CN103556048A - Two-phase automobile steel plate with low yield-strength ratio and high strength and production method of two-phase automobile steel plate - Google Patents
Two-phase automobile steel plate with low yield-strength ratio and high strength and production method of two-phase automobile steel plate Download PDFInfo
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Abstract
The invention discloses a two-phase automobile steel plate with low yield-strength ratio and high strength and a production method of the two-phase automobile steel plate, belonging to the technical field of steel for automobiles. The two-phase automobile steel plate comprises the following chemical components: 0.1-0.40wt% of C, 3.0-8.0wt% of Mn, less than or equal to 0.020wt% of P and less than or equal to 0.02wt% of S; on the basis, the two-phase automobile steel plate can be additionally provided with one or more of the following elements: 0.1-3.0wt% of Ni, 0.2-3.0wt% of Cr, 0.1-0.8wt% of Mo, 0.3-2.3wt% of Si, 0.5-2.0wt% of Cu, 0.0005-0.005wt% of B, 0.02-0.10wt% of Nb, 0.002-0.25wt% of [N], 0.05-0.25wt% of Ti, 0.02-0.25wt% of V, 0.015-0.060wt% of Al, 0.002-0.005wt% of RE (Rare Earth) and 0.005-0.03wt% of Ca. The two-phase automobile steel plate has the advantages that the two-phase automobile steel plate with low yield strength, high tension strength and favorable elongation can be produced through annealing within short time; the performance indexes of the two-phase automobile steel plate are as follows: two-phase steel with the tension strength of 980MPa has the yield-strength ratio of not larger than 0.55 and the elongation of larger than 22%, and two-phase steel with the tension strength of 1180MPa has the yield-strength ratio of not larger than 0.55 and the elongation of larger than 17%.
Description
Technical field
The invention belongs to the production technical field of automobile steel coiled sheet, a kind of low yield strength ratio, high-strength vehicle dual phase sheet steel and production method are particularly provided, by continuous annealing production line produce a kind of have excellent formability, steel dual phase steel coiled sheet for high-strength vehicle, its tensile strength is more than 1GP, but the ratio of yield strength and tensile strength is between 0.45-0.65, there are enough unit elongation simultaneously, improving auto sheet intensity with when realizing loss of weight object, the easy plasticity while also simultaneously guaranteeing steel plate punched.
Background technology
Along with the raising of automotive light weight technology and security requirement, require automobile structure to improve constantly by the intensity of steel, to realize loss of weight with thinner steel plate under the condition that meets security prerequisite.In many automobile steels, dual phase steel (DP steel) has good mechanical property and processability, becomes desirable automotive sheet.In AHSS plate (AHSS) tandem product of having developed, high strength dual phase steel plate is one of the widest kind of application surface in automobile.In IISI's ultralight steel car body plan-advanced car concept (ULSAB-AVC) and U.S. young mobile partner plan (PNGV) project; the bicycle consumption of DP steel is 162.25kg, accounts for 74.3% of AHSS plate total mass for car load; North America dual phase steel consumption in 2010 accounts for 45% of automobile steel total amount.DP600, DP780 and the DP1000 steel developed at present both at home and abroad, be suitable for producing the structural part of automobile and safety component etc., as longeron, crossbeam and stiffener etc.But along with the significantly raising of steel plate tensile strength, be conventionally accompanied by yield strength and also improve and unit elongation decline thereupon.Yield strength raises and to cause material to be difficult to distortion, so the load that the power of stamping machine and mould bear all will significantly improve, and decline to die life; In addition, yield strength raises and causes yield tensile ratio to increase, and the uniform elongation of material declines, thereby unit elongation decline can cause steel plate to ftracture and scrap when punching press.Therefore, in the intensity that improves autobody sheet simultaneously, guaranteeing the easy plasticity of steel plate by low yield strength (maintaining low yield tensile ratio) and high unit elongation, is the mechanical performance index having of desirable automotive sheet.But high tensile strength and low yield strength, high-elongation are all runed counter under normal conditions, this just need to carry out ingehious design and achieve the above object the composition of steel, tissue.
