CN109097705A - A kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production method - Google Patents

A kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production method Download PDF

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Publication number
CN109097705A
CN109097705A CN201811126345.6A CN201811126345A CN109097705A CN 109097705 A CN109097705 A CN 109097705A CN 201811126345 A CN201811126345 A CN 201811126345A CN 109097705 A CN109097705 A CN 109097705A
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cold
steel
temperature
production method
rolling
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CN109097705B (en
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谭文
潘利波
王俊霖
孙伟华
周文强
方芳
祝洪川
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Wuhan Iron and Steel Co Ltd
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Wuhan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips

Abstract

The invention discloses a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steels, its material chemical component mass percent (%) are as follows: C 0.05%-0.10%, Mn 1.60%-2.30%, Als 0.010-1.0%, Si 0.10%-0.60%, Nb 0.010-0.050%, Cr 0.05-0.30%, Mo 0.05-0.30%, P≤0.015%, S≤0.010%, N≤0.008%, remaining is Fe and inevitable impurity, and precious metal element Cr and Mo meet relational expression: 0.05≤Cr+Mo≤0.30, and C+Si/30+Mn/20≤0.22.The production method of the hot dip galvanizing automobile wheel cover steel includes smelting, continuous casting, heating, and hot rolling is cooling, is batched, pickling, cold rolling, annealing and coating step.Expensive alloying elements addition is few in the cold-rolled galvanized duplex steel obtained according to the present invention, and product has good mechanical property, surface quality, forming property and welding performance, and the present invention can produce in existing conventional producing line, increase equipment without additional.

Description

A kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production method
Technical field
The present invention relates to a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production methods, belong to cold rolling hot dip galvanizing automobile With super-high strength steel manufacturing field.
Background technique
In recent years, with the propulsion of energy-saving and emission-reduction technology of vehicles, automotive light weight technology becomes a kind of development trend.780MPa grades Or more super-high strength steel be one of developing direction of light weight material in automobile, due to ferrite+martensite two-phase high-strength steel tool Have good strong plasticity, low yield strength ratio, high initial work hardening rate, good baking hardenability and be used widely.With it is common The high-strength dual phase steel of cold rolling is compared, and Galvanized Dual Phase Steel also has good corrosion resistance, thus be widely used in door anti-collision joist, The automobile structures such as longitudinal beam reinforcing plate, guide groove stiffening plate.
For mechanical property, welding performance, forming property and the surface quality etc. for guaranteeing the zinc-plated strong dual phase steel of superelevation, currently 800MPa grades of Galvanized Dual Phase Steel ingredient designs use the component system of the low silicon of manganese in low-carbon, and compound addition higher Cr, Mo, V Deng more valuable alloying element.Production process route uses the process flow of the zinc-plated annealing of steel making, continuous casting and hot rolling-cold rolling-.
Conventionally, as it is added to higher alloying elements cr, Mo (Cr+Mo content is generally 0.3 or more) etc., Cause cost of alloy higher, and in order to control the surface quality of product, the Si content general control in steel is below 0.05%.For Cost of alloy is reduced, also has technology and produces 800MPa grades of dual phase steels using 0.40% or more Si, but is contained using higher Si For amount when being produced, producing line need to have the function of pre-oxidation or straight fire heating, with solve due to external oxidation leads to zinc-plated when leakage Plating problem, to produce the galvanizing production of great surface quality, therefore the conventional producing line for not having straight fiery heating function, it is difficult to Produce the galvanizing production of great surface quality.It is asked in addition, existing product also will appear forming cracking etc. during user's use Topic.
Bibliography:
A kind of 1.CN 106399857A: production method of the tensile strength 800MPa grades of cold-rolled galvanized duplex steels containing Si；
A kind of 2.CN 106011631A: 800MPa grades of low-carbon hot dip galvanized dual phase steel and preparation method thereof；
A kind of 3.CN 102433509A: 780MPa grade cold rolling hot dip galvanizing dual phase steel and preparation method thereof；
4.CN 105441805A: a kind of 800MPa grades of car Galvanized Dual Phase Steel and production method；
5.CN 1782116A: a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its manufacturing method.
