CN101684533A - High strength cold-rolled plate with excellent formability and production method thereof - Google Patents
High strength cold-rolled plate with excellent formability and production method thereof Download PDFInfo
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- CN101684533A CN101684533A CN200810013481A CN200810013481A CN101684533A CN 101684533 A CN101684533 A CN 101684533A CN 200810013481 A CN200810013481 A CN 200810013481A CN 200810013481 A CN200810013481 A CN 200810013481A CN 101684533 A CN101684533 A CN 101684533A
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Abstract
The invention provides a high strength cold-rolled plate with excellent formability, containing: no more than 0.0040% of C, 0.02-0.15% of Si, 0.20-1.00% of Mn, 0.02-0.09% of P, 0.015-0.06% Ti, 0.01-0.05% of Nb, and the rest being Fe. The production method comprises: smelting, continuous casting, hot-rolling, cold rolling and continuous annealing, wherein the heating temperature of the hot-rolled billet is 1170-1270 DEG C, the finishing temperature of hot-rolling is 850-960 DEG C, and the coiling temperature is 650-760 DEG C; the cold rolling reduction percent is 60-82%; the annealing temperature is 760-880 DEG C, the thermal insulation time is 60-210s, the slow-cooling segment temperature is 630-700 DEG C, and the fast-cooling exit temperature is 300-500 DEG C; and the levelling elongationrate is 0.5-1.0%. The high strength steel plate containing phosphorus of the invention has the features of low carbon, microalloying and purity. The steel added with a certain amount of Nb and Ti hashigher plasticity. Using relevant rolling and annealing technique, the indexes of performance of the steel achieves the demand of high strength automobile stamping parts.
Description
Technical field
The invention belongs to the steel products technical field, relate in particular to a kind of high strength cold-rolled plate that has excellent moldability and production method thereof.
Background technology
Automobile factory generally adopts mild steel such as St13 and St14 to do the stamping parts of automobile both at home and abroad, and this class steel is easy to distortion at the punching course light plate, but because intensity is low, the ability of its anti-collision and depression is low, and safety performance is bad, so be unfavorable for protecting driver and crew.
Adopt High Strength Steel Plate not only can solve this type of problem, simultaneously, because the increase of the intensity of steel, the thickness of steel plate also can reduce, thereby alleviates the weight of automobile, in energy-intensive today, just can effectively reduce oil product consumption, improve resource utilization, also help automobile factory and capture the selling market.
At present, the technology that adopts phosphorus to produce high-strength steel as main strengthening element all has report both at home and abroad, though resemble process, implementation has tangible difference.
High Mn content is adopted in the design that has, and its shortcoming is that the anisotropy of steel is big.For example, application number is 99118334.7, the Chinese patent of " high strength phosphorated steel and manufacture method thereof " by name, the design that this patent adopts is high-carbon, phosphorates, and does not add alloying element, by the segregation of phosphorus at the crystal boundary place, reach the purpose of grain refining, realize the raising of the intensity of steel, the product plasticity index that adopts this mode to produce is bad, when causing deep processing, the plasticity of steel is bad.Be 200510051717.X also as application number, the Chinese patent of " high strength cold rolled steel plate and manufacture method thereof " by name, that this patent adopts is high Mn, high Als, Als content is 0.1%～1.0%, need add a large amount of ferro-aluminums during smelting, and cost is increased.
Summary of the invention
The objective of the invention is to overcome above-mentioned existing in prior technology defective, provide a kind of and can satisfy the automotive industry needs, have the high strength cold-rolled plate and the production method thereof of excellent formability.
The present invention is achieved in that the chemical component weight per-cent of the high strength cold-rolled plate that this has excellent formability: C≤0.0040%, Si:0.02%～0.15%, Mn:0.20%～1.00%, P:0.02%～0.09%, S≤0.025%, AL
S≤ 0.06%, Ti:0.015%～0.06%, Nb:0.01%～0.05%, N≤0.005%, surplus is Fe and unavoidable impurities.
