CN102953001A - Cold-rolled steel sheet with tensile strength larger than 900 MPa and manufacturing method thereof - Google Patents
Cold-rolled steel sheet with tensile strength larger than 900 MPa and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a cold-rolled steel sheet with tensile strength larger than 900 MPa and a manufacturing method of the cold-rolled steel sheet. The cold-rolled steel sheet is composed of the following ingredients in percentage by weight: 0.06-0.095wt% of C, 0.1-0.4wt% of Si, 1.2-1.6wt% of Mn, 0.001-0.004% of B, not larger than 0.015wt% of P, not larger than 0.004wt% of S, 0.003-0.007wt% of N, 0.01-0.03wt% of Nb, 0.03-0.06% of Ti, 0.015-0.045wt% of Al, 0.002-0.007wt% of Ca and the rest balance of Fe and inevitable impurities. Cold-rolled high strength steel with tensile strength larger than 900 MPa and excellent cold bending property and delayed cracking resistance is obtained by reasonable ingredient design and technique design in the invention, and the steel has the characteristics of small and uniform tissues and excellent cold bending property. Meanwhile, the delayed cracking resistance of the steel is excellent, so that the steel meets the manufacturing demands of safety elements and structural members of automobiles.
Description
Technical field
The present invention relates to cold-rolled steel sheet and manufacture method, the particularly above cold-rolled steel sheet of a kind of tensile strength 900MPa and manufacture method, this steel has the cold-bending property excellence, the characteristics of anti-delayed fracture excellent property.
Background technology
Automotive industry requires to use more high-intensity steel plate for the needs of loss of weight.Wherein, tensile strength more and more becomes the first-selection of automobile industry at 900MPa and above ultrahigh-strength steel thereof, because the steel of this intensity rank can effectively alleviate body of a motor car weight, improves security.High Strength Steel Plate is in automobile manufacturing process, and its deformability is occured by crackle mainly and expansion control, and is therefore very high for the partial plastic forming Capability Requirement, also namely hole expansibility and bending property had relatively high expectations.Traditional high-strength steel, often have lower yield tensile ratio and higher unit elongation, possessed good draw forming ability, but because the defectives such as avulsion, necking down when the high-strength steel parts of making take forming modes such as bending, alternating bending and reamings as the master, easily occur in the partial plastic forming deficiency.Generally contain in the high-strength steel than the high alloy element, component segregation easily occurs in the castingprocesses, cause follow-up material because composition and tissue inhomogeneous causes the local deformaton ability to descend, i.e. hole expansibility and clod wash is poor etc.In addition, all unavoidably have inclusion in the steel, plastic occluded foreignsubstance can extend in the operation of rolling of steel, becomes the micro-crack source, further reduces the partial plastic forming ability of steel.
Also there is the possibility of delayed fracture in high-strength steel, generally there is internal stress in steel plate afterwards in shaping, if be subject to the invasion and attack of hydrogen this moment, hydrogen is gathered in the expansion that crack tip can cause crackle, presents progressively crack propagation and final " the delayed fracture phenomenon " that ftractures under the effect of internal stress.It is an important problem that the corresponding high-strength steel of delayed fracture is used, because delayed fracture is not easy discovery, progressively occurs in the part use procedure, may cause a series of problems concerning safety.
Japanese patent laid-open 11-350038 discloses the steel of the good 980MPa of a kind of ductility and plasticity, its Composition Design is C:0.1-0.15%, Si:0.8-1.5%, Mn:1.5-2.0%, P:0.01-0.05%, S≤0.005%, Sol Al:0.01-0.07%, N :≤0.01%, Nb:0.001-0.02%, V:0.001-0.02%, one or more among the Ti:0.001-0.02%.Carbon equivalent=(C+Mn/6+Si/24)=0.4-0.52, in the above hot rolling of Ar3,500-650 ℃ is batched, and is incubated between Ac1-AC3, is cooled to 580-720 ℃, be as cold as room temperature soon after, 230-300 ℃ of overaging.
