CN1970811B - High-strength cold-roll-forming structural steel and method for producing same - Google Patents
High-strength cold-roll-forming structural steel and method for producing same Download PDFInfo
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Abstract
The invention discloses a high-strength cool-bent moulding structural steel and manufacturing method, which comprises the following parts: 0.03-0.12% C,0.08-0.50% Si,1.20-1.95% Mn,not more than 0.02% P,not more than 0.006% S, 0.05%-0.15% Mo,0.005-0.055% Als,0.03-0.07% Nb,0.08-0.15% Ti,0.01-0.05% V ,0.0008-0.004% Ca and Fe and inevitable impurity with Ceq not more than 0.42%. The making method is characterized by the following: controlling the fusing point of smolten steel over 15-30 deg.c; casting continuously; setting drawing speed of casting bland at 1.5-4.0m/min and blank thickness between 100 and 200mm; heating in the furnace directly; setting the even heating temperature at 1100-1250 deg.c, fine-rolling temperature at 940-1070 deg.c and outlet temperature at 840-920 deg.c; freezing rapidly after 0-7s; setting the coiling temperature at 500-610 deg.c with yielding strength of steel board over 700Mpa and drawing-proof strength between 750 and 950Mpa and extending rate over 17%.
Description
Technical field
The present invention relates to the high strength steel plate for welding that be suitable for cold roll forming of a kind of yield strength more than 700MPa, and the method for this high strength cold roll forming structural steel of producing with conventional strand and medium thin slab continuous casting and rolling production line.
Background technology
In the past, the micro-alloying hot rolled strip with hot-rolled strip production line is produced by controlled rolling and controlled chilling will reach the high strength of yield strength more than 700MPa, often needed the alloy element of high level.The alloying element content height can bring carbon equivalent to raise, and welding property degenerates.When reducing alloying element content, reach high requirement of strength, just must reduce rolling temperature and coiling temperature, to the Capability Requirement height of equipment.And the unit elongation of steel also sharply descends, and does not have high clod wash, impact briquetting performance.
Adopt to add Ti, can obtain high intensity by the precipitation of separating out of Ti, but the head of steel band, the tail temperature difference cause the ununiformity of performance, intensity index is widely different.
With the heavy slab casting machine continuous casting (slab thickness 〉=200mm, pulling rate is lower than 1.3m/min) of routine, alloying element is easy to segregation, causes the composition profiles inequality.After strand was produced, even adopt hot charging, because the discontinuity of production process, when arriving the process furnace of rolling line, the temperature of strand also had been reduced to below 800 ℃.Therefore the precipitate of Ti, Nb etc. can be separated out with big graininess, in heat-processed thereafter, when heat-up time, weak point and temperature were low, because the precipitate of Ti, Nb etc. can not moltenly fully again be got back in the steel, has reduced its precipitation strength effect after rolling.The micro alloying elements such as Ti, Nb that make adding play one's part to the full after rolling, cooling, then must improve Heating temperature, prolong heat-up time, therefore can make the energy consumption increase bigger.
If produce in the CSP mode, because the content of Ti is higher, be easy to produce and hold the stream accident, and can not guarantee favorable surface quality and enough compression ratios (thickness of general thin slab is that 50～90mm is thick), product is difficult for obtaining high obdurability coupling.
Summary of the invention
The invention provides the production method of the good cold-forming of the welding property of a kind of yield strength more than 700MPa with high tensile steel plate.
Technical scheme of the present invention is such, its chemical chemical ingredients is (weight percent) C:0.03～0.12%, Si:0.08～0.50%, Mn:1.20～1.95%, P :≤0.02%, S :≤0.006%, Mo:0.05%～0.15%, Als:0.005～0.055%, Nb:0.03～0.07%, Ti:0.08～0.15%, V:0.01～0.05%, Ca:0.0008～0.004%, surplus is Fe and unavoidable impurities, carbon equivalent Ceq≤0.42%, Ceq=C+Mn/6+ (Mo+V)/4+ (Cr+Cu)/15+Si/24.
When needs increase the atmospheric corrosion resistance of steel, in the composition of above-mentioned steel, add Cu:0.15～0.45%; Or add Cu:0.15～0.45%, Ni:0.05～0.20% simultaneously.