The chemical component weight per-cent of high strength cold-rolled plate of the present invention preferably can be: C≤0.0040%, Si:0.02%～0.10%, Mn:0.20%～0.55%, P:0.02%～0.05%, Ti:0.015%～0.045%, Nb:0.01%～0.04%, surplus are Fe and unavoidable impurities; Also can be: C≤0.0040%, Si:0.02%～0.10%, Mn:0.30%～0.70%, P:0.05%～0.07%, Ti:0.03%～0.06%, Nb:0.01%～0.04%, surplus be Fe and unavoidable impurities; Can also be: C≤0.0040%, Si:0.04%～0.15%, Mn:0.70%～1.00%, P:0.05%～0.09%, Ti:0.03%～0.06%, Nb:0.02%～0.05%, surplus be Fe and unavoidable impurities.Can also add B in the steel of the present invention, its content weight percent is 0.0003%～0.0015%.
Production method with high strength cold-rolled plate of excellent formability of the present invention comprises smelting, continuous casting, hot rolling, cold rolling, continuous annealing, finishing, be characterized in that described hot rolled billet heating temperature is 1170～1270 ℃, hot rolling finishing temperature is 850～960 ℃, and coiling temperature is 650～760 ℃; Cold rolling draft is 60%～82%; Annealing temperature is 760～880 ℃, soaking time 60～210s, 630～700 ℃ of slow cooling section temperature, 300～500 ℃ of fast cold section temperature outs; Smooth unit elongation 0.5%～1.0%.
The described cold rolling draft of high strength cold-rolled plate of the present invention is preferably 70%～75%; Described annealing temperature is preferably 800～820 ℃, and soaking time is preferably 120～180s.
Composition design reason of the present invention:
The phosphorous high tensile steel plate of the present invention has characteristics such as Ultra-low carbon, microalloying, steel be pure, have lower yield strength and advantages of higher tensile strength, simultaneously, certain Nb, Ti alloy in steel, have been added, C, N in the steel are existed in steel with the form of second phase, make steel have high plasticity.Added P, Mn, Si content in the steel intensity of steel is improved, but plasticity index can reduce, therefore, must formulate rational composition design.
Ti content adds and too much will exist with the solid solution form in steel, simultaneously, when high temperature Ti easily with steel in P react, generate the FePTi of chemical combination attitude, FePTi has reduced the solution strengthening effect of phosphorus, to the intensity reduction and the reduction of r value of steel, therefore, should control Ti content in the steel in right amount.Ti content is low, and the C in the steel, N atom can not be completely fixed, and be unfavorable to the plasticity of steel; Ti content height causes the waste of production cost.Ti content of the present invention is controlled at 0.015%～0.06%.
In order to reduce the anisotropy of Ti steel, need to add certain Nb in the steel, in the high-strength IF steel plate that Ti+Nb handles, the adding of excessive Nb will make the Nb nucleidic mass of solid solution in the steel increase, and be unfavorable for that recrystallize carries out, and make the recrystallization temperature and the time lengthening of steel.Nb content is low, and the C in the steel, N atom can not be completely fixed.The present invention is controlled at 0.01%～0.05% with Nb content.
Consider the temperature of separating out that temperature is lower than C, N in the steel and Ti, Nb reaction of separating out of FePTi in the steel, in the composition design, should be taken into account that in theory the interpolation of Ti, Nb should meet Ti=4*C+3.43*N+1.5S and Nb=7.76*C, on the maximum addition of Ti, after should guaranteeing the C reaction formation precipitated phase in Ti and the steel, remaining solid solution C can react with the Nb in the steel, exists with the precipitated phase form.
