CN102796956B - High-strength thin band steel for cold forming and manufacturing method thereof - Google Patents
High-strength thin band steel for cold forming and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to high-strength thin band steel for cold forming and a manufacturing method thereof. The method comprises the following steps: after discharging a cast band from a crystal roll, cooling the cast band forcibly and uniformly in a mode of spraying dry ice under high pressure; quickly cooling the cast band to be below 1,280 DEG C at the cooling speed of 200-300 DEG C/s; performing austenite on-line recrystallization rolling, wherein the rolling temperature is 1,050 to 1,200 DEG C and the rolling reduction is 20 to 50 percent; and quickly cooling the band steel subjected to hot rolling in an anti-oxidation mode, wherein the anti-oxidation quick cooling speed is 80 to 200 DEG C/s and the reeling temperature is 500 to 600 DEG C. By the method, the high-strength thin band steel for automobile cold forming and with low yield strength and excellent stamping performance can be obtained, can be directly used in a mode of substituting heat for cold, cancels the cold rolling procedure and greatly reduces the production cost.
Description
Technical field
The invention belongs to continuous casting process, particularly the high-strength Thin Strip Steel of a kind of cold formability and manufacture method thereof.
Background technology
In traditional process Iron and Steel Production, tin (Sn) is typical residual element or harmful element in steel, in steelmaking process, to remove fully Sn very difficult and be very expensive, once contain Sn in steel, substantially cannot thoroughly eliminate, can only by dilution molten steel, reduce the content of Sn, these all cause the rising of steel products cost.
In recent years, continuous circulation utilization due to steel scrap, cause the content of the residual element such as Sn in steel to raise gradually, Sn in steel is easy segregation element, easily being enriched in crystal boundary causes defects i.e.cracks to occur, therefore in traditional technique, the content of Sn element is strictly controlled, and at ordinary construction, with in steel, the content of Sn is all had to clear and definite requirement: Sn(wt%)≤0.005%.
Therefore,, if can accomplish " turning harm into good " to residual element such as Sn in steel (particularly steel scrap), will produce active influence to whole metallurgical boundary; Can realize the effective utilization to existing steel scrap or low-quality ore resources inferior (high tin ore), promote the recycle of steel, reduce production costs, realize iron and steel industry Sustainable development.
Traditional Thin Strip Steel is mostly to be produced through multi-pass continuous rolling by the strand of the thick 70-200mm of reaching, tradition hot rolling technology flow process is: continuous casting+strand reheats insulation+roughing+finish rolling+cooling+batch, first by continuous casting, obtain the strand that thickness is 200mm left and right, after strand is reheated and is incubated, carry out again roughing and finish rolling, obtain the steel band that thickness is generally greater than 2mm, finally steel band is carried out to laminar flow cooling and batch, complete whole hot rolling production process.If produce thickness be less than 1.5mm(containing) steel band, difficulty is relatively large, conventionally will carry out hot rolled strip follow-up cold rolling and annealed.And technical process is long, energy consumption is high, unit equipment is many, capital construction cost is high, causes production cost higher.
Continuous casting and rolling technique of sheet bar flow process is: continuous casting+strand insulation soaking+hot continuous rolling+cooling+batch.The key distinction of this technique and traditional technology is: the slab thickness of sheet bar process is attenuate greatly, for 50-90mm, because strand is thin, strand needs only through 1 ~ 2 passage roughing (when slab thickness is 70-90mm) or does not need through roughing (when slab thickness is 50mm), and the continuously cast bloom of traditional technology will be through multi-pass rolling repeatedly, just can be thinned to required specification before finish rolling; And the strand of sheet bar process is without cooling, directly enters soaking pit and carries out soaking insulation, or a small amount of mend temperature, so sheet bar process shortened technical process greatly, reduced energy consumption, reduced investment, thereby reduced production cost.But CSP improves because cooling rate faster can cause steel strength, yield tensile ratio improves, thereby increase rolling load, the thickness specification that makes to produce economically hot-rolled product also can not be too thin, Yi Ban Wei≤1.5mm, see Chinese patent CN200610123458.1, CN200610035800.2 and CN200710031548.2, and these patents all do not relate to element B and Sn.Solution CSP is organized thinner and inhomogeneous, and the higher problem of yield tensile ratio is suggested as a very important problem.
The technical process shorter than CSP is sheet-band continuous casting and rolling technique, strip continuous casting technology is a cutting edge technology in metallurgy and investigation of materials field, its Iron And Steel Industry that appears as is brought a revolution, it has changed traditional production process of controlling steel band in metal working industry, by continuous casting, rolling, even thermal treatment etc. integrates, make the online hot rolling of strip base process a time of producing with regard to the thin steel band of disposable formation, greatly simplified production process, shortened the production cycle, its processing line length is 50m left and right only; Facility investment is corresponding minimizing also, and product cost significantly reduces, and is a kind of hot rolled thin strip production technique of low-carbon environment-friendly.Twin-roll thin strip continuous casting technique is a kind of principal mode of thin band continuous casting technique, is also unique a kind of thin band continuous casting technique of realizing industrialization in the world.
The typical technical process of twin-roll thin strip continuous casting is: the molten steel in large bag is by large bag long nozzle, tundish and flow distribution device cast directly over one by two, relatively rotate and molten bath that crystallization roll that can be cooling fast and lateral seal surround in, molten steel solidifies and forms solidified shell growth gradually in the peripheral surface of crystallization roll rotation, and then form the thick Cast Strip of 1-5mm at the minimum places of two casting roll roll gap gaps (nip point), the strip that is rolled into 0.7-2.5mm in milling train is sent into via guide plate guiding pinch roll in Cast Strip, cooling through apparatus for supercooling subsequently, after shear arrangement crop, finally send into reeling machine and batch rolling.
Adopt thin strap continuous casting to produce cold formability high-strength steel, due to thinner thickness, for thickness be less than 1.5mm(containing) thin size hot-rolled product, thin band continuous casting technique has stronger manufacture and cost advantage.The consumption of the high-strength Thin Strip Steel of cold formability in worldwide is very large, more than light automobile just reaches 300wt by the high-strength Thin Strip Steel annual requirement of cold-forming, the hot-rolled sheet state directly product specification characteristic thickness of the supply of material is 1.0, 1.2, 1.25mm and 1.5mm, because product thickness is thinner, therefore adopt traditional hot continuous rolling process production cost higher, a lot of producers are due to the capabilities limits of traditional hot-rolling line, the producer of original available hot-rolled sheet supply of material transfers employing Cold Rolled Sheet Steel to or cold rolling hot dip galvanizing steel sheet replaces the supply of material, this has also increased the production cost of cold formability high-strength steel.