The high strength cold roll forming structural steel that the present invention is directed to mentioned component adopts following production process route: molten steel desulfurizing → converter smelting → external refining → medium thin slab continuous casting → direct hot charging → continuous tunnel furnace heating → roughing → Coil Box → finish rolling → laminar flow cools off → batches, characteristics in each production technique are
A. ladle molten steel temperature 15～30 ℃ on fusing point in the middle of the continuous casting time control, high-speed continuous casting, its strand pulling rate 1.5～4.0m/min, the slab thickness specification limit is at 100mm～200mm, and width is at 900mm～2000mm.
B. strand direct hot charging, the roughing cogging is carried out behind insulation 30～90min in strand supplementary heating to 1100～1250 ℃, batches by Coil Box then.
C. finish rolling open rolling temperature in is 940～1070 ℃, 840～920 ℃ of finish rolling temperature outs, and 7s cools off fast with interior employing laminar flow behind the tandem rolling, 500～610 ℃ of coiling temperatures.
The microstructure of steel plate is ferrite+bainite+twin crystal martensite+residual austenite, and ferrite accounts for more than 60%, and mean diameter and has the carbide of the following diameter of a large amount of equally distributed 20nm to separate out precipitated phase below 4 μ m.The thickness range of steel plate is at 1.5mm～10mm, and width is at 900mm～2000mm.
Cast with the medium thin slab casting machine, the thickness of slab is at 100mm～200mm, pulling rate 1.5～4.0m/min, can realize rapid solidification, thereby reduced the time that oxidation takes place Ti in liquid phase, therefore reduced the gathering of oxide compound, Nization thing, taken precautions against the strand crackle that the Ti precipitated phase causes at the base shell.Since in thin strand be easy to realize rapid solidification, also reduced the ununiformity of Ti, Nb and all kinds of segregations that are mingled with that elements such as precipitated phase and P, S, N, C form thereof.
The medium thin slab that casts out is adopted direct hot charging, stopped the temperature section of slab experience below 800 ℃, Ti, Nb can not separate out in the stage before the slab heating, so do not need to consider to make the heat-up time of the abundant Hui Rong of precipitated phase of Ti, Nb.Make the reheat time decreased, when reducing the heating energy consumption significantly, stopped strand and too much caused crackle (when particularly containing Cu) because of heated oxide.
Adopt Coil Box, intermediate blank head when making finish rolling, in, the temperature basically identical of tail, it is inhomogeneous tissue and performance that excuse tail texturing temperature difference caused can not to occur, especially for steel of the present invention, owing to contain higher Nb, Ti, more responsive to rolling temperature, this puts extremely important.
Between 840～1070 ℃, carry out continuous rolling and rolling back cooling fast by the hot continuous rolling unit, can obtain notable effect of crystal grain thinning (grain size number is more than 12 grades), obtain yield strength more than the 700Mpa, tensile strength more than 750Mpa, unit elongation surpasses 17% the good cold-forming high tensile hot rolled steel sheet of welding property.
In the present invention, each element qualification reason is described in detail as follows:
C:C is main gap solution strengthening element as the element use of adjusting structural state, improving intensity.Simultaneously, when rolling postcooling, can become tiny carbide (NbTi) C with Nb, V-arrangement, play important precipitation strength and use with Ti to low temperature.But consumption is lower than at 0.03% o'clock, and the solution strengthening underswing is difficult to the yield strength of guaranteeing that 700MPa is above.Therefore lower limit is determined 0.03%.But C content is higher than at 0.12% o'clock, cools off the ferritic ratio in back fast and reduce after rolling, and the amplitude of build up is excessive, and unit elongation descends, and the clod wash processing characteristics degenerates.The C equivalent raises simultaneously, and welding property is bad.Therefore the upper limit is defined as 0.12%, and best scope is 0.06～0.09%.
Si:Si plays the solution strengthening effect, also is a kind of deoxidant element of cheapness.Make Si be lower than 0.08%, to the requirement height of smelting, process cost increases.But it is easy to make steel plate to produce the red rust defective, and the surface quality, particularly content that influence steel plate are higher than at 0.50% o'clock, can cause the iron sheet layer viscous that produces in the heating phase, is difficult for removing.Therefore determine that its scope is 0.08%～0.50%.
