy high-strength steel plate of a kind of yield strength 420MPa level, by the cold rolling low-alloy high-strength steel plate containing Ti, Nb chemical element is heated to 800 ± 10 DEG C of insulations through two sections, then slow cooling is to 600 ± 20 DEG C of coolings fast, cooling end temp is 270 ± 20 DEG C, last as being water-cooled to room temperature, obtain yield strength and be about 430MPa, tensile strength is about 500MPa, and elongation after fracture is about the steel plate of 21%.This technique is that continuous annealing furnace rapid cooling section is identical with the rate of cooling adjustment of overaging section, decreases the cooling time of steel plate.But this annealing process requires higher to the rate of cooling of continuous annealing furnace overaging section.
Summary of the invention
The object of the invention is the problems referred to above solving prior art existence, a kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet and preparation method thereof is provided, can by the smelting composition of steel and hot rolling, cold rolling and continuous annealing process parameter, realize the fetrite grain refinement of steel plate, the complex intensifying effect of precipitation strength and phase transformation strengthening, to obtain high-yield-ratio and the high-ductility of cold-rolled steel sheet, the vehicle body meeting cold rolling high strength steel plate manufacture has enough strength and stiffness, tensile strength can be produced relatively easily at more than 600MPa on industrial continuous annealing production line, elongation after fracture is greater than 19%, the high-yield-ratio high-ductility cold-rolled steel sheet that yield tensile ratio is greater than 0.8.
For achieving the above object, the present invention takes following technical scheme:
A kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet, it is characterized in that composition is C:0.06% ~ 0.12%, Si:0.02% ~ 0.10%, Mn:1.40% ~ 2.00%, P by mass percentage :≤0.015%, S :≤0.010%, Al:0.02% ~ 0.10%, N :≤0.0050%, Nb:0.015% ~ 0.045%, Ti:0.020% ~ 0.055% and meet 0.035%≤Nb+Ti≤0.100%, surplus is Fe and some other inevitable impurity.
A kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet, it is characterized in that composition is C:0.08% ~ 0.10%, Si:0.05% ~ 0.07%, Mn:1.60% ~ 1.80%, P by mass percentage :≤0.010%, S :≤0.005%, Al:0.05% ~ 0.08%, N :≤0.0030%, Nb:0.025% ~ 0.035%, Ti:0.035% ~ 0.045%, and meet 0.060%≤Nb+Ti≤0.080%, surplus is Fe and some other inevitable impurity.
Steel grades control principle of the present invention is as follows:
C: be strengthening element basic in steel, the intensity of energy active balance steel and ductility.Also be the element of effective bainite and martensite low-temperature transformation phase, be ensure the high-yield-ratio of steel, in the present invention, C controls 0.06% ~ 0.12%, and more preferably 0.08% ~ 0.10%.
Si: be ferrite generating elements, impels carbon to austenite segregation and the formation suppressing carbide, has removing and cleaning action, to avoid gap solution strengthening to solid solution carbon in ferrite.The present invention mainly relies on the precipitation strength of the carbonitride of niobium titanium in ferritic phase, and grain refining improves ferrite intensity, has high yield strength to reach steel plate.Therefore, in the present invention, Si controls 0.02% ~ 0.10%, and more preferably 0.05% ~ 0.07%%.
Mn: belong to and expand austenite phase field, the element of stable austenite, effectively can improve the hardening capacity on austenite island, after thus can reducing steel plate middle temperature transformation, remaining austenitic transformation becomes the necessary rate of cooling of martensite, and plays the effect of solution strengthening and fining ferrite grains.High Mn content easily causes cementite, perlite and bainite to be main banded structure, and affects the welding property of steel plate.Mn content of the present invention controls 1.40% ~ 2.00%, and more preferably 1.60% ~ 1.80%.