When hot rolled strip is used as thin size hot-rolled plate or " with hot Dai Leng " product, to strip surface quality, require very high.The thickness of general requirement belt steel surface oxide skin is got over Bao Yuehao, this just need to be follow-up in Cast Strip the generation of each stage control iron scale, in casting roll until inlet of rolling mill all adopts confined chamber to prevent Cast Strip oxidation, in confined chamber, as patent US6920912 adds hydrogen and control oxygen content in patent US20060182989, be less than 5%, all can control the scale thickness on surface, Cast Strip.But relate to batching the seldom relevant patent of thickness how this section of course of conveying to control oxide skin at milling train, especially adopting the cooling or spraying cooling of laminar flow to carrying out in cooling process with steel, the band steel of high temperature contacts with water coolant, and the scale thickness on surface, Cast Strip increases very fast.Meanwhile, the band steel of high temperature also contacts and can bring a lot of problems with water coolant:
One, can form water spots (rust staining) at belt steel surface, affect surface quality;
Two, the water coolant that laminar flow is cooling or spraying cooling is used easily causes belt steel surface Local cooling inhomogeneous, causes inhomogeneous with steel interior microscopic tissue, thereby causes the inhomogeneous of strip property, affects quality product;
Three, belt steel surface Local cooling is inhomogeneous, can cause the deterioration of plate shape, affects strip shape quality.
But thin strap continuous casting is due to the fast solidification technology characteristic of itself, the problem that steel grade ubiquity tissue odds is even, unit elongation is on the low side, yield tensile ratio is higher, formability is bad of production; Simultaneously Cast Strip austenite crystal has obvious ununiformity, and the finished product that can cause obtaining after austenite phase transformation are organized also inhomogeneous, thereby causes the unstable properties of product.Therefore adopt thin strap continuous casting production line to produce the product with good formability of some automobile industries, petrochemical industry needs, tool acquires a certain degree of difficulty.When thin size hot-rolled band steel is used as cold formability high-strength steel product, require steel grade in mechanical property, to there is preferably strong plasticity coupling, there is higher unit elongation, and in processing performance, there is good impact briquetting performance.In the face of high like this performance requriements, to adopting thin strap continuous casting to produce this steel grade, there is certain challenge, therefore, while adopting thin strap continuous casting to produce the high-strength Thin Strip Steel of cold formability, indiscriminately imitating traditional Composition And Process is to produce qualified cold formability high-strength steel, need in composition and technique, have breakthrough.
International monopoly WO 2008137898, WO 2008137899, WO 2008137900, and Chinese patent CN200880023157.9, CN200880023167.2, CN200880023586.6 disclose a kind of sheet-band continuous casting and rolling explained hereafter thickness that utilizes in the method for the micro-alloyed steel strip of 0.3-3mm.The chemical composition that the method adopts is C :≤0.25%, Mn:0.20 ~ 2.0%, Si:0.05 ~ 0.50%, Al :≤0.01%, in addition, also comprise Nb:0.01 ~ 0.20%, V:0.01 ~ 0.20%, in Mo:0.05 ~ 0.50% at least one.At hot rolling draft, be 20-40%, under ℃ processing condition of coiling temperature≤700, the microstructure of hot-rolled strip is bainite+acicular ferrite.Patent thinks, the alloying element mainly existing with solid melt in Cast Strip has suppressed austenitic recrystallize after hot rolling, even if draft reaches 40%, austenitic recrystallize is also very limited.Because the hot rolling draft of 20-40% does not all make austenite generation recrystallize, thick austenitic hardening capacity is kept after hot rolling, thereby obtain the room temperature texture of bainite+acicular ferrite.In patent, do not provide the temperature range that hot rolling adopts, but in the article relevant to these patents (C.R.Killmore, etc.Development of Ultra-Thin Cast Strip Products by the
process.AIS Tech, Indianapolis, Indiana, USA, May 7-10,2007), having reported the hot-rolled temperature adopting is 950 ℃.
The thin strap continuous casting low-carbon microalloy product made from steel that profit is produced in this way, intensity is higher, and within the scope of above composition system, yield strength can reach 650MPa, tensile strength can reach 750MPa, but that topmost problem is the unit elongation of product is not high (≤6% or≤10%).Cause the not high major cause of unit elongation to be: the Cast Strip obtaining by thin band continuous casting technique, austenite grain size is inhomogeneous, little of tens microns, greatly to seven or eight hundred microns.And it is general only with 1-2 machine frame rolling mill after thin band continuous casting technique, its hot rolling draft is difficult to surpass 50% conventionally, effect by deformation crystal grain thinning is very little, if not by recrystallization softening austenite crystal, inhomogeneous austenite structure is difficult to effectively be improved after hot rolling, also very inhomogeneous by the bainite+acicular ferrite structure producing after the inhomogeneous austenite phase transformation of size, so unit elongation is not high.
In order to improve the strong plasticity coupling of thin strap continuous casting micro-alloyed steel, patent 02825466.X has proposed another and has utilized sheet-band continuous casting and rolling explained hereafter thickness in the method for the micro-alloyed steel strip of 1-6mm.The micro-alloyed steel composition system that the method adopts is C:0.02 ~ 0.20%, Mn:0.1 ~ 1.6%, Si:0.02 ~ 2.0%, Al :≤0.05%, S :≤0.03%, P :≤0.1%, Cr:0.01 ~ 1.5%, Ni:0.01 ~ 0.5%, Mo :≤0.5%, N:0.003 ~ 0.012%, surplus is Fe and inevitable impurity.The hot rolling of Cast Strip is at 1150-(Ar1-100) ℃ within the scope of, hot rolling is carried out in corresponding austenitic area, austenite ferrite two-phase region or ferrite area, hot rolling draft is 15-80%.The method is after sheet-band continuous casting and rolling unit, designed on-line heating system, Heating temperature scope is 670-1150 ℃, and object is to make Cast Strip after different phase region hot rollings, after insulation for some time, there is perfect recrystallization, thereby make steel band obtain preferably strong plasticity coupling.Profit is produced in this way, need to when producing line design, increase online heating system, and due to the length of heat-up time, depends on belt speed and process furnace length, and process furnace must have sufficient length, guarantee heating uniformity.This has not only increased cost of investment, also can significantly increase the floor space that sheet-band continuous casting and rolling produces line, has reduced the advantage of this product line.
Summary of the invention
The object of the present invention is to provide the high-strength Thin Strip Steel of a kind of cold formability and manufacture method thereof, can solve the problem that in thin band continuous casting technique process, tissue odds is even, unit elongation is on the low side, yield tensile ratio is higher, formability is bad, meet the service requirementss such as bending and molding, impact briquetting, thereby meet the service requirements of cold rolling base and " with hot Dai Leng " product.
