CN102534373A - Super-high strength cold rolled steel belt suitable for rolling formation and manufacture method of super-high strength cold rolled steel belt - Google Patents
Super-high strength cold rolled steel belt suitable for rolling formation and manufacture method of super-high strength cold rolled steel belt Download PDFInfo
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Abstract
The invention provide a super-high strength cold rolled steel belt suitable for rolling formation and a manufacture method of the super-high strength cold rolled steel belt. The super-high strength cold rolled steel belt comprises the following ingredients by weight percent: 0.12 to 0.18 percent of C; 0.1 to 0.4 percent of Si; 0.4 to 0.9 percent of Mn; 0.001 to 0.003 percent of B; 0 to 0.015 percent of P; 0 to 0.004 percent of S; 0.003 to 0.008 percent of N; 0.02 to 0.06 percent of Ti; 0.015 to 0.045 percent of Al; 0.002 to 0.006 percent of Ca; and Fe and unavoidable impurities in balancing amount. Through a reasonable ingredient design and a process design, the super-high strength cold rolled steel belt suitable for rolling formation is obtained; the tissue distribution is uniform; the performance uniformity is high; and a steel belt-type tissue is light and small, so that the cold bending performance is high. Moreover, the hardenability is moderate; the weld joint strength of the super-high strength cold rolled steel belt after being welded is approximately the same as that of a base metal; and the content of Si in the super-high strength cold rolled steel belt is lower, so that the surface quality of the super-high strength cold rolled steel belt is better, which meets the requirements for rolling and manufacturing vehicle components.
Description
Technical field
The present invention relates to strong cold-rolled steel strip of superelevation and method of manufacture thereof, particularly a kind of super-high strength cold rolled steel band and method of manufacture thereof that is suitable for rolling formation.
Background technology
Automotive industry requires to use more high-intensity steel plate from the needs of loss of weight.Wherein, tensile strength more and more becomes the first-selection of automobile industry at 980MPa and above ultrahigh-strength steel thereof, because the steel of this intensity rank can effectively alleviate body of a motor car weight, improves security.Ultrahigh-strength steel is produced bigger than the steel difficulty of common intensity in steel mill, to equipment requirements is high, equipment loss is high and quality control is difficult.High Strength Steel Plate is in the automobile making process, because intensity is high, plasticity is low, ftractures easily, and the high-strength steel application difficulty is bigger.
The roll-in technology preferably resolves the difficult problem of shaping of super-high strength steel, and gradual mode of texturing is adopted in roll-in, progressively makes steel plate reach required shape.Roll-in to the requirement of high-strength steel be cold-bending property good, organize tiny evenly (performance uniformity is good), and weldableness is preferably arranged.The present invention is intended to invent a kind of ultrahigh-strength steel that is suitable for rolling formation, possesses higher yield tensile ratio, good cold-bending property, and homogeneous microstructure, performance is even, is suitable for rolling formation.
Japanese patent laid-open 11～350038 discloses the steel of the good 980MPa of a kind of ductility and plasticity, and its composition is designed to, 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 in 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 ℃ are batched, and between Ac1～AC3, are incubated, and are cooled to 580～720 ℃, be as cold as room temperature soon after, 230～300 ℃ of overaging.
Chinese patent 200810119823.0 discloses a kind of method of manufacture of 980MPa dual phase steel, C:0.14～0.21%, Si:0.4～0.9%; Mn:1.5～2.1%, P :≤0.02%, S≤0.01%; Nb:0.001～0.05%, V:0.001～0.02% is after hot rolling is cold rolling; Insulation between 760～820 ℃, 40～50 ℃/s of cooling rate is at 240～320 ℃ of overaging 180～300s.
Japanese patent laid-open 7～197183 discloses a kind of ultrahigh-strength steel plates and method of manufacture thereof of anti-hydrogen embrittlement, C:0.05～0.25%, Si≤3%; Mn:1～3%, P :≤0.1%, S≤0.01%; Al:0.025～0.1%, N≤0.008%, in addition; Among adding Cr, Mo, the W more than one, content is no more than 1%; Also add Ti≤0.2% in the steel, Nb :≤0.1%, V :≤0.1%, Zr: more than one in≤0.1%.In the above soaking of Ac3, slow cooling to 650 ℃, the speed with 50～1000 ℃/s is cooled to back overaging below 300 ℃ 1～20 minute then.This steel tensile strength can reach 980MPa.