Table 1 Nippon Steel formula dual phase steel product performance
| The trade mark | Yield strength/MPa | Yield strength/MPa | Unit elongation, % | Yield tensile ratio, % | Thickness, mm |
| DP590 | 318 | 610 | 31 | 52 | 1.6 |
| DP780 | 437 | 829 | 22 | 53 | 1.6 |
| DP980 (type A) | 630 | 1006 | 17 | 63 | 1.6 |
| DP980 (type B) | 716 | 1015 | 15 | 71 | 1.6 |
| DP1180 | 900 | 1199 | 11 | 75 | 1.6 |
The Japanese JFE of table 2 company dual phase steel product performance
Table 3 meter tal fibre company dual phase steel product performance
Table 4 Pu Xiang company dual phase steel product performance
Table 1 to table 4 has provided respectively external advanced iron and steel enterprise about the performance index of each trade mark of DP product made from steel, this shows, for other dual phase steel of DP980 level (being that tensile strength surpasses 980MPa), the product requirement SMYS 630-716MPa of Nippon Steel Corp, unit elongation 15-17%; Its SMYS of the product 530MPa of JFE company, unit elongation 12-14%; The SMYS of meter Ta Er company product is at 662MPa, unit elongation 13%; Pu Xiang company product SMYS is minimum is 490MPa, but unit elongation is only 6-7%.And for other dual phase steel of DP1180 level (being that tensile strength is 1180MPa), its yield strength of Nippon Steel Corp's product is 900MPa, unit elongation is 11%; JFE company product yield strength is 710MPa, and unit elongation is only 7-11%.And the present invention can maintain two rank dual phase steel high-tensiles of DP980 and DP1180 simultaneously, significantly reduce its yield strength and improve its unit elongation, the plasticity performance of this steel plate is significantly improved.This improvement in performance mainly realizes by new Composition Design and microstructure ultra-fining treatment.In existing industrialized dual phase steel, its Mn content is many in 1-3.5%(weight percentage) between; And the present invention adopts the Composition Design of 3.0-8.5%Mn content, and carbon content is still at conventional interval (0.1-0.4%).The design of this high Mn content significantly increases the hardening capacity of steel, even even if coolingly after hot rolling reeling more also can obtain martensitic stucture, when this martensitic stucture only needs a short period of time continuous annealing (being less than 10 minutes), on Jiu Ke martensite lath circle, forming core forms austenite crystal and the annealing ferrite crystal grain of submicron-scale, the tiny austenite crystal of part can pass through interfacial diffusion fast enriching Mn and C simultaneously, cause obtaining ultra-fine martensite after cooling and ferrite is main duplex structure, and contain due to rich Mn and C and residual tiny austenite crystal, this super fine organization has caused low yield strength (depending on ferritic phase), high tensile strength (depending on martensitic phase), and simultaneously because Mn content in steel is significantly higher than common automobile steel, the tiny austenite crystal further enrichment C of meeting and Mn in annealed rear section, the stability of these austenite crystals significantly increases and causes after cooling still remaining, and then in follow-up distortion, there is also to have improved when deformation induced phase transformation (TRIP effect) is being gained in strength the plasticity of steel plate, describe in detail below.
Summary of the invention
The object of the present invention is to provide a kind of low yield strength ratio, high-strength vehicle dual phase sheet steel and production method, can manufacture by the continuous annealing production line of existing industrialization (in annealing time 10 minutes) the dual phase steel automobile coiled sheet of low yield strength, high-tensile and good unit elongation.