For achieving the above object, technical scheme of the present invention is:
The present invention, by adding microalloy element and the B elements such as Nb, V, Ti, Mo containing in the soft steel of Sn, goes out after crystallization roll at thin strip continuous casting strip steel, to band steel both sides, adopts high pressure to spray dry ice (solid-state CO
2) mode that band steel is carried out to Quick uniform is cooling, the effect that improves cooling uniformity and speed of cooling and reach anti-oxidation, even austenite crystal tissue, reduction rolling temperature; Adopt the online recrystallize rolling of austenite simultaneously, realize the online recrystallize of austenite after the hot rolling of Cast Strip; Then adopt anti-oxidation method for rapid cooling can reduce belt steel surface scale thickness, improve belt steel temperature homogeneity, improve strip surface quality.
Particularly, the high-strength Thin Strip Steel of a kind of cold formability, its chemical component weight per-cent is: C:0.04 ~ 0.12%, Si:0.2 ~ 0.5%, Mn:0.4 ~ 1.7%, P≤0.055%, S≤0.008%, N:0.004 ~ 0.010%, Al:0.015 ~ 0.06%, Sn:0.005 ~ 0.04%, B:0.001 ~ 0.006%, and in Nb, V, Ti, Mo more than one, maximum three kinds, Nb:0.01 ~ 0.08%, V:0.01 ~ 0.08%, Ti:0.01 ~ 0.08%, Mo:0.1 ~ 0.4%, all the other are Fe and inevitable impurity.
In chemical composition design of the present invention:
C:C is strengthening element most economical, the most basic in steel, improves the intensity of steel by solution strengthening and precipitation strength.C separates out the requisite element of cementite in austenitic transformation process, so the height of C content determines the intensity rank of steel to a great extent, i.e. the higher higher intensity rank of C content correspondence.But due to the gap solid solution of C with separate out the plasticity of steel and toughness are had to larger harm, and too high C content is unfavorable to welding property, so C content can not be too high, the intensity of steel makes up by suitable interpolation alloying element.Therefore the C content range that the present invention adopts is 0.04-0.12%.
Si:Si plays solution strengthening effect in steel, and in steel, adds Si and can improve purity of steel and deoxidation, but Si too high levels can cause weldability and welding heat influence area toughness to worsen.Therefore the Si content range that the present invention adopts is 0.2-0.5%.
Mn:Mn is one of alloying element that price is the most cheap, it can improve the hardening capacity of steel, in steel, there is sizable solid solubility, by solution strengthening, improve the intensity of steel, simultaneously substantially harmless to the plasticity of steel and toughness, be the topmost strengthening element of intensity that improves steel in C content situation reducing.But Mn too high levels can cause weldability and welding heat influence area toughness to worsen.Therefore the Mn content range that the present invention adopts is 0.4-1.7%.
P:P can significantly improve the corrosion resistance nature of steel, and can improve intensity.But the P of high-content, easily at grain boundary segregation, increases the cold shortness of steel, and welding property is degenerated, and reduces plasticity, and cold-bending property is degenerated.In thin band continuous casting technique, solidifying with rate of cooling of Cast Strip is exceedingly fast, and can effectively suppress the segregation of P, thereby can effectively avoid the inferior position of P, give full play to the advantage of P, such as the high-strength Thin Strip Steel of automobile cold formability is objectively also requiring steel grade to have certain erosion resistance.Therefore in the present invention, adopt P content higher while producing cold formability high-strength steel compared with traditional technology, suitably relax the content of P element, in steel making working procedure, cancel dephosphorization operation, in actually operating, do not need deliberately to carry out dephosphorization operation, do not need additionally to add phosphorus, scope≤0.055% of P content yet.
S: S is harmful element in steel under normal conditions, makes steel produce red brittleness, reduces ductility and the toughness of steel, causes crackle when rolling.S also can reduce welding property and erosion resistance.Therefore in the present invention, S also controls as impurity element, its content range is≤and 0.008%.
Al:Al is the element adding for deoxidation in steel, and the Al that adds 0.015-0.06% content is conducive to improve the toughness and tenacity of steel.
N: similar with C element, N element can improve by gap solid solution the intensity of steel, the present invention will utilize N in steel with the precipitated phase of B effect generation BN, and needing has certain N content in steel.But the gap solid solution of N has larger harm to the plasticity of steel and toughness, the existence of free N can improve the yield tensile ratio of steel, so N content can not be too high.The N content range that the present invention adopts is 0.004-0.010%.
Nb: in conventional Nb, V, Ti, tetra-kinds of microalloy elements of Mo, Nb is the alloying element of austenite recrystallization after the strongest inhibition hot rolling.In the micro-alloyed steel of using in traditional controlled rolling, generally all add Nb, the one, play the effect of strengthening, the 2nd, suppress austenite generation recrystallize after hot rolling, realize the object of deformation refine austenite crystal grain.Nb can pass through solute atoms drag mechanism, and the niobium carbonitrides Second Phase Particles pinning mechanism of separating out and effectively stop the migration of big angle crystal boundary and subgrain boundary, thereby stop significantly recrystallization process, it is more remarkable that wherein Second Phase Particles stops the effect of recrystallize.
In thin band continuous casting technique, due to its unique steel band rapid solidification and quick cooling characteristic, can make the alloy element Nb adding mainly with solid solution state, be present in steel band, even if steel band cool to room temperature does not almost observe separating out of Nb yet.Therefore, although Nb element can suppress austenite recrystallization effectively, but in thin band continuous casting technique, only depend on solute atoms and do not bring into play Second Phase Particles be used for stoping recrystallize, very difficult under many circumstances, for example, the in the situation that, deformation quantity higher at deformation temperature being larger, even if add Nb element, also can there is recrystallize in austenite.On the other hand, the Nb element of solid solution in steel, can pull austenite grain boundary by solute atoms, suppresses to a certain extent Austenite Grain Growth, thus refine austenite crystal grain, and from this point, Nb is for promoting after austenite hot rolling that recrystallize is favourable.
The present invention should bring into play the intensity of the solution strengthening effect raising steel of Nb, reduces again the restraining effect of Nb to recrystallize as far as possible, and designing its content range is 0.01-0.08%.
V: in conventional Nb, V, Ti, tetra-kinds of microalloy elements of Mo, V is the most weak to the restraining effect of austenite recrystallization.In recrystallize controlled rolling steel, normally add V, both can play strengthening effect, simultaneously smaller again comparatively speaking to the restraining effect of recrystallize, realize the object of recrystallization softening austenite crystal.