P: be a kind of harmful element, can increase the fragility of steel, but in soft steel, suitably increase phosphorus content, little to the forming property influence of steel, but can improve the intensity of steel greatly.Phosphorus content added low, and was little to the intensity effect of steel, and the fragility of too high then steel and segregation influence plasticity, and therefore, P content scope of design is 0.02%～0.09%.
Mn is the solution strengthening element in steel, can improve the intensity of steel, and simultaneously, Mn can separate out with compound second mutually the form with S, Ti in the steel, C, N, and the precipitated phase in the steel is increased, and improves the plasticity of steel.Mn content scope of design is: 0.20%～1.00%, adjust Mn content upper and lower limit in the steel according to the intensity rank of steel.
Si is the solution strengthening element in steel, improves the intensity of steel, but the Si too high levels will influence the plasticity of steel.Si content scope of design is: 0.02%～0.15%, adjust Si content upper and lower limit in the steel according to the intensity rank of steel.
Al: suppress the solid solution of nitrogen in ferrite, eliminate strain aging, improve cold plasticity.
B: in ultra low-carbon steel, the P element is easily in the segregation of crystal boundary place, add a small amount of B after because B is gathered in crystal boundary in the IF steel, the crystal boundary bonding force is strengthened, simultaneously, B has suppressed the segregation of P at the crystal boundary place, has overcome crystal boundary fragility.Compound interpolation B and Nb can make the obvious refinement of IF steel annealed structure crystal grain that contains Ti.The B element adds few, does not have above-mentioned effect, and it is excessive that the B element adds, and causes the steel plate sclerosis easily, influences plasticity.
The present invention has adopted and added molten admittedly strengthening element such as certain Nb, Ti alloy and P, Mn, Si in steel, make steel have low yield strength and high tensile strength and plasticity preferably, be fit to the use of car surface spare and inner structural members, simultaneously, even if also change the original sentence to other products when this product goes wrong aborning easily, can reduce loss.
Operational path of the present invention: hot metal pretreatment → converter → refining (RH) → continuous casting → hot continuous rolling → cold-rolling pickling unit → cold rolling → continuous annealing → finishing unit → packing.
Technological design reason of the present invention:
Hot rolling steel billet Heating temperature of the present invention is 1170～1270 ℃, hot rolling finishing temperature is 850～960 ℃, employing high temperature batches, coiling temperature is 650～760 ℃, and this is can form tiny and uniform ferrite and big and equally distributed two-phase particle in the above hot rolling of recrystallization temperature in order to ensure steel.
Cold-rolling process of the present invention when obtaining high R value, can obtain high unit elongation by rational draft.The increase of cold rolling draft increases recrystallize energy storage broken in the tissue after cold rolling, and in cold rolled annealed process, recrystallize forming core particle increases, and the recrystallize time opening in advance.At holding stage subsequently, the time of grain growth prolongs relatively, helps obtaining separating out, assembling of the big crystal grain and second phase, forms favorable texture, it is favourable to obtain good unit elongation and R value, if but the draft of cold rolling employing is excessive, can cause in the steel recrystallize forming core particle too much, and the motivating force of grain growth mainly come from the interfacial energy between the crystal boundary, interfacial energy circle difference increases, like this, cause the inner crystal grain of steel inhomogeneous easily, influence the unit elongation of steel.The present invention is controlled at 60%～82% with cold rolling draft, and best draft is 70%～75%, at this moment, can obtain high R value and high unit elongation.
The annealing holding stage also forms in this stage the vital fiber texture of deep drawability, and therefore, annealing process plays a decisive role to the deep drawability of high-strength IF steel.Along with the raising of annealing temperature, crystal grain increases.This has illustrated that annealing temperature is high more, and recrystallize and recrystal grain are grown up abundant more, and be favourable more to deep drawability, but the yield strength of steel and tensile strength will reduce, and unit elongation and R value, n value increase.Therefore, need to formulate the rational heat treatment temperature, can obtain unit elongation and R value, n value that high yield strength can obtain again is the heat treated key of production phosphor-containing steel.