The present invention is based on the partition of reasonable chemical composition design and alloying element, key contains enough austenitizing stable element Mn in being in steel plate, and the initial tissue before final two-phase region continuous annealing is martensitic stucture, the ferrito-martensite that can form submicron-scale after annealing is main tissue, contain the tiny austenite structure of enrichment C and Mn simultaneously, and then guaranteed low yield strength, high-tensile and the good unit elongation of this steel.Although the constituent class of steel of the present invention and the high-strength high-ductility automobile steel of the third generation (CN101638749A patent) seemingly, but because annealing temperature is different, cause organizing completely different, the former matrix is ferrite and martensite, and the latter is ferrite and austenite, finally cause mechanical property also very not identical.Essential characteristic of the present invention is:
1,, in the chemical composition of steel, be mainly to realize by 0.1-0.4wt%C and 3.00-8.00wt%Mn alloying.
2, before final two-phase region continuous annealing, its structural state is martensite, and can not have size to surpass carbide or cementite more than 50nm;
3, the present invention requires steel to be heated to a suitable two-phase region temperature insulation no longer than 10 minutes, that austenite forms austenite by ferrite to austenitic reverse transformation at ferrite grain boundaries forming core on the one hand, the tiny transition carbide (size is less than 30nm) forming early stage on the other hand thus can the carbon of enrichment and manganese have been discharged complete solid solution, cause reverse transformation process to be accelerated and the more rich manganese of austenite.Thereby after continuous annealing in short-term, just can in the finished product tissue, obtain that more than 30% size is tiny, the austenite that is evenly distributed and the α phase matrix of ultra-fine size.
4, by the technology of the present invention, can prepare steel continuous annealing coiled sheet for other high-strength vehicle of two levels, yield strength corresponding to 980MPa tensile strength rank is no more than 540MPa, and yield tensile ratio is less than 0.55, and minimum unit elongation is 21%; Yield strength corresponding to 1180MPa tensile strength rank is no more than 650MPa, and yield tensile ratio is less than 0.55, and minimum unit elongation is 17%.This index is all better than the like product of existing external advanced Iron And Steel Company.
Can also further improve or reach performance by following technology on the basis of the above: 1, can add Ni, Mo, Cr, B etc. and further improve the refinement original austenite grains such as the hardening capacity of steel or low-temperature impact toughness, interpolation Nb, V, Ti, add Cu, V etc. and by precipitation strength, improves the intensity of steel and add the raisings intensity such as Si and inhibition Carbide Precipitation etc., interpolation [N] regulate austenitic stability etc.; 2, by rolling technologys such as hot rolling or warm-rollings, control the homogeneity of the heterogeneous microstructure of steel, refining grain size, for final thermal treatment provides desirable weave construction.The present invention is applicable to the production of the production of high-performance cold rolled and hot-rolled high-strength auto sheet, high-performance section bar and excellent wire rod etc. under existing industrial condition.Be equally applicable to realize high performance product by thermal treatment means, as thermoforming part etc.
Key component scope of the present invention and processing parameter are described as follows:
The chemical composition of steel of the present invention is: C:0.1-0.40wt%, Mn:3.0-8.0wt%, P≤0.020wt%, and S≤0.02wt%, surplus is Fe and inevitable impurity.Can separately be descended a kind of or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE(rare earth on this basis): 0.002-0.005wt%, Ca:0.005-0.03wt%.
The effect of each element of the present invention and proportioning are according to as follows:
C: the gap solution strengthening element as main, plays a decisive role to the intensity of quenched martensite steel.Partition by carbon can regulate and control to reverse to become stabilization of austenite, quantity, size, shape and distribution; But carbon content is too high, will worsen the performance of steel, C content should be controlled within the scope of 0.1-0.40wt%.
Mn:Mn has the effect of the hardening capacity that improves steel.Mn expands austenitic area element, by the partition again of Mn in warm treating processes, realize reversing and turn austenitic generation.In the present invention, Mn controls to reverse the one of the chief elements that turns austenitic stability, distribution and size thereof.For guaranteeing high-ductility and the intensity of steel, Mn content should be controlled within the scope of 3.0-8.0%.