In thin band continuous casting technique, V is also mainly present in steel band with solid solution state, even if steel band cool to room temperature does not almost observe separating out of V yet.Therefore, V element is very limited to the restraining effect of austenite recrystallization.The intensity that improves steel at the solution strengthening effect that should bring into play alloying element, reduces alloying element again in the inhibiting situation of recrystallize, and V is more satisfactory alloying element, design the most according to the invention.On the other hand, the V element of solid solution in steel, can pull austenite grain boundary by solute atoms, suppresses to a certain extent Austenite Grain Growth, thus refine austenite crystal grain, and from this point, V is for promoting after austenite hot rolling that recrystallize is favourable.
It is 0.01-0.08% that the present invention adopts the content range of V.
Ti: in conventional Nb, V, Ti, tetra-kinds of microalloy elements of Mo, Ti to the restraining effect of austenite recrystallization inferior to Nb, but higher than Mo, V.From this point, Ti is to promoting that austenite recrystallization is disadvantageous.But Ti has an outstanding advantage, and its solid solubility is very low, the size that it can at high temperature form quite stable is about the Second Phase Particles TiN about 10nm, and AUSTENITE GRAIN COARSENING in the time of can stoping soaking plays the effect that promotes recrystallize thus.Therefore, in recrystallize controlled rolling steel, conventionally add trace Ti, refine austenite crystal grain, promotes austenite recrystallization.
In thin band continuous casting technique, Ti is mainly present in hot steel band with solid solution state, if steel band cool to room temperature may be observed separating out of a little Ti.Therefore, Ti element is limited to the restraining effect of austenite recrystallization.On the other hand, the Ti element of solid solution in steel, can pull austenite grain boundary by solute atoms, suppresses to a certain extent Austenite Grain Growth, thereby refine austenite crystal grain, from this point, is favourable for recrystallize after the hot rolling of promotion austenite.
The present invention should bring into play the intensity of the strengthening effect raising steel of Ti, reduces again the restraining effect of Ti to recrystallize as far as possible, and designing its content range is 0.01-0.08%.
Mo: in conventional Nb, V, Ti, tetra-kinds of microalloy elements of Mo, Mo is also weak to the restraining effect of austenite recrystallization comparatively speaking, only higher than V.
In thin band continuous casting technique, Mo is also mainly present in steel band with solid solution state, even if steel band cool to room temperature does not almost observe separating out of Mo yet.Therefore, Mo element is very limited to the restraining effect of austenite recrystallization.On the other hand, the Mo element of solid solution in steel, can pull austenite grain boundary by solute atoms, suppresses to a certain extent Austenite Grain Growth, thus refine austenite crystal grain, from this point, for promoting that austenite recrystallization is favourable.
It is 0.1-0.4% that the present invention adopts the content range of Mo.
Sn:Sn element is acknowledged as the harmful element in steel, because Sn is easy segregation element, a small amount of Sn will be in crystal boundary enrichment, and causing is that defects i.e.cracks occurs, and therefore in traditional technique, the content of Sn element is strictly controlled.Thin strap continuous casting is due to rapid solidification, and element reduces greatly in interdendritic segregation, can greatly improve the solid solution capacity of element, and therefore, under thin band continuous casting technique condition, the scope of Sn element can expand, and therefore can greatly reduce steel-making cost.Fig. 3 is the relation of Sn element and mean heat flux.As seen from Figure 3, when Sn add-on is less than 0.04%, little on the impact of heat flow density, on the not impact of thin strip solidification process.Fig. 4 is the relation of Sn content and surfaceness.Because the crackle on surface, Cast Strip is all the fold place generation at Cast Strip surface irregularity conventionally, a situation arises by surfaceness, to carry out characterization of surfaces crackle.If roughness is large, the probability that crackle occurs is high.As shown in Figure 4, the increase of Sn content does not exert an adverse impact to the surface quality of Cast Strip under rapid solidification condition.From the result of Fig. 3 and Fig. 4, Sn does not produce detrimentally affect to solidifying with surface quality of Cast Strip.The content range of Sn is at 0.005-0.04%.
The remarkable effect of B:B in steel is: the boron of denier just can make the hardening capacity of steel be multiplied, thereby B can preferentially separate out thick BN particle in high temperature austenite suppresses separating out of tiny AlN, weaken the pinning effect of tiny AlN to crystal boundary, improve the energy for growth of crystal grain, thus alligatoring austenite crystal; The B of some solid solution simultaneously segregation has suppressed ferrite forming core at austenite grain boundary, has reduced ferritic nucleation rate, thereby reaches the effect that reduces yield tensile ratio, improves processability; B can effectively prevent crystal boundary low melting point phase B with the combination of N in addition
2o
3appearance.
B is active easily segregation element, and easily at Grain Boundary Segregation, when traditional technology is produced containing B steel, B content general control very strict, generally in 0.001-0.003% left and right; And in thin band continuous casting technique, solidify with rate of cooling comparatively fast, and can effectively suppress the segregation of B, the more B content of solid solution, so the content of B can suitably relax; Can also generate thick BN particle by rational technology controlling and process, suppress tiny AlN and separate out, play the effect of fixed nitrogen,, the inferior position that formability bad higher with steel yield tensile ratio that solve that thin strap continuous casting produces.Therefore in the present invention, adopt the B content higher compared with traditional technology, scope is 0.001-0.006%.
The manufacture method of the high-strength Thin Strip Steel of a kind of cold formability of the present invention, comprises the steps:
A) smelt
By following compositions, smelt, chemical component weight per-cent is: C:0.04 ~ 0.12%, Si:0.2 ~ 0.5%, Mn:0.4 ~ 1.7%, P≤0.055%, S≤0.008%, N:0.004 ~ 0.010%, Al:0.015 ~ 0.06%, Sn:0.005 ~ 0.04%, B:0.001 ~ 0.006%, and in Nb, V, Ti, Mo more than one, maximum three kinds, Nb:0.01 ~ 0.08%, V:0.01 ~ 0.08%, Ti:0.01 ~ 0.08%, Mo:0.1 ~ 0.4%, all the other are Fe and inevitable impurity;
B) casting
Adopt twin-roll thin strip continuous casting, casting roll diameter 500 ~ 1500mm, the casting rate 60 ~ 150m/min of casting machine;
C) secondary is cooling
Thin-belt continuous casting is taken out of after crystallization roll, and Cast Strip temperature, at 1420 ~ 1480 ℃, arranges two device for cooling in the both sides of Cast Strip along Cast Strip width, and after going out to be with, adopting immediately to both sides, Cast Strip high pressure to spray dry ice is solid-state CO
2the mode of particle is evenly cooled to below 1280 ℃ rapidly to Cast Strip, 200 ~ 300 ℃/s of Cast Strip rate of cooling;
D) online hot rolling
The band steel that is rolled into 0.7 ~ 2.5mm thickness in milling train is delivered in the cooled Cast Strip of secondary, wherein, 1050 ~ 1200 ℃ of rolling temperatures, hot rolling draft is 20 ~ 50%, after hot rolling with the thickness 0.7 ~ 2.5mm of steel;
E) band steel rolls rear cooling
Band steel after online hot rolling is rolled rear cooling, the anti-oxidation fast cooling mode of cooling employing is solid-state CO by dry ice
2inject directly on steel strip surface, to accelerate the cooling of steel band, wherein dry ice mixes with rare gas element or compressed nitrogen, and dry ice is 5:1 ~ 10:1 with the mixed volume ratio of gas, pressure with 0.2 ~ 3MPa is directly injected in steel strip surface by dry ice particles, 80 ~ 200 ℃/s of rate of cooling;
F) strip coiling
Cooled hot rolled strip is after crop shears excise second-rate head, directly batch rolling, 500 ~ 600 ℃ of coiling temperatures, more than the performance of the final high-strength Thin Strip Steel of cold formability reaches yield strength 500MPa, more than tensile strength reaches 650MPa, unit elongation reaches more than 18%, and yield tensile ratio is lower than 0.8.