Annealing temperature of the present invention is 760 ℃～880 ℃, and best annealing temperature is 800 ℃～820 ℃; Reasonably soaking time is 60～210s, and best soaking time is 120～180s, can obtain all extraordinary effects of composite target such as intensity and plasticity.Phosphor-containing steel can not be annealed again, because again after the annealing, will make separating out of FeTiP phase in the steel, and melt back takes place the compound two-phase particle that TiNbCN is bigger.Soaking time is too short, will make recrystallize insufficient, and the two-phase particle can not be assembled fully.Make crystal grain meticulous, influence the unit elongation of steel.Evenly the growing up of two-phase particle that increase to of soaking time provides the time with poly-partially, can occur the bigger compound two-phase particle of TiNbCN in the steel.But along with the continuation of soaking time increases, tiny two-phase particle in the steel presents poly-partially phenomenon, and is therefore bigger to the pinning effect of crystal boundary, hinders dislocation motion, unfavorable to the development of annealing texture, and the development of obstruction recrystallization texture influences the unit elongation of steel.
The present invention is controlled at 630～700 ℃ with the slow cooling section temperature, and fast cold section temperature out is controlled at 300～500 ℃, and smooth unit elongation is 0.5%～1.0%, the performance that this helps obtaining.
The phosphorous high tensile steel plate of the present invention has characteristics such as Ultra-low carbon, microalloying, steel be pure, certain Nb, Ti alloy in steel, have been added, C, N in the steel are existed in steel with the form of second phase, make steel have high plasticity, and the common ultra low-carbon steel of the anisotropy ratio of steel is little.Adopt corresponding hot rolling, cold rolling and annealing process, the steel of producing has good plasticity and very high intensity, can satisfy the requirement of high-strength vehicle stamping parts performance index.Cost of the present invention increases little, but effect stability, remarkable in economical benefits.
Embodiment
The present invention is further described by the following embodiment.
Table 1 is the chemical ingredients of embodiment of the invention steel plate.
Table 2 is the rolling technological parameter of the embodiment of the invention.
Table 3 is the continuous annealing process parameter of the embodiment of the invention.
Table 4 is the detection performance of embodiment of the invention steel plate.
The chemical ingredients of table 1 embodiment of the invention steel plate (wt, %)
| Embodiment | ??C | ??Si | ??Mn | ??P | ??S | ??Als | ??Ti | ??N | ??Nb | ??B |
| ??1 | ??0.0021 | ??0.05 | ??0.52 | ??0.045 | ??0.010 | ??0.035 | ??0.043 | ??0.0024 | ??0.030 | ??- |
| ??2 | ??0.0025 | ??0.03 | ??0.54 | ??0.041 | ??0.011 | ??0.033 | ??0.025 | ??0.0034 | ??0.040 | ??- |
| ??3 | ??0.0019 | ??0.09 | ??0.31 | ??0.024 | ??0.009 | ??0.029 | ??0.042 | ??0.0034 | ??0.038 | ??- |