The clear 63-38526 of Japanese Patent introduces the good high tensile steel plate of a kind of bending property and manufacture method thereof, C:0.1-0.2%, and Si≤0.7%, Mn:1.5-2.5%, S≤0.008%, Al :≤0.1%, Ti:0.05-0.15%, or add Ca:0.005%.By 850-950 ℃ of finish to gauge, 500-650 ℃ is batched, in annealing below 930 ℃ more than the recrystallization temperature, 3-200 ℃/s cooling, then be incubated 2-10 minute, holding temperature is controlled between 1100 ℃～annealing temperature and the 1200 ℃～annealing temperature, finally obtains the high-strength steel of 100kg, and bending radius can reach 0.5～1mm.70 ℃/s of typical case's speed of cooling.
The composition characteristic of above patent be carbon content more than 0.1%, and manganese content is higher.When carbon content is higher than 0.1%, the situation that easily occurs the column crystal Fast Growth in the process of setting, and the space between the column crystal is larger, the molten steel of solute enrichment easily flow into the column crystal gap, cause the aggravation of segregation, Mn content is higher in addition, the segregation degree is high and be difficult to eliminate, therefore all unfavorable for homogeneity and the cold-bending property of tissue, performance, easily cause performance inconsistency and inhomogeneous on the microcosmic, the longitudinal bending performance is undesirable, and anisotropy is large, and the performance of anti-delayed fracture is undesirable.
Summary of the invention
The object of the present invention is to provide the above cold-rolled steel sheet of a kind of tensile strength 900MPa and manufacture method, design by the reasonable component design and processes, obtain the above cold-bending property of tensile strength 900MPa and the cold rolling high strength steel of anti-delayed fracture excellent property, the characteristics of this steel are that fine microstructures is even, and cold-bending property is excellent; Simultaneously, the anti-delayed fracture excellent property of steel makes it meet the requirement of car safety spare and structural part manufacturing.
For achieving the above object, technical scheme of the present invention is:
The problem that draw point of the present invention is had relatively high expectations to local plasticity to high-strength steel by suitable Composition Design and technological design, under normal process conditions, just can obtain good comprehensive mechanical property.Concrete measure is, by the appropriate design of carbon, silicon, manganese, boron, titanium, nitrogen, Ca, obtains desirable tissue and distribution of carbides, reduces the segregation tendency, obtains desirable homogeneity of structure.Select lower carbon content scope, thereby control the process of setting of steel, reduce the overgrowth of column crystal in the casting cycle, reduce C, Mn, S, the P segregation in steel, thereby alleviate banded structure; Select lower Si content, be conducive to reduce the defectives such as surface of steel plate red rust, adopt lower manganese content, on the one hand reduce the machining stress of hot rolling, cold rolling process, be conducive to simultaneously to avoid the macrosegregation that is difficult to eliminate, in order to remedy the low deficiency of Mn content, add certain B element to guarantee hardening capacity, B is interstitial element, has preferably diffustivity, and its segregation is easier to eliminate or improve.Whole Composition Control is to reduce segregation, and the reduction banded structure is main thought.The contents level of control nitrogen adds the Ti that surpasses stoichiometric ratio simultaneously in higher scope, guarantee to generate enough TiN, as the trap of hydrogen invasion, avoids hydrogen to be gathered in the tiny crack tip, alleviates hydrogen-induced delayed cracking.Low S design adds Ca and improves the inclusion shape, improves inclusion to the detrimentally affect of cold-bending property.The Ti that exceeds simultaneously stoichiometric ratio separates out with the form of TiC, is conducive to thinning microstructure, improves homogeneity of structure.Hot rolling technology has adopted higher finishing temperature and normal coiling temperature on the low side, can guarantee homogeneous microstructure, again can crystal grain thinning; Can not be higher during annealing the annealing holding temperature, and sufficient bag temperature time is to realize homogeneous chemical composition as far as possible, avoiding banded forms, just just be cooled to simultaneously more than 700 ℃ with high speed to avoid the diffustivity segregation, to obtain simultaneously the tissue of even refinement but to below 200 ℃.The finished product carbon equivalent is low, surface quality is high, has simultaneously good cold-bending property and anti-delayed fracture performance.