Further, beginning to cool down of two device for cooling is a little arranged on from nip point 250-750mm, whole two cold but segment length 200 ~ 500mm.
Again, dry ice mixes with rare gas element or nitrogen, and the mixed volume of dry ice and gas is than being 5:1 ~ 10:1, with the pressure of 0.5 ~ 5MPa directly by dry ice blasting in steel strip surface.
In addition, rolling temperature is 1050 ~ 1150 ℃.Hot rolling draft scope is 30 ~ 50%.After hot rolling, belt steel thickness is 1.2 ~ 2.0mm.
In manufacture method of the present invention,
1, secondary is cooling
To band steel both sides, adopt and spray dry ice (solid-state CO
2) mode band steel is evenly cooled to below 1280 ℃ rapidly, can significantly improve cooling uniformity and speed of cooling with steel, promote separating out of BN in steel.
Above-mentioned dry ice mixes with rare gas element or nitrogen directly dry ice blasting in steel strip surface, played on the one hand the effect that reduces temperature of steel strips, solid-state dry ice is sprayed onto hot belt steel surface and can gasifies on the other hand, at belt steel surface, forms highdensity vaporific gas, carbonic acid gas (CO
2) belong to a kind of inert atmosphere, can be coated on belt steel surface, play with the anti-oxidation effect of steel, thereby effectively controlled the growth of belt steel surface oxide skin.
In the confined chamber at the cooling place of above-mentioned secondary, need not lead in addition protection of inert gas band steel, directly utilize high pressure to spray the CO that dry ice evaporates
2gas is realized the protection against oxidation with steel.Gas collector is set on confined chamber, to be used for collecting too much high-density CO 2 gas.
In steel, boron and nitrogen, aluminium and the nitrogen thermodynamical equilibrium equation in γ-Fe is as follows:
BN=B+N；Log[B][N]＝-13970/T+5.24(1)
AlN=Al+N；Log[Al][N]＝-6770/T+1.03(2)
As shown in Figure 2, in steel, the beginning Precipitation Temperature of BN is 1280 ℃ of left and right, and in the time of 980 ℃, separating out of BN tended to balance, and now separating out just of AlN just starts (Precipitation Temperature of AlN is 980 ℃ of left and right), and from thermodynamics, separating out of BN will have precedence over AlN.Therefore the present invention, by rational technology controlling and process means, promotes the combination of B and N, generates thick BN particle, thereby even austenite crystal tissue suppresses tiny AlN and separates out.
Conventionally, under thin strap continuous casting, in confined chamber, do not adopt any cooling provision, in long-term casting situation, the envrionment temperature of confined chamber is up to more than 800 ℃, the load-bearing under long-term high temperature of the confined chamber underframe of steel construction and confined chamber wall is on active service, can deform, affect intensity and the precision of whole mechanical framework structure, the danger such as cracking at underframe welding junction place also easily occur.Therefore a lot of work has been done aspect confined chamber cooling by a lot of producers, such as the light factory thin strap continuous casting of Nippon Steel adopts the form of water wall to reach cooling object with regard to having reported time confined chamber wall, concrete scheme is that lower confined chamber wall adopts two block plate welding, middle logical recirculated water; The Castrip of U.S. Nucor (seeing patent US5960856A) adopts the form of " water-cooled pillow " to reach cooling object, concrete scheme is from steel, the place close to slightly arranges water-cooled pillow, the logical recirculated water in the inside, form (confined chamber) just as in large room arranges a hot room of septulum (water-cooled pillow surrounds), with steel, pass the hot room of septulum that water-cooled pillow surrounds, temperature is absorbed, and when being with steel cooling, plays the temperature drop effect to big room (confined chamber).
The present invention sprays dry ice at confined chamber inner high voltage, adopts " distillation " physical property of dry ice self, can absorb a large amount of heats, to when being with steel realization cooling rapidly, the temperature of confined chamber is also played to the effect of effective temperature-reducing; Effective reduction of confined chamber temperature, plays cooling effect to the underframe of whole confined chamber (being generally steel construction) and confined chamber wall, can effectively prevent the distortion of confined chamber underframe.
2, online hot rolling
The cooled band steel that is rolled into 0.7-2.5mm thickness in milling train of delivering to steel of secondary, rolling temperature is 1050 ~ 1200 ℃, object is austenite generation perfect recrystallization after assurance hot rolling.Controlling hot rolling draft is 20 ~ 50%, and hot rolling draught increases can promote austenite recrystallization.
We find by test, and in the temperature range of 1050-1200 ℃, hot rolling draft is greater than 20%, just can there is relatively easily dynamic recrystallization in austenite, can further reach homogenizing tissue, improve the object of unit elongation, this point also will be as an important inventive point of the present invention.
By secondary cooling apparatus, realize 1050 ~ 1200 ℃ of relatively low rolling temperatures, relatively low rolling temperature, for rolling, be favourable, rolling temperature is lower, is more conducive to the control of rolling strip shape quality, in conventional strip technological process, temperature before milling train is often up to more than 1200 ℃, and even more than 1250 ℃, band steel is now very soft, cannot apply larger rolling load, be difficult to effective rolling.Guaranteeing under the prerequisite of the online recrystallize of austenite, preferably, 1050 ~ 1150 ℃ of rolling temperatures.