| ??4 | ??0.0017 | ??0.08 | ??0.33 | ??0.046 | ??0.007 | ??0.027 | ??0.045 | ??0.0018 | ??0.039 | ??- |
| ??5 | ??0.0027 | ??0.08 | ??0.60 | ??0.063 | ??0.007 | ??0.027 | ??0.047 | ??0.0018 | ??0.031 | ??- |
| ??6 | ??0.0017 | ??0.05 | ??0.58 | ??0.055 | ??0.012 | ??0.042 | ??0.041 | ??0.0028 | ??0.037 | ??- |
| ??7 | ??0.0028 | ??0.08 | ??0.63 | ??0.067 | ??0.012 | ??0.042 | ??0.045 | ??0.0022 | ??0.030 | ??- |
| ??8 | ??0.0015 | ??0.04 | ??0.68 | ??0.069 | ??0.012 | ??0.042 | ??0.055 | ??0.0029 | ??0.017 | ??- |
| ??9 | ??0.0023 | ??0.09 | ??0.92 | ??0.062 | ??0.018 | ??0.039 | ??0.042 | ??0.0035 | ??0.038 | ??- |
| ??10 | ??0.0021 | ??0.12 | ??0.88 | ??0.069 | ??0.013 | ??0.039 | ??0.049 | ??0.0017 | ??0.028 | ??- |
| ??11 | ??0.0018 | ??0.11 | ??0.76 | ??0.083 | ??0.008 | ??0.029 | ??0.053 | ??0.0017 | ??0.025 | ??- |
| ??12 | ??0.0024 | ??0.09 | ??0.25 | ??0.039 | ??0.011 | ??0.048 | ??0.044 | ??0.0032 | ??0.032 | ??0.0009 |
| ??13 | ??0.0018 | ??0.06 | ??0.51 | ??0.032 | ??0.010 | ??0.037 | ??0.055 | ??0.0025 | ??0.024 | ??0.0012 |
| ??14 | ??0.0016 | ??0.08 | ??0.92 | ??0.055 | ??0.009 | ??0.042 | ??0.033 | ??0.0025 | ??0.044 | ??0.0006 |
Table 2 embodiment of the invention rolling technological parameter
| Embodiment | Heating temperature (℃) | Hot rolling finishing temperature (℃) | The hot rolling reeling temperature (℃) | Cold rolling draft (%) |
| ??1 | ??1202 | ??901 | ??708 | ??68 |
| ??2 | ??1245 | ??889 | ??697 | ??81 |
| ??3 | ??1190 | ??924 | ??727 | ??66 |
| ??4 | ??1233 | ??920 | ??713 | ??73 |
| ??5 | ??1201 | ??904 | ??702 | ??72 |
| ??6 | ??1241 | ??897 | ??735 | ??73 |
| ??7 | ??1239 | ??902 | ??701 | ??70 |
| ??8 | ??1270 | ??929 | ??715 | ??69 |
| ??9 | ??1255 | ??915 | ??712 | ??64 |
| ??10 | ??1228 | ??917 | ??705 | ??69 |
| ??11 | ??1264 | ??933 | ??723 | ??69 |
| ??12 | ??1236 | ??905 | ??722 | ??73 |
| ??13 | ??1192 | ??897 | ??735 | ??72 |
| ??14 | ??1180 | ??899 | ??702 | ??68 |
Table 3 embodiment of the invention continuous annealing process parameter
| Embodiment | Annealing temperature (℃) | Soaking time (S) | The slow cooling section temperature out (℃) | Fast cold section temperature out (℃) | Smooth unit elongation (%) |
| ??1 | ??812 | ??88 | ??653 | ??402 | ??0.6 |
| ??2 | ??815 | ??194 | ??644 | ??387 | ??0.65 |
| ??3 | ??796 | ??121 | ??655 | ??409 | ??0.70 |
| ??4 | ??828 | ??76 | ??669 | ??428 | ??0.6 |
| ??5 | ??821 | ??132 | ??667 | ??416 | ??0.7 |
| ??6 | ??817 | ??115 | ??650 | ??397 | ??0.7 |
| ??7 | ??815 | ??144 | ??642 | ??399 | ??0.6 |
| ??8 | ??822 | ??124 | ??646 | ??392 | ??0.92 |
| ??9 | ??799 | ??133 | ??655 | ??422 | ??0.5 |
| ??10 | ??820 | ??160 | ??673 | ??404 | ??0.8 |
| ??11 | ??809 | ??95 | ??677 | ??427 | ??0.7 |
| ??12 | ??812 | ??149 | ??687 | ??403 | ??0.7 |
| ??13 | ??817 | ??105 | ??649 | ??396 | ??0.5 |
| ??14 | ??809 | ??172 | ??692 | ??422 | ??0.8 |
The performance of table 4 embodiment of the invention steel plate
| Embodiment | Yield strength MPa | Tensile strength MPa | Unit elongation % | ??r | ??n |
| ??1 | ??198 | ??354 | ??39 | ??2.02 | ??0.23 |