Particularly, the above cold-rolled steel sheet of tensile strength 900MPa of the present invention, its composition weight percent is:
C：0.06～0.095wt％，
Si：0.1～0.4wt％，
Mn：1.2～1.6wt％，
B：0.001～0.004％，
P：≤0.015wt％，
S：≤0.004wt％，
N：0.003～0.007wt％，
Nb：0.01～0.03wt％，
Ti：0.03～0.06％，
Al：0.015～0.045wt％，
Ca：0.002～0.007wt％，
Surplus is Fe and inevitable impurity.
Preferably, its composition weight percent is: C:0.07～0.09wt%, Si:0.15～0.35wt%, Mn:1.2～1.6wt%, B:0.002～0.004%, P :≤0.01wt%, S :≤0.002wt%, N:0.0035～0.0055wt%, Nb:0.01～0.03wt%, Ti:0.035～0.05%, Al:0.02～0.04wt%, Ca:0.003～0.006wt%.
In the Composition Design of steel of the present invention:
C: affect martensitic hardness and content, very large to intensity effect.Carbon content is high easily grows up to column crystal in the unfavorable while casting cycle of weldability, causes intercrystalline segregation.The present invention selects carbon content between 0.06-0.095wt%, can effectively avoid the hypertrophy of column crystal, if carbon content is lower than 0.06%, and insufficient strength; If be higher than 0.095%, column crystal is flourishing, is difficult for formation and waits axle columnar ferrite crystal grain.
Si: in steel, play the effect that improves unit elongation.Si is also very large on the tissue impact of steel.Si easily forms oxide film at surface enrichment.The span of control of Si is 0.1-0.4%, if be higher than 0.4%, easily affects surface quality.
Mn: can improve the hardening capacity of steel, the intensity of Effective Raise steel, Mn is segregation in steel, easily is rolled into the Mn enrichment region that becomes band and distribute in course of hot rolling, forms banded structure, is unfavorable for cold-bending property.The content of choosing Mn is 1.2-1.6%, cooperates the low-carbon (LC) design, greatly improves the generation of banded structure.
B: can improve the hardening capacity of steel, the intensity of Effective Raise steel; In the situation that do not add Mo, add B 0.002-0.004%, be lower than 0.002% B, insufficient strength is higher than 0.004% B intensity higher.
P: be impurity element in steel, requirement≤0.015wt%.
S: be impurity element in steel, form MnS and have a strong impact on hole expansibility, require≤0.004%.
Al: in steel, played the effect of desoxydatoin and crystal grain thinning, required Al:0.015-0.045wt%.
N: in steel and Ti reaction generate TiN, TiN can be as hydrogen trap, forms a certain amount of rear beneficially to improving hydrogen-induced delayed cracking, requires 0.003-0.007wt%.Crossing low TiN, to separate out few effect that improves delayed fracture not obvious, too high unfavorable to clod wash.
Ti:0.02-0.045% plays the effect of fixed nitrogen element and crystal grain thinning.
Nb: be the precipitation strength element, play the effect of adjusting strength, require to be distributed between the 0.01-0.03wt%.
Ca: to the MnS modification, make it to form and disperse and short inclusion, be conducive to improve cold-bending property.The addition of Ca should guarantee Ca/S 〉=1.5.
Composition Design of the present invention is the useful effect of the common generation of the compound action of multiple element.Aspect the raising cold-bending property, by the low-carbon (LC) design, be aided with the compound interpolation of manganese, boron, and Ca processes and the microalloy crystal grain thinning.Adopt lower carbon, and adopt rational continuous casting process for cooling, can reduce the growth of column crystal in the casting cycle, finally obtain the cast structure of the carbide of granular ferrite+disperse distribution.Because the small-particle that carbide becomes disperse to distribute is distributed on the ferrite matrix, has therefore effectively alleviated C, the Mn segregation in steel, thereby alleviated banded structure; Can avoid forming the banded martensitic stucture of continuous distribution.Aspect the hardenability element, adopt lower manganese content, be aided with preferably B of diffustivity, be conducive to alleviate segregation and eliminate the macrosegregation that is difficult to eliminate.Adopt low S design, add Ca and improve the inclusion shape.Alleviated the detrimentally affect of inclusion to cold-bending property.