3, band steel rolls rear cooling
Band steel after online hot rolling is rolled rear cooling, the anti-oxidation fast cooling mode of cooling employing, anti-oxidation quickly cooling device is by dry ice (solid-state CO
2) inject directly on steel strip surface, to accelerate the cooling of steel band, wherein dry ice mixes with rare gas element or compressed nitrogen, with the pressure of 0.2 ~ 3MPa directly by dry ice blasting in steel strip surface, played on the one hand the effect that reduces temperature of steel strips, on the other hand CO
2belong to a kind of inert atmosphere, its proportion is larger than oxygen, can be coated on belt steel surface, plays with the anti-oxidation effect of steel, thereby has effectively controlled the growth of Surfaces of Hot Rolled Strip oxide skin.This kind of problem that the type of cooling can avoid traditional laminar flow cooling zone, evenly declines belt steel surface temperature, improves belt steel temperature homogeneity, thereby reaches the effect of homogenizing interior microscopic tissue; Simultaneously cooling even, can improve the strip shape quality with steel; Reduce the scale thickness of belt steel surface, the follow-up pickling while being convenient to make cold rolling base.Anti-oxidation cooling rate of cooling scope is fast 80-200 ℃/s.
The present invention adopts high-speed gas to wrap dry ice particles (CO
2) to spray belt steel surface cooling for broken phosphorus and strengthening, because dry ice touches after hot band steel can absorb heat fast, can become CO
2gas, affects surface quality of strips and composition so can not embed belt steel surface; In addition, due to the quick heat-absorbing action of dry ice, can play quick cooling effect to band; The more important thing is, after dry ice volatilization, become atmospheric carbon dioxide (CO
2), completely cut off and oxygen (O
2) contact, restriction strip surface oxide skin further generate.
4, strip coiling
Cooled hot rolled strip, after crop shears excise second-rate head, directly batches rolling.The coiling temperature of controlling hot-rolled strip is 500 ~ 600 ℃, so that hot-rolled strip has the tissue signature of bainite.Reeling machine adopts two forms of batching, and guarantees the continuous production with steel.
Through above-mentioned manufacturing processed, more than the performance of the final high-strength Thin Strip Steel of cold formability reaches yield strength 500MPa, more than tensile strength reaches 650MPa, unit elongation reaches more than 18%, and yield tensile ratio is lower than 0.8.
The present invention is compared with the prior art:
The patent of existing thin strap continuous casting production thin strip product and technique has a lot, but adopts thin strap continuous casting to produce containing the high-strength Thin Strip Steel of B cold formability, yet there are no directly open report.
As mentioned a kind of method and device of casting black metal strip in patent EP0830223A1/CN1180325A/US5960856A/DE69700737D, at band steel, solidify after two rollers, arrange a pair ofly for the cooling contactless heat absorber of steel, be used for the latent heat of solidification that discharges after absorption band steel solidifies completely.This patent is compared with the present invention, the key distinction is in speed of cooling, the present invention adopts high pressure to spray the method for dry ice, directly contacting with the strip, it is cooling to force, can realize 200 ℃/more than s speed of cooling, higher than the cooling performance of contactless heat absorber, effectively reduce rolling temperature far away, be conducive to the raising of rolling strip shape quality.
Chinese patent CN1472019A discloses a kind of method for continuous casting sheet band and device, in crystallization roll exit, to high temperature Cast Strip broad ways blowing gas, Cast Strip is realized cooling.Although this patent can play cooling effect to Cast Strip, but adopt the mode of air cooling, the span of control of rate of cooling has certain limitation, the present invention adopts high pressure to spray the method for dry ice, directly contacting with the strip, it is cooling to force, can realize 200 ℃/more than s speed of cooling, effectively reduce rolling temperature, be conducive to the raising of rolling strip shape quality.
The driven roll that day JP-A-5-277654 of the present invention has increased a pair of external diameter Φ 200mm at crystallization roll outlet lower end 300-400mm, by the transmission of heat by contact of driven roll and Cast Strip, reaches the cooling effect with steel.The present invention is completely different from the means that the method adopts, and the present invention is by spray the method for dry ice to directly carry out high pressure with steel, band tape transport heat of steel.The main drawback of day JP-A-5-277654 of the present invention is that speed of cooling is limited, is secondly the speeds match problem of crystallization roll and pony roll, if mate badly, easily give a discount in Cast Strip, and production operation inconvenience, controls dumb.
In sum, the cold formability high-strength steel in order to utilize thin band continuous casting technique to produce with preferably strong plasticity coupling, the present invention is adding microalloy element and the B elements such as Nb, V, Ti, Mo containing in the soft steel of Sn, by rational two cold patterns, at thin strip continuous casting strip steel, go out after crystallization roll, to band steel both sides, adopt high pressure to spray dry ice (solid-state CO
2) mode band steel is carried out evenly cooling rapidly, the effect that improves cooling uniformity and speed of cooling and reach anti-oxidation, even austenite crystal tissue, reduction rolling temperature; Band steel after rolling adopts anti-oxidation Cooling Mode can reduce belt steel surface scale thickness, improves belt steel temperature homogeneity, improves strip surface quality.Thin strap continuous casting, when producing this type of steel grade, can solve the problem that in thin band continuous casting technique process, tissue odds is even, unit elongation is on the low side, yield tensile ratio is higher, formability is bad, thereby meet the service requirementss such as bending and molding, impact briquetting.
Utilize strip continuous casting technology to produce boracic (B) cold formability high-strength steel, there is not yet up to now report, conclude advantage as follows:
(1) saved heating of plate blank, the multi-pass complex process such as hot rolling repeatedly, to directly carrying out the online hot rolling of a time in thin Cast Strip, production cost significantly reduces.
(2) Cast Strip thickness itself is thinner, and by being hot-rolled down to online expected product thickness, the production of thin slab product does not need through cold rolling, directly " with hot Dai Leng "; On the other hand, due to thinner thickness, during for cold rolling base, can greatly reduce the passage of follow-up cold rolling attenuate, greatly save production cost.
(3) utilize the steel scrap containing Sn, the Sn in steel is accomplished to " turning harm into good ", realize the effective utilization to existing steel scrap or low-quality ore resources inferior (high tin ore), promote the recycle of steel, reduce production costs, realize iron and steel industry Sustainable development.
(4) add the microalloy elements such as Nb, V, Ti, Mo, can significantly improve the intensity of steel plate; Add B element, can solve the problem that in thin band continuous casting technique process, tissue odds is even, yield tensile ratio is higher, thereby meet the service requirements of cold rolling base; Be easy to bending, impact briquetting simultaneously.
(5) in traditional technology slab process of cooling, there is alloying element and separate out, when slab reheats, tend to reduce because alloying element back dissolving is insufficient alloying element utilization ratio.In thin band continuous casting technique, the direct hot rolling in high temperature Cast Strip, the alloying element adding mainly exists with solid solution state, can improve alloy utilization ratio.