Mn: be the bioelement that improves steel strength.In the present invention, it is less than at 1.20% o'clock and is difficult to obtain the above high yield strength of 700MPa.Surpass 1.95% at addition, ratio of ferrite reduces too much, and the reinforcement amplitude is big, and unit elongation reduces many, the formability variation.Therefore determine that its scope is 1.20%～1.95%.
Ti: be precipitation strength element important among the present invention, below 630 ℃, precipitation is separated out and is TiC below the 20nm or (NbTi) C particle from steel, effective pinning dislocation, thus yield strength improved. it is less than 0.08%, separates out precipitation strength effect deficiency. be higher than the trouble that then caused on the continuous casting at 0.15% o'clock, be easy to cause the crack defect of strand, under quick refrigerative prerequisite, its precipitation strength effect also is tending towards saturated, is 0.08%～0.15%. so select its span of control simultaneously
Nb: be important micro alloying element, can improve the non-recrystallization district temperature of steel, ensure the effect of controlled rolling, make grain refining after the Steel Rolling, Nb and the compound precipitation particles of separating out of Ti have the precipitation strength effect simultaneously.Be lower than 0.03%, the effect deficiency.0.07% effect that is higher than reaches capacity.Therefore determine that its scope is 0.03%～0.07%.
V: separating out below 630 ℃, good strengthening effect is arranged, in the present invention, relying on it to play additional strengthening effect, simultaneously the same with Mo have the welded heat affecting zone of an inhibition ramollescence.Under the prerequisite of adding foregoing Nb, Ti, reach at 0.01% o'clock at its content, just obviously improved intensity, during superelevation 0.05%, effect in the present invention reaches capacity, and adds too much, cause unnecessary cost to increase, therefore limiting its scope is 0.01%～0.05%.
Mo: the effect that play and adjust the bainite ratio, improves intensity.Simultaneously can suppress the welded heat affecting zone ramollescence.Reaching at 0.05% o'clock, acting on obvious.Increase but surpass 0.15% cost, and the carbon equivalent increase, it is unfavorable that welding is become again.Therefore determine that its scope is 0.05%～0.15%.
Cu: among the present invention, propose, add Cu as the element that improves atmospheric corrosion resistance for the occasion that needs atmospheric corrosion resistance.Cu content reaches effect in 0.15% o'clock clearly, and is saturated effect in 0.45% o'clock.Therefore be limited to 0.45% on, be limited to 0.15% down.
Ni: be as preventing that the element that Cu splits defective from adding, the Ni element can also improve the low-temperature flexibility of steel simultaneously.After adding Cu, during bad adjustments of the atmosphere of process furnace, the Ni of interpolation more than 0.05% can effectively prevent the thermal fragmentation defect that the Cu element causes.Content surpasses 0.20%, and effect reaches capacity, and cost increases too much.Therefore its span of control is 0.05%～0.20%.
P: in the present invention, as harmful element,, cause processability bad P, can cause the welding joint bending property bad simultaneously because it is easy to cause segregation.It is 0.02% when following, influence not obvious, so will be defined as 0.02% on it.
S: be harmful element, the MnS ribbon that itself and Mn form is mingled with cold roll forming performance and impelling strength is had a significant impact.And it is easy to form big TiS precipitation particles, reduces the precipitation strength effect of Ti.It is 0.006% when following, and is not obvious to the influence of intensity and cold-bending property.Be limited to 0.006% on therefore definite its span of control.Be preferably below 0.004%.
Ca: make the nodularization of Sization thing, can further ensure the lateral extensibility of steel plate, improve the cold roll forming performance.As the means of nodularization Sization thing, carry out Ca later in refining and handle, Ca content reaches 0.0008% can play nodularization Sization thing, the effect of pure molten steel quality.Excessive Ca can make thickization of Sization thing, and the anti-ductility that causes reduces.Therefore rule of thumb, stipulate that it under aforementioned Sization thing contents level, is limited to 0.008% on it.
Adopt the reasons are as follows of medium thin slab continuous casting and direct hot charging:
The invention provides a kind of yield strength more than 700MPa and contain the manufacture method of the steel plate of Nb, Ti, Cu etc., this plate property is even, and has good cold roll forming performance.