Al:Al is main reductor, and Al can also form AlN precipitation simultaneously, plays certain Grain refinement.When in steel, Al is added for deoxidation, unsuitable too low, otherwise the oxide compound that Mn, Si etc. are thick disperses in a large number in steel, deterioration steel, but too much tufted aluminum oxide inclusion increases, the plasticity of steel and weldability are deteriorated, steelmaking and continuous casting can be affected again and produce, in the present invention, Al content controls 0.02% ~ 0.10%, and more preferably 0.05% ~ 0.08%.
Nb, Ti: have precipitation strength effect effectively improve the yield strength of steel and the element of crystal grain thinning.Add Nb and Ti element in steel, form carbonitride, refining grain size also keeps the effect of carbon.Ferrite matrix is strengthened, reduces the difference of hardness with bainite and martensite phase, effectively improve the plasticity of steel plate.For making fining ferrite grains size and improving ferritic intensity, Nb of the present invention, the content of Ti controls 0.015% ~ 0.045% and 0.020% ~ 0.055%, and more preferably 0.025% ~ 0.035% and 0.035% ~ 0.045%, and meet 0.060%≤Nb+Ti≤0.080%.
N: make nitride separate out in steel plate, contribute to strengthening steel plate, but superfluous, then nitride is separated out in a large number, and cause unit elongation and weldability deterioration, in the present invention, N content controls below 0.0050%, and more preferably less than 0.0030%.
P, S: be the harmful element in steel.P easily on crystal boundary segregation cause embrittlement, S easily forms the inclusiones such as MnS in steel, and the performance of steel and weldability are deteriorated.In the present invention, P, S content controls respectively below 0.015% and 0.010%, and more preferably less than 0.010% and 0.005%.
A kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet manufacture method, comprise converter smelting, cast after external refining, anneal on hot continuous rolling, pickling and cold-rolling, continuous annealing furnace, smooth, it is characterized in that, during hot continuous rolling, by heating of plate blank to 1200 ~ 1300 DEG C, insulation 120-180min, finish rolling start rolling temperature is 1000 ~ 1100 DEG C, finishing temperature is 890 ~ 950 DEG C, coiling temperature 600 ~ 650 DEG C, obtains the hot-rolled coil that microstructure is ferrite and pearlite, and hot-rolled coil thickness is 2.0 ~ 6.5mm; In described pickling and cold-rolling, cold rolling draft is 60 ~ 80%, and cold rolling coil plate thickness is 0.5 ~ 2.5mm; In described anneal, steel band is 790 ~ 850 DEG C in the holding-zone temperature of annealing furnace, and soaking soaking time is 110 ~ 240s; After steel band insulation, two-stage cooling is cooled fast after adopting first Slow cooling, steel band is cooled to 700-730 DEG C from holding temperature by slow cooling section, rate of cooling is 1 ~ 5 DEG C/s, steel band is cooled to 320 ~ 360 DEG C with the rate of cooling of 25 ~ 50 DEG C/s by rapid cooling section, then at 320 ~ 360 DEG C, carry out Wetted constructures, overaging time 440 ~ 920s, air-cooledly after timeliness, smooth to batch.
The present invention selects the reason of processing parameter in above-mentioned each feature as follows:
Slab soaking temperature is between 1200 ~ 1300 DEG C, and soaking time is 120-180min.Soaking temperature controls more than 1200 DEG C, and being increases the solid solution capacity of Nb, improves precipitating reinforcing effect, but soaking temperature can not higher than 1300 DEG C, to avoid the overheated and burning of slab.Soaking time controls between 120-180min, for making microstructure and composition full and uniformization of slab, and avoids the energy consumption of long generation heat-up time.
Finish rolling start rolling temperature controls between 1000 ~ 1100 DEG C, in order to frame several before finish rolling realizes recrystallization zone rolling, and the mill milling load before reducing under several frame heavy reduction.