Summary of the invention
The present invention is intended to provide a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production method, solve in the prior art Existing expensive alloying elements Cr, Mo, V addition is more, causes higher cost；In the conventional producing line production for not having straight fire heating When upper Galvanized Dual Phase Steel higher containing Si, to surface quality problems occur；And existing product formability in forming process Can be lower, there are the technical problems such as cracking.The expensive alloying elements addition of cold-rolled galvanized duplex steel of the present invention is few, product Have good mechanical property, surface quality, forming property and welding performance, and the present invention can be enterprising in existing conventional producing line Row production increases equipment without additional.
The present invention relates to a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel, material chemical component mass percents (%) Are as follows: C 0.05%-0.10%, Mn 1.60%-2.30%, Als 0.010-1.0%, Si 0.10%-0.60%, Nb 0.010-0.050%, Cr 0.05-0.30%, Mo 0.05-0.30%, P≤0.015%, S≤0.010%, N≤0.008%, Remaining is Fe and inevitable impurity, and precious metal element Cr and Mo meet relational expression: 0.05≤Cr+Mo≤0.30, and C +Si/30+Mn/20≤0.22。
On the other hand, the invention further relates to a kind of production methods of 800MPa grade cold rolling hot dip galvanizing dual phase steel, including smelt, Continuous casting, heating, hot rolling is cooling, batches, pickling, cold rolling, annealing and coating step, it is characterised in that:
1) molten steel is refined using refining routes such as RH, LF in the smelting step；
2) it in the continuous casting step, casts 15-30 DEG C of the degree of superheat；
3) in the heating of plate blank step, 1180-1300 DEG C of slab tapping temperature, heating time 150min-300min；
4) in the hot-rolled step, 850-950 DEG C of hot rolling finishing temperature；
5) in the cooling step, when belt steel temperature >=620 DEG C or more, average cooling rate >=15 DEG C/s of strip；
6) described to batch in step, 500-620 DEG C of coiling temperature；
7) in the pickling and cold-rolling step, cold rolling reduction ratio is controlled in 40%-70%；
8) in the continuous annealing step, 760-840 DEG C of annealing temperature, wherein heating speed≤5 of temperature≤760 DEG C DEG C/s, 760-840 DEG C of soaking time 60-300s, cooling velocity >=15 DEG C/s, 0~-40 DEG C of dew point in annealing furnace, H in furnace2Contain Amount is 1-5%, H2O/H2≤1.0；
9) in the coating step, strip enters 440-500 DEG C of zinc pot temperature, and 450-470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15-0.25%.
The detailed description of the invention
The present invention provides a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel, material chemical component mass percent (%) Are as follows: C 0.05%-0.10%, Mn 1.60%-2.30%, Als 0.010-1.0%, Si 0.10%-0.60%, Nb 0.010-0.050%, Cr 0.05-0.30%, Mo 0.05-0.30%, P≤0.015%, S≤0.010%, N≤0.008%, Remaining is Fe and inevitable impurity, and precious metal element Cr and Mo meet relational expression: 0.05≤Cr+Mo≤0.30, and C +Si/30+Mn/20≤0.22。
Cold-rolled galvanized duplex steel according to the present invention, chemical component can also include in Ti, Ca, Ni, Cu, B At least one or more than one elements, ingredient percent (%) are as follows: Ti 0.005-0.030%, Ca 0.0001- 0.10%, Ni 0.03-0.20%, Cu 0.03-0.30%, B 0.0005-0.0050%.
It is the effect and its restriction explanation of main component according to the present invention below:
Carbon: carbon plays solution strengthening effect in steel, or with carbide formers such as Nb, Ti, Mo in steel to form MC thin Little particle plays the role of precipitation strength and refinement crystal grain, improves the intensity of steel.Carbon content also influences containing for martensite in steel Amount and intensity, while excessively high carbon content reduces the welding performance of steel, therefore comprehensively considers, the C element content in steel limits It is 0.05%~0.10%.
Manganese: manganese plays solution strengthening and stable austenite in steel, improves harden ability, and content is too low, invigoration effect Too small, austenite is unstable.Mn too high levels are easy to form macrosegregation in strip mid-depth, reduce toughness of products, molding It is easy to cause cracking, while Mn too high levels in the process, the cost of alloy of product dramatically increases, therefore Mn constituent content of the present invention It is limited to 1.50~2.30%.