Aspect the improvement of delayed fracture performance, adopt on the one hand the low-carbon (LC) design, can reduce the martensitic hardness of formation, improve the intensity of steel by improving martensite volume, the supression effect of softer martensite On Crack Propagation is better.Simultaneously, because the segregation of steel is slighter, the component segregation district of rich carbon and rich Mn is less in the steel, can not form the martensitic phase of high rigidity, therefore, has further improved the anti-delayed fracture performance of steel.Add simultaneously the Ti that surpasses stoichiometric ratio, guarantee to generate enough TiN, as the trap of hydrogen invasion, avoid hydrogen to be gathered in the tiny crack tip, alleviate hydrogen-induced delayed cracking.The Ti that exceeds simultaneously stoichiometric ratio separates out with the form of TiC, is conducive to thinning microstructure, improves homogeneity of structure.
The manufacture method of the above cold-rolled steel sheet of tensile strength 900MPa of the present invention, it comprises the steps:
1) smelt, press mentioned component and smelt, deeply take off S, converter adds refining, and S is controlled at below 0.004%, reduces MnS and is mingled with;
2) continuous casting, 0.9～1.4 m/min pulling speed of continuous casting helps inclusion floating and reduces segregation;
3) hot rolling, be heated to 1200～1280 ℃ after hot rolling, 840～940 ℃ of finishing temperatures are rolled rear quick cooling, 15～40 ℃/s of speed of cooling is cooled to batch between 500～620 ℃;
4) cold rolling, 40～65% drafts;
5) annealing, 830～860 ℃ of insulations, insulation 60～200s; 5～10 ℃/s is cooled between 700～750 ℃, is cooled to below 300 ℃ in the mode of water-cooled, and is then behind 200～300 ℃ of tempering 100～400s, smooth through 0.1～0.3% again.
Further, described pulling speed of continuous casting is 1～1.2 m/min.
Again, in the described hot-rolled step, be heated to 1220～1260 ℃, 860～920 ℃ of finishing temperatures are rolled rear evenly fast cooling, and 20～40 ℃/s of speed of cooling is cooled to batch between 520～600 ℃.
In addition, in the described annealing process, 840～860 ℃ of holding temperatures, insulation 80～100s; 5～10 ℃/s is cooled between 720～750 ℃, is cooled to below 200 ℃ in the mode of water-cooled, and is then through behind 200～300 ℃ of tempering 100～400s, smooth through 0.1～0.3% again.
Beneficial effect of the present invention:
The characteristics of steel of the present invention are mainly for the raising of cold-bending property and two aspects of improvement of anti-delayed fracture performance.By the low-carbon (LC) design, be aided with the compound interpolation of manganese, boron, and Ca processing and microalloy crystal grain thinning, and effectively alleviated C, the Mn segregation in steel, and alleviating banded structure, the inclusion shape improves simultaneously, thereby has improved the cool bending natures of steels energy.
In addition, by adopting the low-carbon (LC) design, can reduce the martensitic hardness of formation, the supression effect of softer martensite On Crack Propagation is better.Simultaneously, because the segregation of steel is slighter, can not form the martensitic phase of extreme hardness, therefore, favourable to improving anti-delayed fracture performance.Add simultaneously the Ti that surpasses stoichiometric ratio, guarantee to generate enough TiN, as the trap of hydrogen invasion, avoid hydrogen to be gathered in the tiny crack tip, alleviate hydrogen-induced delayed cracking.