Because the present invention utilizes the Ti of higher content to improve the intensity of steel plate.And Ti is easy to form the Nization thing in molten steel.The segregation meeting of these Nization things causes steel plate lamination defect to occur, on float to casting billet surface and then can cause strand lobe defective.Medium thin slab can be realized rapid solidification, reduces the incidence of above-mentioned two kinds of situations.So select to use the medium thin slab continuous casting.
The medium thin slab casting machine links to each other with rolling line simultaneously, can realize direct hot charging, strand does not need to be cooled to below 800 ℃ like this, there is not Ti, the C of Nb, the Nization thing is precipitation process in strand before rolling. therefore do not need the long-time again reheat of slab, the Ti also overwhelming majority is solid-solubilized in the preceding steel of finish rolling, thereby the precipitated phase disperse that guarantees the Ti etc. when roll the back is cooled to low temperature to it is tiny, just can give full play to the precipitation strength effect of separating out of Ti. otherwise, must be to the long-time heat of slab, it is bigger to remove the strand scaling loss like this, outside the power consumption, steel plate is easy to occur the limit and splits defective.
Adopt the reason of Coil Box:
Steel among the present invention will utilize the controlled rolling crystal grain thinning owing to contain higher Ti and Nb.The temperature difference of controlled rolling, the structural state of steel plate will have very big-difference.Generally speaking, do not use Coil Box, owing to rolling order reason, the temperature contrast of intermediate blank head, tail can reach 100 ℃, causes finished product yield strength difference maximum end to end to reach 150MPa.Performance inconsistency is very big.Adopt the Coil Box technology, the temperature fluctuation of intermediate blank will be lower than 30 ℃.Reduced finished product poor performance end to end significantly.
Slab heating temperature and soaking time:
Strand is in tunnel heating, owing to adopt direct hot charging, in the abundant solid solution that has been enough to ensure Nb, Ti more than 1100 ℃, thereby gives full play to the precipitation strength effect of Nb, Ti.Temperature surpasses 1250 ℃, and the strand scaling loss increases.Therefore determine that Heating temperature is 1100 ℃～1250 ℃.And the strand of the continuous tunnel furnace of directly packing into still keeps the medial temperature more than 900 ℃, behind 30～90min heating samming, and can be normally rolling.Therefore determine that soaking temperature is 30～90min.
Final rolling temperature:
In order to make the crystal grain miniaturization, the finish rolling start rolling temperature is answered below 1070 ℃, and best start rolling temperature is lower than 940 ℃ at 1010 ℃～940 ℃, and then the deflection at two-phase region increases, and the ductility of finished product reduces, and the load of milling train increases simultaneously, is unfavorable for producing.Finishing temperature is being necessary more than 840 ℃, is lower than 840 ℃, and the stress induced number of particles of separating out earlier increases, and is unfavorable for precipitation strength.If surpass 920 ℃, easy thickization of crystal grain, the effect of controlled rolling is bad.So finish rolling finishing temperature scope is determined at 840 ℃～920 ℃.
Cooling opportunity and speed of cooling: through cooling again behind the 7s, the effect of controlled rolling will be given a discount after rolling, and grain refining effect is insufficient.Therefore rolling back should not be higher than 7s to cooling off the time opening.Speed of cooling is lower than 20 ℃/s, and the Cization thing of Ti can be separated out in process of cooling, and population thick in the finished product increases, and the precipitation strength effect after batching is with deficiency.Therefore rolling postcooling speed should be higher than 20 ℃/s.Cool off discontinuously, also occur thickization of precipitation particles easily, and crystal grain may thickization, cause the product intensity deficiency, so the present invention recommends cooling to carry out continuously.
Coiling temperature: coiling temperature is lower than 650 ℃, and the crystal grain of formation is not being grown up substantially.But still the particle that the precipitation that is easy to occur large-size is separated out.Be lower than 630 ℃, the particle that precipitation is separated out can play good strengthening effect, but does not have bainite, martensitic stucture strengthening effect, intensity index deficiency.When coiling temperature is lower than 610 ℃, can obtain the favorable tissue strengthening effect.But cross low coiling temperature (being lower than 500 ℃), the bainite in the finished product, martensitic ratio are increased, intensity increases too much and the ductility reduction, and the cold roll forming degradation is difficult to batch simultaneously.Therefore determine that coiling temperature is 500 ℃～610 ℃.