| ??2 | ??191 | ??347 | ??40 | ??2.12 | ??0.24 |
| ??3 | ??207 | ??367 | ??39 | ??2.09 | ??0.23 |
| ??4 | ??210 | ??356 | ??38 | ??1.95 | ??0.25 |
| ??5 | ??242 | ??390 | ??35 | ??1.79 | ??0.20 |
| ??6 | ??229 | ??374 | ??37 | ??1.86 | ??0.22 |
| ??7 | ??248 | ??392 | ??36 | ??1.83 | ??0.24 |
| ??8 | ??252 | ??387 | ??35 | ??1.79 | ??0.19 |
| ??9 | ??274 | ??423 | ??34 | ||
| ??10 | ??269 | ??437 | ??35 | ||
| ??11 | ??283 | ??441 | ??33 | ||
| ??12 | ??212 | ??362 | ??38 | ??2.09 | ??0.24 |
| ??13 | ??244 | ??397 | ??36 | ??2.02 | ??0.22 |
| ??14 | ??281 | ??429 | ??33 |
Claims (8)
1. high strength cold-rolled plate with excellent formability, the chemical component weight per-cent that it is characterized in that this steel is: C≤0.0040%, Si:0.02%～0.15%, Mn:0.20%～1.00%, P:0.02%～0.09%, S≤0.025%, ALs≤0.06%, Ti:0.015%～0.06%, Nb:0.01%～0.05%, N≤0.005%, surplus are Fe and unavoidable impurities.
2. high strength cold-rolled plate according to claim 1 is characterized in that the chemical component weight per-cent of this steel is: Si:0.02%～0.10%, Mn:0.20%～0.55%, P:0.02%～0.05%, Ti:0.015%～0.045%, Nb:0.01%～0.04%.
3. high strength cold-rolled plate according to claim 1 is characterized in that the chemical component weight per-cent of this steel is: Si:0.02%～0.10%, Mn:0.30%～0.70%, P:0.05%～0.07%, Ti:0.03%～0.06%, Nb:0.01%～0.04%.
4. high strength cold-rolled plate according to claim 1 is characterized in that the chemical component weight per-cent of this steel is: Si:0.04%～0.15%, Mn:0.70%～1.00%, P:0.05%～0.09%, Ti:0.03%～0.06%, Nb:0.02%～0.05%.
5. according to claim 1,2,3 or 4 described high strength cold-rolled plates, it is characterized in that also containing in the steel B, its weight percent is 0.0003%～0.0015%.
6. the production method of each described high strength cold-rolled plate in the claim 1～5, comprise smelting, continuous casting, hot rolling, cold rolling, continuous annealing, finishing, it is characterized in that described hot rolled billet heating temperature is 1170～1270 ℃, hot rolling finishing temperature is 850～960 ℃, and coiling temperature is 650～760 ℃; Cold rolling draft is 60%～82%; Annealing temperature is 760 ℃～880 ℃, soaking time 60～210s, 630～700 ℃ of slow cooling section temperature, 300～500 ℃ of fast cold section temperature outs; Smooth unit elongation 0.5%～1.0%.
7. the production method of high strength cold-rolled plate according to claim 6 is characterized in that described cold rolling draft is 70%～75%.
8. the production method of high strength cold-rolled plate according to claim 6 is characterized in that described annealing temperature is 800～820 ℃, and soaking time is 120～180s.
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| RU2755318C1 (en) * | 2020-10-08 | 2021-09-15 | Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") | Method for producing high-strength cold-rolled continuously annealed flat stock of if-steel |
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2008
- 2008-09-27 CN CN200810013481A patent/CN101684533A/en active Pending
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