Silicon: silicon plays significant solution strengthening effect in steel, and in phase transition process, effectively inhibits the precipitation of carbide, Perlitic transformation etc. is postponed, Si content is too low, inhibits the effect of Carbide Precipitation and perlitic transformation unobvious, but Si content mistake Height is easy to form the iron sheet for being difficult to remove in hot rolling, and finally remains in product surface, seriously affects surface quality, therefore Si constituent content of the present invention is limited to 0.10~0.60%.
Aluminium: aluminium is strong deoxidier, can effectively reduce the residual oxygen in steel, reduces the content of steel inclusion, adds excessive Als is easy to cause to be difficult to the problems such as casting.Therefore Als constituent content is limited to 0.01~1.0% in the present invention.
Sulphur: sulphur is the impurity element in steel, easily generates segregation in crystal boundary, and the FeS of low melting point, drop are formed with the Fe in steel The toughness of low steel, when steel-making, should sufficiently remove, by the control of S constituent content below 0.010%.
Phosphorus: phosphorus is the impurity element in steel, is easy to influence the toughness of product in crystal boundary segregation, thus its content it is more low more It is good.According to practical controlled level, S constituent content should be controlled below 0.015%.
Nitrogen: nitrogen is the impurity element in steel, reduces the toughness of steel, is easy and the shapes nitride grains such as Al, Nb, Ti in steel Son, too high levels easily form coarse AlN and TiN and reduce the toughness of steel, therefore reduce its content as far as possible, N element is contained Amount control is below 0.008%.
Chromium: chromium is remarkably improved the harden ability of steel, and has the function of inhibiting Carbide Precipitation and perlitic transformation, has Conducive to the formation for promoting martensite in dual phase steel, but the too high increase cost of content, therefore Cr constituent content is limited in the present invention 0.05~0.30%.
Molybdenum: molybdenum is remarkably improved the harden ability of steel, and inhibits the effect of perlitic transformation and bainite transformation, and Mo contains The excessively high manufacturing cost that can dramatically increase steel is measured, therefore Mo constituent content is limited to 0.05~0.30% in the present invention.
Niobium: niobium can significantly refine ferrite crystal grain in steel, improve the intensity and toughness of steel, also first with C, N in steel etc. Element forms the particles such as NbC, NbN, plays the role of significant precipitation strength, improves steel strength, but Nb too high levels will increase The manufacturing cost of steel, therefore Nb constituent content is limited to 0.01~0.05% in the present invention.
Titanium: titanium plays solution strengthening effect in steel, and Ti forms TiC and TiN in conjunction with C, N in steel, and it is strong to play precipitation The effect of change.But Ti too high levels bring increased costs, therefore Ti constituent content is limited to 0.005 in the present invention~ 0.030%.
Calcium: the calcium of certain content can improve the state of steel inclusion, to be conducive to improve the toughness of steel, therefore this hair It is bright middle Ca constituent content to be limited to 0.0001-0.10%.
Nickel: nickel is solution strengthening element in steel, and the inoxidizability and corrosion resistance of steel, but Ni can be improved in the Ni of certain content It is expensive, therefore Ni constituent content is 0.03-0.20% in the present invention.
Copper: copper plays the role of solution strengthening and precipitation strength in steel, but the excessively high Surface Quality of Cu generates unfavorable shadow It rings, and due to expensive, Cu constituent content is 0.03~0.30% in the present invention.
Boron: boron has the function of raising austenite harden ability, the formation of martensite in dual phase steel is effectively facilitated, in steel N is combined and is formed BN, plays the role of precipitation strength, but B content is excessively high can make steel degraded toughness, and will increase the manufacture of steel Cost, therefore B element content is limited to 0.0005~0.0050% in the present invention.
The internal microstructure of herein described cold-rolled galvanized duplex steel be ferrite+martensitic structure, grain size >= 13 grades, which can guarantee that the cold-rolled galvanized duplex steel has good mechanical property, surface quality, forming property And welding performance.
In the present patent application, it is designed using low-carbon-equivalent, and adds Si appropriate, and reduce the conjunction of Cr, Mo precious metal The use of gold element, substantially reduces cost of alloy, and finished steel is made to have good welding performance, and above element comprehensive function is protected The mechanical property of card finished steel can reach: tensile strength >=800MPa, yield strength >=450MPa, elongation percentage A80 >=16%, The value >=0.12%, r of n10~20% value >=0.70, hole expansibility >=30%.