Finishing temperature control, between 890 ~ 950 DEG C, is in order to alloying element solid solution, separates out with crystal grain thinning in annealing.Further, at more than Ar3 high-temperature final rolling, be conducive to homogeneity of structure, prevent the generation of deformation texture, anisotropy and banded structure.Finishing temperature is no more than 950 DEG C, to prevent the excessive abnormal growth of recrystal grain, meanwhile, too high finishing temperature causes the growing amount of oxide compound sharply to increase, plate surface quality after pickling (there is the oxide skin of owing pickling and not eliminating) is cold rolling is deteriorated, and reduces the plasticity of steel plate.
Oiler temperature control, between 600 ~ 650 DEG C, batches under this temperature range, can prevent carbide thicker in eutectoid transformation subsequently from generating, also can alleviate the Carbonitride Precipitation thing of niobium titanium and the degree of growing up of ferrite crystal grain.
After hot-rolled coil, after pickling, cold rolling draft controls between 60 ~ 80%, is for giving full play to cold rolling mill ability.Cold rolling draft is lower than 60%, and cold rolling efficiency is low, and cold rolling draft is higher than 80%, and work hardening is strengthened, and cold roller and deformed drag increases, and easily causes cold mill complex load to transfinite.In addition, the pearlite colony spacing under this draft in structure of steel reduces and perlite is broken more abundant, for the grain refining in annealing process provides condition.
Because the carbonitride of niobium in steel and titanium suppresses ferritic recrystallization temperature, during continuous annealing, soaking temperature should control between 790 ~ 850 DEG C, and soaking time is 110 ~ 240s.All changing the alloying element such as austenitizing and C, Mn into for making the perlite in steel to spread in austenite from ferrite, improving austenitic stability.Soaking temperature lower than 790 DEG C, steel organize austenitizing degree inadequate, suitable bainite and martensite content can not be obtained during cooling.Soaking temperature is higher than 850 DEG C, and the Ovshinsky scale of construction is many but alloy amount that is that dissolve in wherein is relatively less, and the Critical cooling speed of martensitic transformation and the lower transformation Critical cooling speed of bainite transformation improve, under the rate of cooling that annealing furnace is limited, not easily obtain bainite and martensite.
In continuous annealing line slow cooling section, steel band is cooled to 700 ~ 730 DEG C from soaking temperature, rate of cooling is 1 ~ 5 DEG C/s, is for regulating austenitic quantity and distribution in steel, improving the distributional pattern of alloying element in austenite and ferrite.Rapid cooling section is with the rate of cooling of 25 ~ 50 DEG C/s, steel plate is cooled to 320 ~ 360 DEG C, for avoiding perlitic transformation, in guarantee, the bainite and martensite of low temperature changes, overaging 440 ~ 920s after steel plate rapid cooling, make martensite self-tempering, coordinate and ferritic difference of hardness, improve the plasticity of steel plate.
Beneficial effect of the present invention: by the content of control C, Mn element during smelting, reduce Si content, and compound adds a certain amount of Nb and Ti element, obtains the excellent hot-rolled substrate of rational hot rolling microstructure and surface and plate shape by controlled rolling and controlled cooling during hot rolling; The slow cooling after soaking and rapid cooling section twice type of cooling is adopted when continuous annealing, finally obtain yield strength and be greater than 500MPa, tensile strength is at more than 600MPa, elongation after fracture is greater than 19%, yield tensile ratio is greater than 0.8, the cold-reduced sheet of the high-yield-ratio high-ductility of thickness between 0.5 ~ 2.5mm, the cold-reduced sheet of manufacture can be used as automobile stiffener and structural part, meets the requirement of body of a motor car to strength and stiffness.Can be used as the structural part of automobile, as the stiffener etc. of automobile longitudinal girder, door anti-collision joist, center pillar lower reinforcing plate and collision bumper.
Accompanying drawing explanation
Fig. 1 is the microstructure picture of embodiment hot-rolled sheet;
Fig. 2 is the microstructure of the cold rolled annealed steel plate of embodiment;
Fig. 3 is the precipitate in the ferrite in embodiment hot-rolled sheet tissue;
Fig. 4 is the transmission electron microscope photo of the cold rolled annealed steel plate of embodiment.