Ni:Ni is austenitizing stable element, can effectively reduce Ms point, can improve material plasticity and low-temperature flexibility, but Ni price is high simultaneously, and its content should be controlled at below 2.0%.
P: form microsegregation when solidification of molten steel, when temperature heats after austenite subsequently, segregation, to crystal boundary, enlarges markedly the fragility of steel, raises thereby make hydrogen cause delayed fracture susceptibility.Therefore, P content should be controlled at below 0.020%.
S: inevitable impurity, forms MnS inclusion and can worsen the toughness of steel at grain boundary segregation, thereby reduce the toughness plasticity of steel, and make hydrogen cause delayed fracture susceptibility to raise.Therefore, S content should be controlled at below 0.015%.
Mo: effectively improve the hardening capacity of steel, can also strengthen crystal boundary.Content is less than 0.20% to be difficult to function as described above, but content is saturated over 0.80% above-mentioned action effect, and cost is higher, should be controlled within the scope of 0-0.8wt%.
Cr: can effectively improve the hardening capacity of steel and prevent high temperature surface oxidation, Cr content should be controlled at 0.1-3.0wt%.
Cu: realize precipitation strength by separating out ε-Cu, improve the intensity of steel, add scope 0.1-2.00wt%.
B: can significantly improve the hardening capacity of steel and purify crystal boundary.Content above effect lower than 0.0005% time is not obvious, and effect increases not obvious higher than 0.0050% time.Therefore,, as added, B content should be controlled within the scope of 0.0005-0.0050wt%.
Si: suppress Carbide Precipitation, improve the partition effect of C.Si content when following, can not play above effect 0.30%; Si content is higher than 2.30% time, and above effect is saturated, and may affect toughness.Therefore, Si content should be controlled within the scope of 0.30-2.30wt%.
Nb: forming carbonitride can crystal grain thinning, and the niobium of solid solution simultaneously can improve non-recrystallization district temperature, is easy to realize austenitic flattening by controlled rolling.Above-mentioned effect is not obvious lower than 0.02% time, and effect increases not obviously higher than 0.10% time, reaches capacity.Nb content should be controlled within the scope of 0.01-0.10wt%.
Ti: be a kind of strong carbonitride forming element, can form the carbonitride that small and dispersed distributes, play the effect of refine austenite crystal grain.Ti content should be controlled within the scope of 0.01-0.25wt%.
V: with tiny carbonitride, form while existing, can crystal grain thinning; While existing with solid solution form, can improve hardening capacity, thereby improve intensity.Add in right amount and can improve performance, easily form macrobead carbonitride higher than 0.15% time, make on the contrary toughness plasticity decline.In addition, V also has precipitation strength effect, can further improve the intensity of steel.V content should be controlled within the scope of 0.02-0.50wt%.
Al: effectively deoxidation and crystal grain thinning, improve toughness.Content above effect lower than 0.015% time is not obvious, and effect increases not obviously higher than 0.060% time, and may form thick aluminate, worsens the toughness of steel.Therefore, Al content should be controlled within the scope of 0.015-0.060wt%.
[N]: with Al, Ti, Nb, V etc. in conjunction with forming compound, thereby crystal grain thinning, but also can segregation crystal boundary and reduce grain-boundary strength.In addition, [N] is austenitic area expansion element, and it can improve reverse and turn austenitic stability.[N] content should be controlled within the scope of 0.002-0.35wt%.
RE: play deoxidation and desulfidation, and make inclusion modification, thereby can improve the toughness plasticity of steel.Above effect is not obvious lower than 0.001% time, and effect increases not obviously higher than 0.050% time, reaches capacity.Therefore,, as added, RE content should be controlled within the scope of 0.001-0.050wt%.
Ca: deoxidation and desulfurization, and make inclusion distortion, thus can improve the toughness plasticity of steel.The addition of Ca and the S content in molten steel are 3:1.Therefore, Ca content should be controlled within the scope of 0.005-0.030wt%.