Japanese Patent clear 63～38526 discloses good high tensile steel plate of a kind of bending property and method of manufacture thereof, C:0.1～0.2%, Si≤0.7%; Mn:1.5～2.5%, S≤0.008%, Al :≤0.1%; Ti:0.05～0.15%, or add Ca:0.005%.Through 850～950 ℃ of finish to gauges; 500～650 ℃ are batched, in annealing below 930 ℃ more than the recrystallization temperature, 3～200 ℃/s cooling; Be incubated 2～10 minutes then; 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.
Above-mentioned cold rolling ultrahigh-strength steel all utilizes the quick cooling of continuous annealing process, obtains the performance of super-high strength steel steel.Its composition characteristic is the C of employing 0.1～0.2% and 1～3% Mn.Because C, Mn content are all higher, very easily form the martensite belt of a large amount of zonal arrangements, cause the inhomogeneous of tissue and performance, big like the bending property anisotropy.As be used for roll-in, will exist bending property poor, the distortion inhomogeneous, the not first-class problem of extent of rebound, be difficult to obtain the ideal part shape.There are some inventions also need add expensive metals such as Cr, Mo, increased the cost of steel.The present invention is intended to invent a kind of cold rolling super-high strength steel that is used for roll-in, and it organizes tiny, even, has tangible banded structure hardly, when rolling formation, and the distortion uniformity, part shape is good.Simultaneously, because cold-bending property is good, condition of surface is good after the part forming shape, and it is strong to bear further deformation ability.
The composition synopsis (wt%) of table 1 the present invention and existing other invention:
The continuous table of composition synopsis (wt%) of table 2 the present invention and existing other invention:
Summary of the invention
The object of the present invention is to provide a kind of super-high strength cold rolled steel band and method of manufacture thereof that is suitable for rolling formation,, obtain to be suitable for the super high tensile cold-rolled steel plate of rolling formation through the design of reasonable component design and processes.The characteristics of this steel are that homogeneous microstructure distributes, thereby performance uniformity is good; This steel band shape tissue is slight, and therefore, cold-bending property is good, and the cold-bending property anisotropy is little.Simultaneously, the hardenability of this steel is moderate, and welding back weld strength and mother metal difference are less.In addition, the Si element is lower in the steel, and the surface quality of steel plate is better, and These characteristics makes steel of the present invention meet the requirement that automobile component are made in roll-in.
For achieving the above object, technical scheme of the present invention is:
A kind of super-high strength cold rolled steel band that is suitable for rolling formation, its composition weight percent is: C:0.12～0.18wt%, Si:0.1～0.4wt%, Mn:0.4～0.9wt%, B:0.001～0.003%, P :≤0.015wt%, S :≤0.004wt%, N:0.003～0.008wt%, Ti:0.02～0.06%, Al:0.015～0.045wt%, Ca:0.002～0.006%, all the other are Fe and inevitable impurity.
Preferably, the composition of steel weight percent is: C:0.13～0.17wt%, Si:0.2～0.4wt%, Mn:0.5～0.8wt%, B:0.015～0.003%, P :≤0.010wt%, S :≤0.003wt%, N:0.004～0.006wt%, Ti:0.025～0.05%, Al:0.02～0.04wt%, Ca:0.0025～0.0055%, all the other are Fe and inevitable impurity.
In the composition design of steel of the present invention:
C: improve martensitic intensity, influence martensitic content, very big to intensity effect.The higher carbon content of special design is to guarantee when manganese content is low the intensity that still can obtain to require.Carbon content is too high unfavorable to weldableness, therefore, selects carbon content between 0.12～0.18wt%.