The present invention also provides a kind of production methods of 800MPa grade cold rolling hot dip galvanizing dual phase steel, including smelt, and continuous casting adds Heat, hot rolling is cooling, batches, pickling, cold rolling, annealing and coating step, it is characterised in that:
1) molten steel is refined using refining routes such as RH, LF in the smelting step；
2) it in the continuous casting step, casts 15-30 DEG C of the degree of superheat；
3) in the heating of plate blank step, 1180-1300 DEG C of slab tapping temperature, heating time 150min-300min；
4) in the hot-rolled step, 850-950 DEG C of hot rolling finishing temperature；
5) in the cooling step, when belt steel temperature >=620 DEG C or more, average cooling rate >=15 DEG C/s of strip；
6) described to batch in step, 500-620 DEG C of coiling temperature；
7) in the pickling and cold-rolling step, cold rolling reduction ratio is controlled in 40%-70%；
8) in the continuous annealing step, 760-840 DEG C of annealing temperature, wherein heating speed≤5 of temperature≤760 DEG C DEG C/s, 760-840 DEG C of soaking time 60-300s, cooling velocity >=15 DEG C/s, 0~-40 DEG C of dew point in annealing furnace, H in furnace2Contain Amount is 1-5%, H2O/H2≤1.0；
9) in the coating step, strip enters 440-500 DEG C of zinc pot temperature, and 450-470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15-0.25%.
The production method of the cold-rolled galvanized duplex steel according to the present invention, since the alloying element that the method is related to contains Measure higher, the continuous casting in step 2) can reduce segregation using 15-30 DEG C of degree of superheat control, improve slab ingredient and The uniformity finally organized improves forming property.
The production method of the cold-rolled galvanized duplex steel according to the present invention, slab heating temperature described in step 3) use 1180-1300 DEG C, board briquette is unfavorable for alloying element in steel lower than 1180 DEG C and homogenizes, and causes ingredient and microstructure segregation, adds Hot temperature is higher than 1300 DEG C, the surface Fe easy to form for being difficult to remove2SiO4, product surface quality is made to be deteriorated.Heating time 150min-300min, the time is too short, and alloying element is difficult to sufficiently spread in slab, causes ingredient and microstructure segregation, time mistake It is long, it be easy to cause surface iron sheet to thicken and formed the Fe for being difficult to remove2SiO4, and decarburization is caused, reduce product strength.
Preferably, it is the abundant diffusion for guaranteeing alloying element, should ensure that heating time of the slab at 1200 DEG C or more For 40-100min.
It is highly preferred that the slab is 50-90min in 1200 DEG C or more of heating time.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 4), finishing temperature in course of hot rolling It is lower to be easy to form non-uniform tissue in steel, and higher coarse grain structure easy to form, it is unfavorable for the power of product Performance is learned, therefore hot rolling finishing temperature of the present invention is limited to 850-950 DEG C.
Preferably, the hot rolling finishing temperature is 860-900 DEG C.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 5), in 620 DEG C or more of cooling speed Degree is easy to form first coarse uneven ferritic structure in steel lower than 15 DEG C/s, causes performance especially elongation percentage of product etc. Toughness index decline.
Preferably, average cooling rate >=20 DEG C/s of the strip.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 6), coiling temperature is excessively high, is easy to make It is shaped to coarse ferrite and pearlite tissue, is unfavorable for the raising of toughness of products index, and coiling temperature is too low, is easy to lead The edge crack of product and increase rolling load etc. during refrigeration is rolled, therefore coiling temperature is 500~620 DEG C in the present invention.
Preferably, the coiling temperature is 540~600 DEG C.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 7), the cold rolling of 40% or more use Reduction ratio can sufficiently be crushed hot rolling microstructure, and the fine microstructures after making continuous annealing are uniform, and cold rolling reduction ratio is too big, be easy to cause rolling Load is too big, unfavorable to plate shape and quality of edges control, and therefore, in the present invention, cold rolling reduction ratio is controlled 40%~70%.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 8), annealing temperature is too low, cold rolling group Sufficient Recovery and recrystallization cannot be occurred by knitting, and form non-uniform tissue, unfavorable to the extension and forming property of product, temperature It is too high, coarse heterogeneous structure easy to form, and be easy to facilitate surface external oxidation, it is unfavorable to final paintability, therefore this 760-840 DEG C of invention annealing temperature if the heating speed of temperature≤760 DEG C is too high, is not easy shape during heating in steel At martensite annular tissue, forming property is lower, therefore heating speed≤5 DEG C of annealing temperature≤760 DEG C of the present invention/s.