Major advantage of the present invention:
1. adopt thin band continuous casting technique to produce the high-strength Thin Strip Steel of cold formability, after carrying out hot rolling, direct supply market is used, reach the object of the thin size hot-rolled plate supply of material and meet that cold rolling base requires and " cold with the torrid zone " object, can significantly improve the cost performance of Strip.
2. the present invention adopts and adds micro-boron, reaches effective reduction band steel yield tensile ratio, improves the effect with steel processability, and production cost is more traditional and thin slab production technique is obviously cheap.The further volume of comprehensive utilization improving harmful residual element P in steel, cancels the dephosphorization operation in steel-making simultaneously, makes production cost more traditional obviously cheap with thin slab production technique.
3. utilize the steel scrap containing Sn, the Sn in steel is accomplished to " turning harm into good ", realize the effective utilization to existing steel scrap or low-quality ore resources inferior (high tin ore), promote the recycle of steel, reduce production costs, realize iron and steel industry Sustainable development.
4. adopt secondary cooling apparatus to realize relatively low rolling temperature, be conducive to online hot rolling, be conducive to the control of rolling strip shape quality; In addition utilize the physics heat-absorbing action of dry ice " distillation ", play effective reduction confined chamber temperature and prevent the effect that confined chamber steel structure frame is out of shape.The rear anti-oxidation cooling iron scale thickness that effectively reduces Surfaces of Hot Rolled Strip is fast rolled in employing, can greatly improve plate surface quality.
5. reasonable process parameter control has flexibly been widened the state space of production line, can meet the need of production of variant production specification.
6. the present invention is applicable to the metal casting steel band with double-roll type strip caster cast thickness 1.5-3mm, the high-strength Thin Strip Steel of especially a kind of automobile cold formability.
Accompanying drawing explanation
Fig. 1 is that production technique of the present invention is arranged schematic diagram.
Fig. 2 is BN, the thermomechanical curve schematic diagram that AlN separates out.
Fig. 3 is the schematic diagram that is related to of Sn content and mean heat flux.
Fig. 4 is the schematic diagram that is related to of Sn content and Cast Strip surfaceness.
Embodiment
Referring to Fig. 1, it is depicted as technological process of the present invention, molten steel casts directly over by large bag long nozzle 2, tundish 3 and flow distribution device 4 in the molten bath 7 that crystallization roll 5a, a 5b who relatively rotates by two and can be cooling fast and side seal board device 6a, 6b surround through large bag 1, molten steel solidifies in the peripheral surface of crystallization roll 5a, 5b rotation, and then forms solidified shell and grow and at the minimum places of two crystallization roll roll gap gaps (nip point), form the thick Cast Strip 11 of 1.5-3mm subsequently gradually.Cast Strip is through two device for cooling 8 in confined chamber 10, and after going out to be with, to Cast Strip, 11 both sides high pressure spray dry ice particles (solid-state CO immediately
2), control its rate of cooling, Cast Strip 11 Quick uniforms are cooled to below 1280 ℃.Then by swing guide 9, pinch roll 12, hot rolls 13 is delivered to in Cast Strip, after hot rolling, forms the hot rolled strip of 0.7-2.5mm, then after rolling anti-oxidation quickly cooling device 14, by dry ice (solid-state CO
2) inject directly on belt steel surface, cooling with accelerated band steel, controls rate of cooling, after rollgang 15 is delivered to shear arrangement 16 crops, crop is fallen in flying shear hole 18 along flying shear guide plate 17, and the hot-rolled strip after crop enters reeling machine 19,19 ' and batches.Coil of strip, after reeling machine takes off, is naturally cooled to room temperature.
In the confined chamber 10 at the cooling place of above-mentioned secondary, need not lead in addition protection of inert gas band steel, directly utilize high pressure to spray the CO that dry ice evaporates
2gas is realized the protection against oxidation with steel.Gas collector 20 is set on confined chamber 10, to be used for collecting too much high-density CO 2 gas.
The cooled Cast Strip 11 of secondary, goes out confined chamber 10 and by pinch roll 12, Cast Strip 11 is delivered to the thin strip that is rolled into 0.7-2.5mm thickness in milling train 13.Wherein, controlled rolling temperature is 1050-1200 ℃ (can control by two cooling rate rates), and object is austenite generation perfect recrystallization after assurance hot rolling.Controlling hot rolling draft is 20-50%, and hot rolling draught increases can promote austenite recrystallization, and preferably, hot rolling draft scope is 30-50%.Thickness range with steel after hot rolling is 0.7-2.5mm, and preferably, thickness is 1.2-2.0mm.
Embodiment of the present invention chemical composition is as shown in table 1.Performance after processing parameter and hot-rolled strip cool to room temperature is in Table 2.Comparative example 1 is not added B element in thin band continuous casting technique composition; Comparative example 2 is the high-strength Thin Strip Steel of cold formability that traditional hot rolling technology is produced, and does not add B element in composition.
In sum, the present invention utilizes thin band continuous casting technique technology, the high-strength Thin Strip Steel of cold formability of manufacture, and more than yield strength reaches 500MPa, more than tensile strength reaches 650MPa, unit elongation reaches more than 18%, and yield tensile ratio is lower than 0.8, and cold working buckling performance is qualified.The present invention can effectively solve the problem that the ubiquitous tissue odds of steel grade is even, yield tensile ratio is higher, formability is bad that thin strap continuous casting is produced, and meets the stamping forming service requirements of cold formability high-strength steel.