Si: in steel, play the effect that improves unit elongation.Si is also very big to the tissue influence of steel.Si forms sull at surface enrichment easily.The span of control of Si is 0.1～0.4%, if be lower than 0.1%, the undercapacity of steel if be higher than 0.4%, influences surface quality easily.
Mn: can improve the hardening capacity of steel, effectively improve the intensity of steel.Mn is segregation in steel, in course of hot rolling, is rolled into the Mn enrichment region that becomes band and distribute easily, forms banded structure, is unfavorable for homogeneity of structure.Therefore, the phase transformation strengthening steel grade that Mn content is high forms in the line of segragation of Mn with the banded tissue of the martensite of high firmness usually, and is totally unfavorable to homogeneity of structure.For fear of this ill effect of Mn, the content of choosing Mn is 0.4～0.9%, and Mn has certain contribution to the hardening capacity of steel in this scope, is unlikely to form tangible banded structure again.
B: can improve the hardening capacity of steel, effectively improve the intensity of steel; Under the insufficient situation of Mn, add B0.001～0.003%, be lower than 0.001% B, insufficient strength is higher than 0.003% B, and the hardenability of steel is significantly improved, and possibly cause welding back intensity and improve too much.B is an interstitial element, and diffusion is very fast, and can improve hardenability has and be unlikely to cause macrosegregation.
The combination of above C, Mn, B is to guarantee that steel of the present invention had both had enough intensity, and the key of uniform tissue (do not have continuous band-shaped distribution martensite) and uniform performance is arranged again simultaneously.
P: in steel impurity element, 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, can separate out oarse-grained TiN with the Ti reaction, hydrogen caused the delay cracking have some improvement, be 0.003～0.006% so set the scope of Ti, to guarantee a certain amount of TiN.
Ti:0.025～0.05% plays the effect of fixed nitrogen element and crystal grain thinning.
A kind of method of manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation of the present invention comprises the steps:
1) smelts
The composition of steel weight percent is: C:0.12～0.18wt%, Si:0.1～0.4wt%, Mn:0.4～0.9wt%, B:0.001～0.003%, P :≤0.015wt%, S :≤0.004wt%, N:0.003～0.008wt%, Ti:0.02～0.06%, Al:0.015～0.045wt%, Ca:0.002～0.006%, all the other are Fe and inevitable impurity;
Adopt converter to add refining, take off S deeply, S is controlled at below 0.004%, reduce MnS and be mingled with;
2) continuous casting becomes base
0.9～1.4 meter/minute of continuous casting pulling rate helps inclusion floating and reduces segregation;
3) hot rolling
Heating temperature: be higher than 1200 ℃, hot-rolled temperature: more than the Ar3, roll back cooling fast, 20～70 ℃/s of speed of cooling, 500～640 ℃ of coiling temperatures;
4) cold rolling
40～65% drafts;
5) annealing
830～880 ℃ of annealing holding temperatures, insulation 40～200s adopts higher annealing holding temperature, to help the abundant diffusion and the grain growing of element, alleviates elements segregation; 10～20 ℃/s is cooled between 700～750 ℃, is cooled to below 200 ℃ to be not less than the shrend of 500 ℃/s speed, and is behind 200～300 ℃ of tempering 100～400s, smooth through 0～0.4% again; Adopt one section higher speed of cooling, fully distribute, cause the formation again of segregation to avoid element.
Preferably, step 1) is taken off S deeply, and S is controlled at below 0.003%.
Step 2) the continuous casting pulling rate is 1～1.3 meter/minute.
Step 3) hot rolling, Heating temperature be more than 1220 ℃, 30～60 ℃/s of speed of cooling, 520～620 ℃ of coiling temperatures.
Step 4) is cold rolling, 40～60% drafts.
Step 5) annealing, 840～870 ℃ of insulations are cooled between 710～740 ℃ with 10～20 ℃/s cooling rate, are cooled to below 200 ℃ with the above speed shrend of 500 ℃/s again, and are behind 220～280 ℃ of tempering 200～300s, smooth through 0.1～0.3% again.