In addition, hot rolling technology of the present invention has adopted higher finishing temperature and lower coiling temperature, can guarantee homogeneous microstructure, again can crystal grain thinning; With higher annealing holding temperature, and sufficient soaking time to realize homogeneous chemical composition as far as possible, is avoided banded and is formed during annealing.Martensite is evenly distributed in the tissue of steel of the present invention, and banded structure is slight, and the amount of inclusions is few and be evenly distributed; Can produce high-strength steel more than the intensity 900MPa according to the present invention, cold-bending property is good, anti-delayed fracture excellent property, and simultaneously, carbon equivalent is low, is conducive to welding, and surface quality is good.High-strength steel balancing performance of the present invention is stable, can adapt to well the needs that automobile component are made.
Embodiment
The present invention will be further described below in conjunction with embodiment.
Table 1 is the chemical composition of steel embodiment of the present invention.Table 2 is the technique of steel of the present invention.Table 3 for steel of the present invention through smelting, hot rolling, cold rolling, annealing and smooth after the performance intensity that obtains.As can be seen from Table 3, can produce high strength dual phase steel more than the intensity 900MPa according to the present invention, its cold-bending property is good.Adopt its delayed fracture characteristic of the curved test of U, specimen size is that the rectangular specimen U bend diameter of 150mm * 20mm is 80mm, sample is curved U-shaped, and fixes with bolt.The HCl solution of preparation 5% at room temperature immerses solution with sample, record sample crackle crack initiation time and rupture time.
Compared steel 1 is taken from commercially available conventional 1000MPa high-strength steel, and compared steel 2 is the steel that does not have the delayed fracture tendency of 600MPa for intensity.Compared steel 1 can satisfy service requirements substantially, may have the tendency of delayed fracture; And compared steel 2 intensity are low, do not have the delayed fracture tendency, choose as contrast delayed fracture characteristic of the present invention.Can see that steel of the present invention obviously is better than compared steel 1 in the performance of delayed fracture simulation test, reached the level equal with compared steel 2, show that the present invention is with respect to the high-strength steel with intensity rank, its delayed fracture characteristic has larger improvement, has approached the low strength rank steel grade that does not have the delayed fracture tendency.
Table 1 unit: wt%
Table 2
Table 3
Claims (6)
1. above cold-rolled steel sheet of tensile strength 900MPa, its composition weight percent is:
C：0.06～0.095wt％，
Si：0.1～0.4wt％，
Mn：1.2～1.6wt％，
B：0.001～0.004％，
P：≤0.015wt％，
S：≤0.004wt％，
N：0.003～0.007wt％，
Nb：0.01～0.03wt％，
Ti：0.03～0.06％，
Al：0.015～0.045wt％，
Ca：0.002～0.007wt％，
Surplus is Fe and inevitable impurity.
2. the above cold-rolled steel sheet of tensile strength 900MPa as claimed in claim 1 is characterized in that, its composition weight percent is preferably C:0.07～0.09wt%, Si:0.15～0.35wt%, Mn:1.2～1.6wt%, B:0.002～0.004%, P :≤0.01wt%, S :≤0.002wt%, N:0.0035～0.0055wt%, Nb:0.01～0.03wt%, Ti:0.035～0.05%, Al:0.02～0.04wt%, Ca:0.003～0.006wt%.
3. the manufacture method of the above cold-rolled steel sheet of tensile strength 900MPa as claimed in claim 1 or 2, it comprises the steps:
1) smelt, press mentioned component and smelt, deeply take off S, converter adds refining, and S is controlled at below 0.004%, reduces MnS and is mingled with;
2) continuous casting, 0.9～1.4 m/min pulling speed of continuous casting helps inclusion floating and reduces segregation;
3) hot rolling, be heated to 1200～1280 ℃ after hot rolling, 840～940 ℃ of finishing temperatures are rolled rear quick cooling, 15～40 ℃/s of speed of cooling is cooled to batch between 500～620 ℃;
4) cold rolling, 40～65% drafts;
5) annealing, 830～860 ℃ of insulations, insulation 60～200s; 5～10 ℃/s is cooled between 700～750 ℃, is cooled to below 300 ℃ in the mode of water-cooled, and is then behind 200～300 ℃ of tempering 100～400s, smooth through 0.1～0.3% again.