Preferably, the heating speed of annealing temperature≤760 DEG C is 1-4.5 DEG C/s.
Soaking time when annealing is too short, and sufficient Recovery and recrystallization, unevenness easy to form cannot occur for cold rolling microstructure Even tissue has a significant impact the toughness indexs such as elongation percentage, forming property is caused to reduce, and soaking time is too long, easy to form Coarse tissue, and surface peroxidating easy to form causes surface quality to decline, therefore annealing temperature of the present invention is 760-840 DEG C when, soaking time 60-300s.
Preferably, the annealing temperature be 760-820 DEG C when, the soaking time be 60-250s, the cooling velocity >= 15℃/s。
Cooling velocity after annealing is lower than 15 DEG C/s, is easy excessive ferrite and pearlite in steel, causes steel strength It reduces, therefore cooling velocity >=15 DEG C of the invention/s.
The production method of the cold-rolled galvanized duplex steel according to the present invention, in step 8), the present invention is controlled in annealing furnace 0~-40 DEG C of dew point, hydrogen content H in furnace21~5%, 0.1≤H2O/H2≤ 1.0, dew point is too high to need special equipment, and Dew point is too high to be easy to cause external oxidation and decarburization serious, so that galvanizing production the surface defects such as plating leakage is occurred, and make under product strength Drop, and dew point is too low is not easily accomplished, and dew point is too low is easily formed external oxidation, and the higher product containing Si is made plating leakage etc. occur Defect, H2The too low external oxidation for also be easy to causeing belt steel surface of content, and too high increase cost, therefore annealing furnace H of the present invention21 ~5%；H2O/H2Ratio is too low and too high be easy to cause external oxidation, therefore 0.1≤H in the present invention2O/H2≤1.0。
Preferably, dew point is -5~-35 DEG C in the annealing furnace, H in furnace2Content is in 1~4%, H2O/H2For 0.2~ 1.0。
The cold-rolled galvanized duplex steel of the method preparation has the advantage that compared with the prior art according to the present invention
(1) present invention adds Si appropriate, and reduces the use of Cr, Mo noble metal alloy element, substantially reduces alloy Cost, and each segment process parameters such as hot rolling heats, cools down, batches, cold rolling is heated, cooled down are controlled, make product not only tensile strength Reach 800MPa or more, while there is high elongation percentage, n, r, hole expansibility, the forming property of product greatly improves；
(2) increase bring cosmetic issue to solve Si, by using lower coiling temperature, and reduce existing annealing and produce H2 content in line, dew point control the ratio of the H2O/H2 in annealing furnace, so that product of the invention has good paintability And surface quality, in the process, the more existing producing line of H2 usage amount further decreases, and production cost further decreases；
(3) present invention is designed using low-carbon-equivalent, and product has good welding performance；
(4) production technology of the present invention can be realized on existing production line, increase equipment and investment etc. without additional；
(5) mechanical property of product of the present invention can reach: tensile strength >=800MPa, yield strength >=450MPa, extend The rate value >=0.12%, r of A80 >=16%, n10~20% value >=0.70, hole expansibility >=30%.
Detailed description of the invention
Fig. 1 is the metallographic microstructure photo of cold-rolled galvanized duplex steel of the present invention.
Specific embodiment
Below in conjunction with specific embodiment and embodiment, it is specifically described the present invention, advantages of the present invention and various effects It thus will clearly present.It will be understood by those skilled in the art that these specific embodiments and embodiment are for illustrating The present invention is not intended to limit the present invention.
Throughout the specification, unless otherwise specified, terms used herein are interpreted as usual in this field Used meaning.Therefore, unless otherwise defined, all technical and scientific terms used herein has leads with belonging to the present invention The identical meaning of the general understanding of field technique personnel.Contradiction if it exists, this specification are preferential.