Roll-in is that performance is even and cold-bending property good to the requirement of steel plate.When rolling formation, uniform performance can guarantee the consistence in roll-in cross section, helps obtaining the ideal part shape.The resistance continuous welding is generally adopted in the welding of roll-in process, and is comparatively loose to the requirement of carbon equivalent, but the hardenability of steel plate is had certain requirement, and steel plate non-hardenable property is too high, in order to avoid weld strength is too high, becomes fragile easily and when following process, ftractures.
The characteristics that draw point of the present invention is had relatively high expectations for cold-bending property with ultrahigh-strength steel to rolling formation, the composition design and processes design through suitable can obtain higher cold-bending property.Concrete measure is, adopts higher carbon carbon content scope, and purpose is to reduce the content of Mn.In the phase transformation strengthening steel, Mn content height very easily causes segregation, finally forms banded structure, and tissue inhomogeneous causes the inhomogeneous of performance, and be unfavorable to rolling formation.Adopt higher carbon content and lower Mn content collocation, because Mn content is very low, the segregation in the steel is slight, helps obtaining uniform tissue, has guaranteed the homogeneity of mechanical property.The deficiency of the hardenability that reduction causes for Mn remedies through adding a small amount of B.B is an interstitial element, and diffusion ratio is very fast, even segregation takes place, also is easy to improve through follow-up thermal treatment, can not cause the banded structure that is difficult to eliminate.The design of higher carbon, low manganese and trace B can guarantee the existing enough intensity of steel, and homogeneous microstructure, performance are even, satisfy the requirement of rolling formation to the steel plate characteristic.The homogeneity of tissue is bigger to the clod wash anisotropy influence of steel plate, therefore, obtains uniform tissue, can obtain the lower anisotropy of cold-bending property.In addition, select lower Si content, help reducing defectives such as surface of steel plate red rust.Aspect smelting, control lower sulphur content, be mingled with the MnS that reduces in the steel, add shape and the distribution of Ca simultaneously to improve inclusion.Hot rolling technology adopts conventional finishing temperature and coiling temperature; During annealing; In order to guarantee the steel plate homogeneous microstructure, alleviate banded structure, employing must conventional higher annealing holding temperature (Ac3+50 ℃～150 ℃); To guarantee that all even of austenite crystal gives the condition that alloying element spreads as far as possible, form thereby alleviate banded structure.Soaking is cooled to 700～750 ℃ with 10～20 ℃/s after accomplishing.The more conventional two-part refrigerative of this section cooling rate cooling rate is high, to restrain elemental diffusion as far as possible, helps eliminating segregation.Then with water-cooling pattern at a high speed but to below 200 ℃, effectively obtain the martensitic stucture of even refinement, carry out low-temperaturetempering and smooth on a small quantity at last.The finished product carbon equivalent is low, surface quality is high, has good partial plastic forming ability simultaneously, and balancing performance property is good.
The present invention compared with prior art has following advantage and positively effect:
In the tissue of steel of the present invention, martensite is evenly distributed, and banded structure is slight, and The amount of inclusions is few and be evenly distributed; Produce the plow-steel more than the intensity 980MPa according to the present invention, cold-bending property is good, and anisotropy is low, and mechanical property has good uniformity; Be suitable for the requirement of rolling formation.Simultaneously, the hardenability of steel is moderate, and the hardness of welding zone, welding back rises few with respect to mother metal, part overall performance good uniformity, effectively control cracking.In a word, steel of the present invention can adapt to the requirement that automobile component are made in roll-in well.
Embodiment
Below in conjunction with embodiment the present invention is further specified.
The chemical ingredients of embodiment of the invention steel is referring to table 3.The process condition of steel of the present invention is as shown in table 4, steel of the present invention through smelting, hot rolling, cold rolling, annealing and smooth after the intensity that obtains as shown in table 5.Can find out from table 5, can produce the plow-steel more than the intensity 980MPa according to the present invention, compare with the high-strength steel (comparative example 1) of commercially available equality strength, cold-bending property is good, and the bending property anisotropy is low, can satisfy the requirement of rolling formation preferably.Be suitable for the manufacturing of HS vehicle body component.Aspect banded structure control, the control of cold-bending property anisotropy and cost, steel of the present invention is different from existing invention and is superior to original invention in composition design and the final each side such as result that obtain.