Embodiment
Below by some embodiments, the present invention is further described.The composition of embodiment steel is in table 1, and hot-rolled process parameter is in table 2, and continuous annealing process parameter is in table 3, and the mechanical property of continuous annealing steel plate is in table 4.The hot-rolled sheet microstructure of embodiment 1 is shown in Fig. 1, and the microstructure of cold rolled annealed plate is shown in Fig. 2, and the precipitate in hot rolling fire plate is shown in Fig. 3, the transmission electron microscope photo of cold rolled annealed plate is shown in Fig. 4.
Chemical composition (massfraction) % of table 1 embodiment steel
| Embodiment | C | Si | Mn | P | S | Al | N | Nb | Ti | Nb+Ti |
| 1 | 0.06 | 0.02 | 1.90 | 0.010 | 0.007 | 0.10 | 0.0050 | 0.020 | 0.025 | 0.045 |
| 2 | 0.08 | 0.09 | 1.72 | 0.009 | 0.010 | 0.02 | 0.0030 | 0.025 | 0.035 | 0.060 |
| 3 | 0.09 | 0.05 | 1.80 | 0.007 | 0.006 | 0.05 | 0.0020 | 0.030 | 0.035 | 0.065 |
| 4 | 0.10 | 0.08 | 1.85 | 0.012 | 0.005 | 0.04 | 0.0050 | 0.045 | 0.055 | 0.100 |
| 5 | 0.11 | 0.04 | 1.63 | 0.008 | 0.009 | 0.08 | 0.0045 | 0.035 | 0.045 | 0.080 |
| 6 | 0.12 | 0.07 | 1.50 | 0.011 | 0.006 | 0.03 | 0.0036 | 0.040 | 0.050 | 0.090 |
| 7 | 0.07 | 0.10 | 2.00 | 0.014 | 0.004 | 0.06 | 0.0050 | 0.015 | 0.020 | 0.035 |
| 8 | 0.09 | 0.07 | 1.65 | 0.009 | 0.003 | 0.07 | 0.0028 | 0.025 | 0.045 | 0.070 |
| 9 | 0.08 | 0.06 | 1.70 | 0.008 | 0.005 | 0.06 | 0.0026 | 0.035 | 0.040 | 0.075 |
| 10 | 0.12 | 0.03 | 1.40 | 0.015 | 0.008 | 0.09 | 0.0040 | 0.030 | 0.025 | 0.055 |
The rolling technological parameter of table 2 embodiment steel
The continuous annealing process parameter of table 3 embodiment steel
The mechanical property of table 4 embodiment steel annealed sheet
By the chemical composition of the present invention's design, the steel of embodiment is through smelting continuous casting, slab thickness is for being 230mm, and according to the hot rolling technology controlled rolling and controlled cooling of setting, obtaining thickness is 2.0 ~ 6.5mm, plate shape and the good hot-rolled sheet of surface quality, hot-rolled sheet tissue is made up of ferrite and pearlite, and ferrite grain size is tiny, and the Carbonitride Precipitation thing of the niobium titanium having a large amount of small and dispersed to distribute, play reinforced ferrite effect, finally effectively improve the yield strength of annealed sheet steel.Hot-rolled sheet becomes the substrate of 0.5 ~ 2.5mm through pickling and cold-rolling, then anneals on continuous annealing line, and the steel plate finally obtained is made up of ferrite and tempered martensite and a small amount of bainite, and its tensile strength is reached for more than 600MPa, yield tensile ratio R
p0.2/ R
m>=0.80, strength and ductility mates good cold-rolled steel sheet.
Claims (3)
1. a 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet, it is characterized in that composition is C:0.06% ~ 0.12%, Si:0.02% ~ 0.10%, Mn:1.40% ~ 2.00%, P by mass percentage :≤0.015%, S :≤0.010%, Al:0.02% ~ 0.10%, N :≤0.0050%, Nb:0.015% ~ 0.045%, Ti:0.020% ~ 0.055% and meet 0.035%≤Nb+Ti≤0.100%, surplus is Fe and some other inevitable impurity.