4. the manufacture method of the above cold-rolled steel sheet of tensile strength 900MPa as claimed in claim 3 is characterized in that, described pulling speed of continuous casting is 1～1.2 m/min.
5. the manufacture method of the above cold-rolled steel sheet of tensile strength 900MPa as claimed in claim 3, it is characterized in that, in the described hot-rolled step, be heated to 1220～1260 ℃, 860～920 ℃ of finishing temperatures, roll rear evenly fast cooling, 20～40 ℃/s of speed of cooling is cooled to batch between 520～600 ℃.
6. the manufacture method of the above cold-rolled steel sheet of tensile strength 900MPa as claimed in claim 3 is characterized in that, in the described annealing process, and 840～860 ℃ of holding temperatures, insulation 80～100s; 5～10 ℃/s is cooled between 720～750 ℃, is cooled to below 200 ℃ in the mode of water-cooled, and is then through behind 200～300 ℃ of tempering 100～400s, smooth through 0.1～0.3% again.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102747280A (en) * | 2012-07-31 | 2012-10-24 | 宝山钢铁股份有限公司 | Wear resistant steel plate with high intensity and high toughness and production method thereof |
| CN107699791A (en) * | 2017-09-28 | 2018-02-16 | 邯郸钢铁集团有限责任公司 | High cold-bending property low-alloy high-strength steel plate of 900MPa levels and preparation method thereof |
| JP2022507855A (en) * | 2018-11-23 | 2022-01-18 | 宝山鋼鉄股▲分▼有限公司 | High yield ratio cold rolled duplex stainless steel and its manufacturing method |
| WO2024041540A1 (en) * | 2022-08-23 | 2024-02-29 | 宝山钢铁股份有限公司 | 60-kilogram-grade cold-rolled low-alloy annealed dual-phase steel and manufacturing method therefor |
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| CN1788099A (en) * | 2003-06-19 | 2006-06-14 | 新日本制铁株式会社 | High strength steel plate excellent in formability and method for production thereof |
| CN101851732A (en) * | 2009-03-31 | 2010-10-06 | 株式会社神户制钢所 | The high strength cold rolled steel plate of excellent in bending workability |
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| CN1788099A (en) * | 2003-06-19 | 2006-06-14 | 新日本制铁株式会社 | High strength steel plate excellent in formability and method for production thereof |
| CN101851732A (en) * | 2009-03-31 | 2010-10-06 | 株式会社神户制钢所 | The high strength cold rolled steel plate of excellent in bending workability |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102747280A (en) * | 2012-07-31 | 2012-10-24 | 宝山钢铁股份有限公司 | Wear resistant steel plate with high intensity and high toughness and production method thereof |
| CN102747280B (en) * | 2012-07-31 | 2014-10-01 | 宝山钢铁股份有限公司 | Wear resistant steel plate with high intensity and high toughness and production method thereof |
| US9797033B2 (en) | 2012-07-31 | 2017-10-24 | Baoshan Iron & Steele Co., Ltd. | High-strength, high-toughness, wear-resistant steel plate and manufacturing method thereof |
| CN107699791A (en) * | 2017-09-28 | 2018-02-16 | 邯郸钢铁集团有限责任公司 | High cold-bending property low-alloy high-strength steel plate of 900MPa levels and preparation method thereof |
| CN107699791B (en) * | 2017-09-28 | 2019-05-03 | 邯郸钢铁集团有限责任公司 | 900MPa grades high cold-bending property low alloy high strength steel plate and preparation method thereof |
| JP2022507855A (en) * | 2018-11-23 | 2022-01-18 | 宝山鋼鉄股▲分▼有限公司 | High yield ratio cold rolled duplex stainless steel and its manufacturing method |
| WO2024041540A1 (en) * | 2022-08-23 | 2024-02-29 | 宝山钢铁股份有限公司 | 60-kilogram-grade cold-rolled low-alloy annealed dual-phase steel and manufacturing method therefor |
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