Advantage of the present invention and effect are:
1. produce continuously cast bloom with the medium thin slab casting machine.Setting rate is fast, effectively prevented the segregation of Ti etc., and has taken precautions against separate out the infringement to the quality of strand of Ti at base shell solidificating period.Simultaneously, solidifying of higher speed makes the continuously cast bloom composition even, and the segregation degree is little.
2. employing direct hot charging, the strand thermosteresis is few, for the short period of time reheat provides assurance, so the reheat energy consumption is low.The temperature of strand is not reduced to below 800 ℃, so Ti, Nb etc. can not separate out before reheat in a large number, has ensured its precipitation strength effect after rolling.Heat-up time is short, and oxidation is few, and the probability that thermal crack takes place strand (when particularly containing Cu) reduces significantly.
3. employing Coil Box, intermediate blank longitudinal temperature difference when making the finish rolling distortion reduces to very little, the performance difference of logical volume is little. in addition, be easy to realize the accurate control of rolling temperature, laminar flow speed of cooling, coiling temperature, thereby realize the accurate control of performance level. realize good over-all properties coupling such as high strength, high tenacity, good welds performance.
4. be mingled with form more tiny, disperse, the composition profiles even matter that more becomes, structure refinement is even, has improved over-all properties, and has guaranteed good cold roll forming performance.
5. controlled rolling on the basis of Nb microalloying is rolled the back and is adopted cooling fast, and speed of cooling 〉=20 ℃ have ensured the effect of refined crystalline strengthening.Quick cooling has suppressed the alternate of Ti separates out, and has suppressed excessively growing up of precipitated phase.Adopt 500～610 ℃ the batching of temperature, C, the N compound precipitation that makes Nb, Ti etc. with strengthening effect separate out but its most of yardstick all below 30nm, also brought into play certain build up effect when having given full play to the precipitation strength effect.
7. compare with sheet blank continuous casting, the selection of production efficiency height, strand intermediate gauge section has ensured rolling big compression ratio, has effectively eliminated the subsurface defect that casting brings, so the product stable mechanical property.
Embodiment
Chemical chemical ingredients of the present invention is (weight percent) C:0.03～0.12%, Si:0.08～0.50%, Mn:1.20～1.95%, P :≤0.02%, S :≤0.006%, Mo:0.05%～0.15%, Als:0.005～0.055%, Nb:0.03～0.07%, Ti:0.08～0.15%, V:0.01～0.05%, Ca:0.0008～0.004%, surplus is Fe and unavoidable impurities, carbon equivalent Ceq≤0.42%, Ceq=C+Mn/6+ (Mo+V)/4+ (Cr+Cu)/15+Si/24.
When needs increase the atmospheric corrosion resistance of steel, in the composition of above-mentioned steel, add Cu:0.15～0.45%; Or add Cu:0.15～0.45%, Ni:0.05～0.20% simultaneously.
The high strength cold roll forming structural steel that the present invention is directed to mentioned component adopts following production process route: molten steel desulfurizing → converter smelting → external refining → medium thin slab continuous casting → direct hot charging → continuous tunnel furnace heating → roughing → Coil Box → finish rolling → laminar flow cools off → batches, characteristics in each production technique are
A. ladle molten steel temperature 15～30 ℃ on fusing point in the middle of the continuous casting time control, high-speed continuous casting, its strand pulling rate 1.5～4.0m/min, the slab thickness specification limit is at 100mm～200mm, and width is at 900mm～2000mm.
B. strand direct hot charging, the roughing cogging is carried out behind insulation 30～90min in strand supplementary heating to 1100～1250 ℃, batches by Coil Box then.
C. finish rolling open rolling temperature in is 940～1070 ℃, 840～920 ℃ of finish rolling temperature outs, and 7s cools off fast with interior employing laminar flow behind the tandem rolling, 500～610 ℃ of coiling temperatures.
By the steel plate that aforesaid method is produced, be ferrite+bainite+twin crystal martensite+residual austenite in microstructure, ferrite accounts for more than 60%, and mean diameter and has the carbide of the following diameter of a large amount of equally distributed 20nm to separate out precipitated phase below 4 μ m.The thickness range of steel plate is at 1.5mm～10mm, and width is at 900mm～2000mm.