2. a kind of 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet according to claim 1, it is characterized in that composition is C:0.08% ~ 0.10%, Si:0.05% ~ 0.07%, Mn:1.60% ~ 1.80%, P by mass percentage :≤0.010%, S :≤0.005%, Al:0.05% ~ 0.08%, N :≤0.0030%, Nb:0.025% ~ 0.035%, Ti:0.035% ~ 0.045%, and meet 0.060%≤Nb+Ti≤0.080%, surplus is Fe and some other inevitable impurity.
3. a 600MPa level high-yield-ratio high-ductility cold-rolled steel sheet manufacture method according to claim 1 and 2, comprise converter smelting, cast after external refining, anneal on hot continuous rolling, pickling and cold-rolling, continuous annealing furnace, smooth, it is characterized in that, during hot continuous rolling, by heating of plate blank to 1200 ~ 1300 DEG C, insulation 120-180min, finish rolling start rolling temperature is 1000 ~ 1100 DEG C, finishing temperature is 890 ~ 950 DEG C, coiling temperature 600 ~ 650 DEG C, obtains the hot-rolled coil that microstructure is ferrite and pearlite, and hot-rolled coil thickness is 2.0 ~ 6.5mm; In described pickling and cold-rolling, cold rolling draft is 60 ~ 80%, and cold rolling coil plate thickness is 0.5 ~ 2.5mm; In described anneal, steel band is 790 ~ 850 DEG C in the holding-zone temperature of annealing furnace, and soaking soaking time is 110 ~ 240s; After steel band insulation, two-stage cooling is cooled fast after adopting first Slow cooling, steel band is cooled to 700-730 DEG C from holding temperature by slow cooling section, rate of cooling is 1 ~ 5 DEG C/s, steel band is cooled to 320 ~ 360 DEG C with the rate of cooling of 25 ~ 50 DEG C/s by rapid cooling section, then at 320 ~ 360 DEG C, carry out Wetted constructures, overaging time 440 ~ 920s, air-cooledly after timeliness, smooth to batch.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410256779.3A CN105274432B (en) | 2014-06-11 | 2014-06-11 | 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410256779.3A CN105274432B (en) | 2014-06-11 | 2014-06-11 | 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof |
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| Publication Number | Publication Date |
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| CN105274432A true CN105274432A (en) | 2016-01-27 |
| CN105274432B CN105274432B (en) | 2017-04-26 |
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| CN106756547A (en) * | 2016-12-12 | 2017-05-31 | 东北大学 | A kind of yield strength 500MPa grades of cold-rolled steel sheet and preparation method thereof |
| CN107012392A (en) * | 2017-05-15 | 2017-08-04 | 河钢股份有限公司邯郸分公司 | A kind of 600MPa grade high-strengths low-alloy cold-strip steel and its production method |
| CN107164700A (en) * | 2017-05-27 | 2017-09-15 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacture method |
| CN107460404A (en) * | 2017-07-17 | 2017-12-12 | 河钢股份有限公司 | A kind of yield strength 800MPa ultra-high strength strip steels and preparation method thereof |
| CN109023053A (en) * | 2018-08-14 | 2018-12-18 | 武汉钢铁有限公司 | A kind of 600MPa grade multi-phase Steels and production method with good flange performance |
| CN109898017A (en) * | 2019-03-01 | 2019-06-18 | 鞍钢股份有限公司 | Cold-rolled dual-phase steel with excellent 1000 MPa-level cold bending performance and production method thereof |
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| CN106756547B (en) * | 2016-12-12 | 2018-10-23 | 东北大学 | A kind of yield strength 500MPa grades of cold-rolled steel sheets and preparation method thereof |