The technical parameter of production technique of the present invention and control is:
(1) smelting of steel with solidify: be applicable to converter, electric furnace and induction furnace and smelt, smelt composition and be: 0.1-0.4wt%C and 3.0-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, remaining be Fe and inevitable impurity,
(2) solidify: adopt continuous casting to produce strand or die casting production ingot casting;
(3) hot continuous rolling of strand or ingot casting:
Hot continuous rolling: strand, through 1100-1250 ℃ of heating, is carried out to the rolling of 5-20 passage by roughing mill, and hot rolling is to 30-50mm thickness specification, connects unit by heat and carries out 5-7 passage and be rolled down to after 3-25mm, after rolling, at 250-700 ℃, batches, and volume is heavily no more than 15 tons;
(4) cold rolling: above-mentioned hot continuous rolling involves in after row cleanup acid treatment, at cold continuous mill group, is directly rolled after 0.8-4.0mm, obtains cold-rolled steel sheet;
Or by above-mentioned hot continuous rolling volume, through bell-type coil annealing, slow cooling reduces cold rolling processing load with softening tissue, then carries out pickling, cold rolling;
(5) when the cold-rolled steel sheet obtaining contains thicker carbide or cementite, need to utilize the continuous annealing production line of steel mill, steel plate heating is heated rapidly to Ac3+30 to 80 ℃ and carries out first annealing austenitizing, after insulation 3-10min, high-pressure air is chilled to soon within the scope of 150-350 ℃ and batches, and speed of cooling is not less than 10 ℃/s;
When not carbide-containing or cementite, through solution treatment, obtain the martensite lath of uniform-dimension, or omit this operation and directly enter (6) described two-phase region continuous annealing operation;
(6) by cooling fast after the annealing of 5-10 minute on industrial continuous annealing production line after pretreated annealing winds off volume, during heating, its rate of heating is greater than 50 ℃/s; When cooling, being cooled to 200 ℃ of times is no more than 50 seconds; Continuous annealing temperature T scope is as follows according to C in composition of steel and Mn cubage:
For 980MPa rank steel annealing temperature, be
1025-12×[%wtMn]-89×[%wtC]≤T(K)≤1055-12×[%wtMn]-89×[%wtC]
For 1080MPa rank steel annealing temperature, be
1040-12×[%wtMn]-89×[%wtC]≤T(K)≤1070-12×[%wtMn]-89×[%wtC]
Following rule is followed in the selection of annealing temperature and annealing time: when annealing temperature capping, annealing time removes the limit; And the former removes the limit, the latter's capping.
First advantage of the present invention is, the Composition Design of simple economy (mainly by C and Mn), through simple continuous annealing process once, just can produce with currently available products and compare, its intensity rank remains unchanged but the better two-phase automobile steel of (low yield strength ratio, high-elongation) of plasticity;
The present invention be advantageous in that and by existing industrial continuous annealing production line, through short-cycle annealing, just can produce the two-phase automobile steel of low yield strength, high-tensile and good unit elongation, its performance index reach following requirement: for tensile strength 980MPa rank dual phase steel, yield tensile ratio is no more than 0.55, and unit elongation is greater than 22%; For 1180MPa rank dual phase steel, its yield tensile ratio is no more than 0.55, and unit elongation is greater than 17%.
Accompanying drawing explanation
Fig. 1 is the relation of final residual austenite mark and annealing temperature.
Embodiment
Embodiment:
The present embodiment is mainly for the exploitation with continuous annealing steel plate in automobile, and process of the test is simulated pre-treatment and the continuous annealing process of cold-rolling of steel plate steel plate.But this technique is equally applicable to medium-thick plate, section bar and excellent wire rod.