Be several optimum examples of the present invention and product test result below.
1. Composition Control example
Annotate: Ceq=C+Mn/6+ (Mo+V)/4+ (Cu+Ni)/15+Si/24
2. rolling technology
The molten steel of mentioned component is controlled its temperature high-speed continuous casting 20～50 ℃ time the on fusing point, its strand pulling rate 1.5～4.0m/min, the slab thickness specification limit is at 100mm～200mm, width is at 900mm～2000mm, directly advance process furnace, 1180～1260 ℃ of strand soaking temperatures, 1020 ± 30 ℃ of finish rolling start rolling temperatures, 840～910 ℃ of finishing temperature scopes, the input laminar flow is cooled fast to and batches warm area in rolling back 2～5s, 50 ℃/s of cooling rate～140 ℃/s, 500～610 ℃ of coiling temperatures, 570 ± 30 ℃ of controls of best coiling temperature.
3. finished product mechanical property level
Claims (4)
1. high strength cold roll forming Structural Steel Plate, it is characterized in that, its chemical ingredients is C:0.03%～0.12% by weight percentage, Si:0.08%～0.50%, Mn:1.20%～1.95%, P :≤0.02%, S :≤0.006%, Mo:0.05%～0.15%, Als:0.005%～0.055%, Nb:0.03%～0.07%, Ti:0.12%～0.15%, V:0.01%～0.05%, Ca:0.0008%～0.004%, surplus is Fe and unavoidable impurities, carbon equivalent Ceq≤0.42%, Ceq=C+Mn/6+ (Mo+V)/4+ (Cr+Cu)/15+Si/24.
2. a kind of high strength cold roll forming Structural Steel Plate according to claim 1 is characterized in that, adds Cu:0.15%～0.45% in the composition of steel.
3. a kind of high strength cold roll forming Structural Steel Plate according to claim 1 is characterized in that, adds Cu:0.15%～0.45% in the composition of steel, Ni:0.05%～0.20%.
4. by the production method of each high strength cold roll forming Structural Steel Plate among the claim 1-3, its production process route is:
Desulfurizing iron-converter smelting-external refining-medium thin slab continuous casting-direct hot charging-continuous tunnel furnace heating-roughing-Coil Box-finish rolling controlled rolling-cool off fast-batch is characterized in that,
A. ladle molten steel temperature 15～30 ℃ on fusing point in the middle of the continuous casting time control, high-speed continuous casting, its strand pulling rate 1.5～4.0m/min, the slab thickness specification limit is at 100mm～200mm, and width is at 900mm～2000mm;
B. direct hot charging, strand is heated to 1100～1250 ℃, carries out the roughing cogging be incubated 30～90min in stove after, batches by Coil Box then, reduces the head and tail temperature difference in the intermediate blank operation of rolling;
C. finish rolling open rolling temperature in is 940～1070 ℃, 840～920 ℃ of finish rolling temperature outs, and steel plate adopts fast cooling behind the tandem rolling behind 0～7s, and cooling rate 〉=20 ℃/s are up to 200 ℃/s, 500～610 ℃ of coiling temperatures;
D. the microstructure of steel plate is ferrite+bainite+twin crystal martensite+residual austenite, ferrite accounts for more than 60%, mean diameter is below 4 μ m, and there is the carbide of the following diameter of a large amount of equally distributed 20nm to separate out precipitated phase, the thickness range of steel plate is at 1.5mm～10mm, and width is at 900mm～2000mm.
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| CN1151913A (en) * | 1996-08-29 | 1997-06-18 | 攀枝花钢铁（集团）公司钢铁研究院 | Prodn of steel plate for automobile girder |
| CN1418978A (en) * | 2001-11-14 | 2003-05-21 | 住友金属工业株式会社 | Anti-fatigue crack fine expansivity steel material and method for making same |
| CN1563467A (en) * | 2004-03-17 | 2005-01-12 | 广州珠江钢铁有限责任公司 | Manufacturing technique of hot rolled high tensile steel plate in use for cars based on compact type process flow of producing band steel |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102041447A (en) * | 2010-12-21 | 2011-05-04 | 南阳汉冶特钢有限公司 | Q345C steel plate and production method thereof |
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| CN1970811A (en) | 2007-05-30 |
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