| CN106756547A (en) * | 2016-12-12 | 2017-05-31 | 东北大学 | A kind of yield strength 500MPa grades of cold-rolled steel sheet and preparation method thereof |
| CN107012392A (en) * | 2017-05-15 | 2017-08-04 | 河钢股份有限公司邯郸分公司 | A kind of 600MPa grade high-strengths low-alloy cold-strip steel and its production method |
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| CN107460404B (en) * | 2017-07-17 | 2019-05-17 | 河钢股份有限公司 | A kind of yield strength 800MPa ultra-high strength strip steel and preparation method thereof |
| CN109023053B (en) * | 2018-08-14 | 2020-01-14 | 武汉钢铁有限公司 | 600 MPa-grade multi-phase steel with good flanging performance and production method thereof |
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| WO2020103927A1 (en) * | 2018-11-23 | 2020-05-28 | 宝山钢铁股份有限公司 | High-yield-ratio cold-rolled dual-phase steel and manufacturing method therefor |
| CN111218620B (en) * | 2018-11-23 | 2021-10-22 | 宝山钢铁股份有限公司 | High-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof |
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| CN111218620A (en) * | 2018-11-23 | 2020-06-02 | 宝山钢铁股份有限公司 | High-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof |
| JP2022507855A (en) * | 2018-11-23 | 2022-01-18 | 宝山鋼鉄股▲分▼有限公司 | High yield ratio cold rolled duplex stainless steel and its manufacturing method |
| CN110004854A (en) * | 2019-01-21 | 2019-07-12 | 北京中交畅观科技发展有限公司 | Three (A) grade degree of protection highway barriers of one kind and its manufacturing method |
| CN109898017A (en) * | 2019-03-01 | 2019-06-18 | 鞍钢股份有限公司 | Cold-rolled dual-phase steel with excellent 1000 MPa-level cold bending performance and production method thereof |
| CN109988969A (en) * | 2019-04-01 | 2019-07-09 | 山东钢铁集团日照有限公司 | A kind of cold rolling Q&P1180 steel and its production method with different yield tensile ratios |
| CN109988969B (en) * | 2019-04-01 | 2021-09-14 | 山东钢铁集团日照有限公司 | Cold-rolled Q & P1180 steel with different yield ratios and production method thereof |
| CN111763875A (en) * | 2019-04-02 | 2020-10-13 | 上海梅山钢铁股份有限公司 | High-hardness cold-rolled electrotinning substrate for bottle cap and production method thereof |
| CN110527923B (en) * | 2019-06-03 | 2021-10-26 | 武汉钢铁有限公司 | High-yield-ratio structural steel for 600 MPa-grade automobile body and production method thereof |
| CN110527923A (en) * | 2019-06-03 | 2019-12-03 | 武汉钢铁有限公司 | A kind of 600MPa grades of body of a motor car high-yield-ratio structural steel and production method |
| CN112680655A (en) * | 2020-11-27 | 2021-04-20 | 邯郸钢铁集团有限责任公司 | 700 MPa-grade low-alloy high-strength cold-rolled steel plate for automobile and preparation method thereof |
| CN112680655B (en) * | 2020-11-27 | 2022-06-14 | 邯郸钢铁集团有限责任公司 | 700 MPa-grade low-alloy high-strength cold-rolled steel plate for automobile and preparation method thereof |
| CN113403541A (en) * | 2021-06-22 | 2021-09-17 | 攀钢集团攀枝花钢铁研究院有限公司 | 550 MPa-level low-alloy high-strength cold-rolled steel plate and production method thereof |
| CN113403540A (en) * | 2021-06-22 | 2021-09-17 | 攀钢集团攀枝花钢铁研究院有限公司 | 500 MPa-level low-alloy high-strength cold-rolled steel plate and production method thereof |
| CN113403543A (en) * | 2021-06-23 | 2021-09-17 | 宝钢湛江钢铁有限公司 | 60 kilogram-grade low-silicon easy-welding cold-rolled low-alloy high-strength steel plate and production method thereof |
| CN115679193A (en) * | 2021-07-29 | 2023-02-03 | 宝山钢铁股份有限公司 | Steel for cold-rolled flexible pipe with yield strength of more than 750MPa and manufacturing method thereof |
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