It is the example explanation of cold-rolled galvanized duplex steel produced by the invention below:
Embodiment 1-6:
Various embodiments of the present invention follow the steps below production (smelting, continuous casting → heating or soaking → rolling → laminar flow Cool down → batch → pickling → cold rolling → continuous annealing → zinc-plated → finished product)
1) smelt, continuous casting: slab pulling rate 0.1-10.0m/min, 15-30 DEG C of the degree of superheat, specific ladle chemistry is as follows (wt%) shown in table 1；
2) above-mentioned slab is heated, 1180-1300 DEG C of slab tapping temperature, heating time 150-300min, wherein 1200 DEG C or more of heating time 40-120min；
3) hot rolling: 850-950 DEG C of hot rolling finishing temperature, preferably 860-900 DEG C；
4) cooling: when belt steel temperature >=620 DEG C or more, average cooling rate >=15 DEG C/s of strip；
5) it batches: 500-620 DEG C of coiling temperature, preferably 540-600 DEG C；
6) pickling；
7) cold rolling: cold rolling reduction ratio is controlled in 40%-70%；
The main rolling technological parameter such as hot rolling and cold rolling is as shown in table 2 below；
8) continuous annealing: 760-840 DEG C of annealing temperature, wherein heating speed≤5 DEG C of temperature≤760 DEG C/s, 760~ 840 DEG C of 60~300s of soaking time, the strip after heat preservation are cooled down, cooling velocity >=15 DEG C/s, and dew point 0 in annealing furnace~- 40 DEG C, hydrogen content H in furnace21~5%, 0.10≤H2O/H2≤ 1.0, parameter and annealing is as shown in table 3 below；
9) hot galvanizing: strip enters 440-500 DEG C of temperature when zinc pot, and 450-470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15-0.25%.
The cold-rolled galvanized duplex steel finished product mechanical property of 1-6 of embodiment of the present invention production, as shown in table 4.
The chemical component of molten steel, Wt% in 1. embodiment 1-6 of table
The main rolling technological parameter such as hot rolling and cold rolling in 2. embodiment 1-6 of table
Parameter and annealing in 3 embodiment 1-6 of table
Cold-rolled galvanized duplex steel detects finished product mechanical property in 4 embodiment 1-6 of table
From table 4, it can be seen that the product tensile strength of 1-6 of the embodiment of the present invention is up to 815MPa or more；Elongation percentage A80 reaches 18% or more, reach 30%, n in embodiment 610~20%Reach 0.12 or more, embodiment 6 has reached 0.17, r value and reached 0.75 or more, embodiment 6 has reached 1.0, and hole expansibility has reached 34% or more, and embodiment 2 has reached 50%；The surface of implementation column Quality and welding performance are good, but the precious alloy Cr+Mo content of 1-6 of the embodiment of the present invention is below 0.30.Comparative example 1-3 It is less than 40min in 1200 DEG C or more heating times when heating, the segregation that will lead in steel aggravates, elongation percentage, reaming to steel The forming properties such as rate are unfavorable, and the cooling velocity after 1 finish to gauge of comparative example is lower than 15 DEG C/s, and the coiling temperature of comparative example 2 and 3 is 620 DEG C or more, it is easily formed unevenly with coarse microstructure, reduces the toughness and forming property of steel, comparative example 1-3 is in continuous annealing When average heating rate be greater than 5 DEG C/s, the soaking time of comparative example 1 and 2 is short, and 3 soaking time of comparative example is too long, is unfavorable for microcosmic The diffusion of the elements such as the Recovery and recrystallization and metallic element C, Mn, Cr, Si of tissue, will cause the nonuniform organization in steel, Banded structure is obvious, reduces steel toughness and forming property.Cooling rate of the comparative example 1 and 3 after continuous annealing soaking is lower than 15 DEG C/s, no Conducive to the formation of martensitic structure in steel, therefore the tensile strength of steel is relatively low.Dew point, the H of comparative example 1-32Content and H2O/ H2Ratio not within the scope of the present invention, therefore product it is final surface quality it is poor.In addition, the Cr+Mo content of comparative example 1-3 0.50 or more, comparative example 1 is since Si content is higher, and comparative example 3 is since carbon content and carbon equivalent are high, welding performance It is poor.