The smelting of steel:
Steel of the present invention can cast out the continuously cast bloom of 200-220mm left and right by converter smelting as the chemical composition of table 5 through continuous caster, be rolling to the hot rolled coil of 3mm through hot continuous mill, and its coiling temperature >500 ℃, is cold-rolled to 1.6mm.The subsequent anneal of cold-reduced sheet completes on the annealing simulation machine in laboratory.Cold-rolled steel sheet is divided into two batches, (A) after 850 ℃ of solid solution half an hour, and air cooling after taking out; (B) without solution treatment.Then this cold-rolled steel sheet is quickly heated up to 670-710 insulation cold soon after 10 minutes, then measure residual austenite mark and mechanical property in the finished product, respectively as shown in Fig. 1 and table 6.
The chemical composition of table 5 invention steel, weight percentage
| ? | C | Mn | P | S |
| 1 | 0.1 | 5.0 | 0.01 | 0.005 |
| 2 | 0.20 | 5.0 | 0.009 | 0.002 |
Table 6 be composition shown in table 5 steel plate through 670-710 ℃ 10 minutes annealing after mechanical mechanics property
Claims (3)
1. low yield strength ratio, a high-strength vehicle dual phase sheet steel, is characterized in that, chemical composition is: C:0.1-0.40wt%, Mn:3.0-8.0wt%, P≤0.020wt%, and S≤0.02wt%, surplus is Fe and inevitable impurity; Separately descended on this basis a kind of or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE:0.002-0.005wt%, Ca:0.005-0.03wt%.
2. a production method for low yield strength ratio, high-strength vehicle use dual phase sheet steel described in claim 1, is characterized in that, the technical parameter of production technique and control is:
(1) smelting of steel with solidify: be applicable to converter, electric furnace and induction furnace and smelt, smelt composition and be: 0.1-0.4wt%C and 3.0-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, remaining be Fe and inevitable impurity,
(2) solidify: adopt continuous casting to produce strand or die casting production ingot casting;
(3) hot continuous rolling of strand or ingot casting:
Hot continuous rolling: strand, through 1100-1250 ℃ of heating, is carried out to the rolling of 5-20 passage by roughing mill, and hot rolling is to 30-50mm thickness specification, connects unit by heat and carries out 5-7 passage and be rolled down to after 3-25mm, after rolling, at 250-700 ℃, batches, and volume is heavily no more than 15 tons;
(4) cold rolling: above-mentioned hot continuous rolling involves in after row cleanup acid treatment, at cold continuous mill group, is directly rolled after 0.8-4.0mm, obtains cold-rolled steel sheet;
(5) when the cold-rolled steel sheet obtaining contains thicker carbide or cementite, need to utilize the continuous annealing production line of steel mill, steel plate heating is heated rapidly to Ac3+30 to 80 ℃ and carries out first annealing austenitizing, after insulation 3-10min, high-pressure air is chilled to soon within the scope of 150-350 ℃ and batches, and speed of cooling is not less than 10 ℃/s;
When not carbide-containing or cementite, through solution treatment, obtain the martensite lath of uniform-dimension, or omit this operation and directly enter (6) described two-phase region continuous annealing operation;
(6) by cooling fast after the annealing of 5-10 minute on industrial continuous annealing production line after pretreated annealing winds off volume, during heating, its rate of heating is greater than 50 ℃/s; The time that is cooled to 200 ℃ when cooling is no more than 50 seconds; Continuous annealing temperature T scope is as follows according to C in composition of steel and Mn cubage:
For 980MPa rank steel annealing temperature, be
1025-12×[%wtMn]-89×[%wtC]≤T(K)≤1055-12×[%wtMn]-89×[%wtC]
For 1080MPa rank steel annealing temperature, be
1040-12×[%wtMn]-89×[%wtC]≤T(K)≤1070-12×[%wtMn]-89×[%wtC]。
3. method according to claim 2, is characterized in that, in step (4), by above-mentioned hot continuous rolling volume, through bell-type coil annealing, slow cooling reduces cold rolling processing load with softening tissue, then carries out pickling, cold rolling.
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