The chemical composition (wt.%) of table 1 embodiment steel
| C | Si | Mn | P | S | N | Al | Nb | V | Ti | Mo | Sn | B | Fe | |
| Embodiment 1 | 0.10 | 0.26 | 0.85 | 0.05 | 0.004 | 0.0074 | 0.06 | 0.08 | 0.15 | 0.02 | 0.003 | All the other | ||
| Embodiment 2 | 0.078 | 0.20 | 0.90 | 0.035 | 0.003 | 0.0061 | 0.055 | 0.02 | 0.04 | 0.01 | 0.005 | 0.001 | All the other | |
| Embodiment 3 | 0.090 | 0.34 | 0.78 | 0.015 | 0.004 | 0.0058 | 0.04 | 0.05 | 0.03 | 0.004 | All the other | |||
| Embodiment 4 | 0.085 | 0.26 | 1.00 | 0.021 | 0.006 | 0.0087 | 0.015 | 0.08 | 0.07 | 0.04 | 0.006 | All the other | ||
| Embodiment 5 | 0.044 | 0.34 | 0.65 | 0.009 | 0.005 | 0.0052 | 0.03 | 0.05 | 0.01 | 0.003 | All the other | |||
| Embodiment 6 | 0.055 | 0.40 | 0.67 | 0.025 | 0.006 | 0.0046 | 0.025 | 0.01 | 0.40 | 0.025 | 0.005 | All the other | ||
| Embodiment 7 | 0.040 | 0.28 | 0.85 | 0.055 | 0.008 | 0.0040 | 0.05 | 0.08 | 0.035 | 0.003 | All the other | |||
| Embodiment 8 | 0.048 | 0.37 | 1.00 | 0.014 | 0.005 | 0.0100 | 0.045 | 0.35 | 0.015 | 0.002 | All the other | |||
| Embodiment 9 | 0.066 | 0.36 | 0.84 | 0.018 | 0.005 | 0.0078 | 0.03 | 0.04 | 0.05 | 0.027 | 0.004 | All the other | ||
| Embodiment 10 | 0.12 | 0.33 | 0.60 | 0.022 | 0.004 | 0.0055 | 0.04 | 0.05 | 0.25 | 0.016 | 0.006 | All the other | ||
| Embodiment 11 | 0.11 | 0.50 | 1.65 | 0.050 | 0.006 | 0.0090 | 0.025 | 0.04 | 0.06 | 0.008 | 0.003 | All the other | ||
| Embodiment 12 | 0.075 | 0.36 | 1.70 | 0.042 | 0.007 | 0.0085 | 0.035 | 0.07 | 0.06 | 0.10 | 0.012 | 0.002 | All the other | |
| Embodiment 13 | 0.066 | 0.45 | 1.37 | 0.038 | 0.004 | 0.0045 | 0.045 | 0.05 | 0.04 | 0.32 | 0.032 | 0.005 | All the other | |
| Embodiment 14 | 0.084 | 0.37 | 0.40 | 0.027 | 0.003 | 0.0064 | 0.04 | 0.02 | 0.07 | 0.20 | 0.027 | 0.004 | All the other | |
| Comparative example 1 | 0.085 | 0.35 | 0.85 | 0.022 | 0.005 | 0.0080 | 0.03 | 0.05 | 0.06 | All the other | ||||
| Comparative example 2 | 0.11 | 0.24 | 0.50 | 0.015 | 0.007 | 0.0050 | 0.05 | 0.03 | 0.02 | 0.05 | All the other |
Processing parameter and the product performance of table 2 embodiment steel
Claims (5)
1. a manufacture method for the high-strength Thin Strip Steel of cold formability, comprises the steps:
A) smelt
By following compositions, smelt, chemical component weight per-cent is: C:0.04～0.12%, Si:0.2～0.5%, Mn:0.4～1.7%, P≤0.055%, S≤0.008%, N:0.004～0.010%, Al:0.015～0.06%, Sn:0.005～0.04%, B:0.001～0.006%, and in Nb, V, Ti, Mo more than one, maximum three kinds, Nb:0.01～0.08%, V:0.01～0.08%, Ti:0.01～0.08%, Mo:0.1～0.4%, all the other are Fe and inevitable impurity;
B) casting
Adopt twin-roll thin strip continuous casting, casting roll diameter 500～1500mm, the casting rate 60～150m/min of casting machine;
C) secondary is cooling
Thin-belt continuous casting is taken out of after crystallization roll, and Cast Strip temperature, at 1420～1480 ℃, arranges two device for cooling in the both sides of Cast Strip along Cast Strip width, and beginning to cool down of two device for cooling is a little arranged on from nip point 250-750mm, whole two cold but segment length 200～500mm; After going out to be with, adopting sprinkling dry ice immediately to both sides, Cast Strip is solid-state CO
2mode Cast Strip is evenly cooled to below 1280 ℃ rapidly, 200～300 ℃/s of Cast Strip rate of cooling;
D) online hot rolling
The band steel that is rolled into 0.7～2.5mm thickness in milling train is delivered in the cooled Cast Strip of secondary, wherein, 1050～1200 ℃ of rolling temperatures, hot rolling draft is 20～50%, after hot rolling with the thickness 0.7～2.5mm of steel;
E) band steel rolls rear cooling
Band steel after online hot rolling is rolled rear cooling, the anti-oxidation fast cooling mode of cooling employing is solid-state CO by dry ice
2inject directly on belt steel surface, cooling with accelerated band steel, wherein dry ice mixes with rare gas element or compressed nitrogen, dry ice with the mixed volume of gas than being 5:1～10:1, with the pressure of 0.2～3MPa directly by dry ice blasting at belt steel surface, 80～200 ℃/s of rate of cooling;
F) strip coiling
Cooled hot rolled strip is after crop shears excise second-rate head, directly batch rolling, 500～600 ℃ of coiling temperatures, more than the performance of the final high-strength Thin Strip Steel of cold formability reaches yield strength 500MPa, more than tensile strength reaches 650MPa, unit elongation reaches more than 18%, and yield tensile ratio is lower than 0.8.
2. the manufacture method of the high-strength Thin Strip Steel of cold formability as claimed in claim 1, it is characterized in that, in step c) secondary cooling process, dry ice mixes with rare gas element or nitrogen, the mixed volume of dry ice and gas is than being 5:1～10:1, with the pressure of 0.5～5MPa directly by dry ice blasting at belt steel surface.
3. the manufacture method of the high-strength Thin Strip Steel of cold formability as claimed in claim 1, is characterized in that, 1050～1150 ℃ of the rolling temperatures of online hot rolling.
4. the manufacture method of the high-strength Thin Strip Steel of cold formability as claimed in claim 1, is characterized in that, the hot rolling draft 30～50% of online hot rolling.
5. the manufacture method of the high-strength Thin Strip Steel of cold formability as claimed in claim 1, is characterized in that, after hot rolling, belt steel thickness is 1.2～2.0mm.
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| CN112296285B (en) * | 2020-09-18 | 2022-04-05 | 江苏沙钢集团有限公司 | Method for improving wrinkles of double-roller cast-rolled thin strip |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1547620A (en) * | 2001-08-24 | 2004-11-17 | �ձ�������ʽ���� | Steel plate exhibiting excellent workability and method for producing the same |
| CN102301027A (en) * | 2009-02-02 | 2011-12-28 | 杰富意钢铁株式会社 | High-strength hot-dip galvanized steel sheet and manufacturing method therefor |
-
2012
- 2012-08-31 CN CN201210319504.0A patent/CN102796956B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1547620A (en) * | 2001-08-24 | 2004-11-17 | �ձ�������ʽ���� | Steel plate exhibiting excellent workability and method for producing the same |
| CN102301027A (en) * | 2009-02-02 | 2011-12-28 | 杰富意钢铁株式会社 | High-strength hot-dip galvanized steel sheet and manufacturing method therefor |
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