Although preferred embodiments of the present invention have been described, it is created once a person skilled in the art knows basic Property concept, then additional changes and modifications may be made to these embodiments.So it includes excellent that the following claims are intended to be interpreted as It selects embodiment and falls into all change and modification of the scope of the invention.Obviously, those skilled in the art can be to the present invention Carry out various modification and variations without departing from the spirit and scope of the present invention.If in this way, these modifications and changes of the present invention Within the scope of the claims of the present invention and its equivalent technology, then the present invention is also intended to encompass these modification and variations and exists It is interior.

Claims (10)

1. a kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel, material chemical component mass percent (%) are as follows: C 0.05%- 0.10%, Mn 1.60%-2.30%, Als 0.010-1.0%, Si 0.10%-0.60%, Nb 0.010-0.050%, Cr 0.05-0.30%, Mo 0.05-0.30%, P≤0.015%, S≤0.010%, N≤0.008%, remaining is Fe and can not keep away The impurity exempted from, and precious metal element Cr and Mo meet relational expression: 0.05≤Cr+Mo≤0.30, and C+Si/30+Mn/20≤ 0.22。
2. cold-rolled galvanized duplex steel as described in claim 1, which is characterized in that the chemistry of the cold-rolled galvanized duplex steel Ingredient further includes at least one of Ti, Ca, Ni, Cu, B or more than one elements, ingredient percent (%) are as follows: Ti 0.005-0.030%, Ca 0.0001-0.10%, Ni 0.03-0.20%, Cu 0.03-0.30%, B 0.0005- 0.0050%.
3. cold-rolled galvanized duplex steel as described in claim 1, which is characterized in that the inside of the cold-rolled galvanized duplex steel Microscopic structure is ferrite+martensite, ferrite grain size >=13 grade.
4. a kind of production method of 800MPa grade cold rolling hot dip galvanizing dual phase steel, including smelt, continuous casting, heating, hot rolling is cooling, volume It takes, pickling, cold rolling, annealing and coating step, it is characterised in that:
1) molten steel is refined using refining routes such as RH, LF in the smelting step, the ladle chemistry quality hundred Divide than as described in claim 1；
2) it in the continuous casting step, casts 15-30 DEG C of the degree of superheat；
3) in the heating of plate blank step, 1180-1300 DEG C of slab tapping temperature, heating time 150min-300min；
4) in the hot-rolled step, 850-950 DEG C of hot rolling finishing temperature；
5) in the cooling step, when belt steel temperature >=620 DEG C or more, average cooling rate >=15 DEG C/s of strip；
6) described to batch in step, 500-620 DEG C of coiling temperature；
7) in the pickling and cold-rolling step, cold rolling reduction ratio is controlled in 40%-70%；
8) in the continuous annealing step, 760-840 DEG C of annealing temperature, wherein heating speed≤5 DEG C of temperature≤760 DEG C/s, 760-840 DEG C of soaking time 60-300s, cooling velocity >=15 DEG C/s, 0~-40 DEG C of dew point in annealing furnace, H in furnace2Content is 1- 5%, H2O/H2≤1.0；
9) in the coating step, strip enters 440-500 DEG C of zinc pot temperature, and 450-470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15-0.25%.
5. cold-rolled galvanized duplex steel production method as claimed in claim 4, which is characterized in that slab described in step 3) is excellent The heating time for being selected in 1200 DEG C or more is 40-100min.
6. cold-rolled galvanized duplex steel production method as claimed in claim 5, which is characterized in that the slab more preferably exists 1200 DEG C or more of heating time is 50-90min.
7. cold-rolled galvanized duplex steel production method as claimed in claim 4, which is characterized in that hot rolling described in step 4) is whole Rolling temperature is preferably 860-900 DEG C.
8. cold-rolled galvanized duplex steel production method as claimed in claim 4, which is characterized in that strip described in step 5) Average cooling rate >=20 DEG C/s.
9. cold-rolled galvanized duplex steel production method as claimed in claim 4, which is characterized in that batch temperature described in step 6) Preferably 540~600 DEG C of degree.
10. cold-rolled galvanized duplex steel production method as claimed in claim 4, which is characterized in that anneal described in step 8) The heating speed of temperature≤760 DEG C is 1-4.5 DEG C/s；When the annealing temperature is 760-820 DEG C, the soaking time is 60- 250s, cooling velocity >=15 DEG C/s；Dew point is -5~-35 DEG C in the annealing furnace, H in furnace2Content is in 1~4%, H2O/ H2It is 0.2~1.0.
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