Table 3 chemical ingredients (wt%)
The critical process process parameter of table 4 invention steel and mechanical property contrast
The performance of table 5 invention steel
See from the bending property contrast of the different directions of table 5; The present invention can the bending crestal line be parallel to roll to the time; Obtain littler bending radius; With the bending crestal line perpendicular to roll to the time the bending radius gap less, not only bending property is superior to Comparative Examples, and also more excellent aspect the anisotropy of bending property.
Claims (9)
1. super-high strength cold rolled steel band that is suitable for rolling formation, its composition weight percent is:
C：0.12～0.18wt％
Si：0.1～0.4wt％
Mn：0.4～0.9wt％
B：0.001～0.003％
P：≤0.015wt％
S：≤0.004wt％
N：0.003～0.008wt％
Ti：0.02～0.06％
Al：0.015～0.045wt％
Ca：0.002～0.006％
All the other are Fe and inevitable impurity.
2. the super-high strength cold rolled steel band that is suitable for rolling formation as claimed in claim 1; It is characterized in that its composition weight percent is: C:0.13～0.17wt%, Si:0.2～0.4wt%, Mn:0.5～0.8wt%, B:0.015～0.003%, P :≤0.010wt%, S :≤0.003wt%, N:0.004～0.006wt%, Ti:0.025～0.05%, Al:0.02～0.04wt%, Ca:0.0025～0.0055%, all the other are Fe and inevitable impurity.
3. a method of manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation comprises the steps:
1) smelts
The composition of steel weight percent is: C:0.12～0.18wt%, Si:0.1～0.4wt%, Mn:0.4～0.9wt%, B:0.001～0.003%, P :≤0.015wt%, S :≤0.004wt%, N:0.003～0.008wt%, Ti:0.02～0.06%, Al:0.015～0.045wt%, Ca:0.002～0.006%, all the other are Fe and inevitable impurity;
Adopt converter to add refining, take off S deeply, S is controlled at below 0.004%, reduce MnS and be mingled with;
2) continuous casting becomes base
0.9～1.4 meter/minute of continuous casting pulling rate helps inclusion floating and reduces segregation;
3) hot rolling
Heating temperature: be higher than 1200 ℃, hot-rolled temperature: more than the Ar3, roll back cooling fast, 20～70 ℃/s of speed of cooling, 500～640 ℃ of coiling temperatures;
4) cold rolling
40～65% drafts;
5) annealing
830～880 ℃ of annealing holding temperatures, insulation 40～200s; Be cooled between 700～750 ℃ with 10～20 ℃/s of speed of cooling, be cooled to below 200 ℃ to be not less than the shrend of 500 ℃/s speed, behind 200～300 ℃ of tempering 100～400s, smooth through 0～0.4% again.
4. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3; It is characterized in that; Step 1) is smelted, and the composition of steel weight percent is: C:0.13～0.17wt%, Si:0.2～0.4wt%, Mn:0.5～0.8wt%, B:0.015～0.003%, P :≤0.010wt%, S :≤0.003wt%, N:0.004～0.006wt%, Ti:0.025～0.05%, Al:0.02～0.04wt%, Ca:0.0025～0.0055%, all the other are Fe and inevitable impurity.
5. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3 is characterized in that step 1) is taken off S deeply, and S is controlled at below 0.003%.
6. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3 is characterized in that step 2) 1～1.3 meter/minute of continuous casting pulling rate.
7. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3 is characterized in that, the step 3) hot rolling, and Heating temperature is more than 1220 ℃, 30～60 ℃/s of speed of cooling, 520～620 ℃ of coiling temperatures.
8. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3 is characterized in that step 4) is cold rolling, 40～60% drafts.
9. the method for manufacture that is suitable for the super-high strength cold rolled steel band of rolling formation as claimed in claim 3; It is characterized in that step 5) annealing, 840～870 ℃ of insulations; Be cooled between 710～740 ℃ with 10～20 ℃/s cooling rate; Be cooled to below 200 ℃ with the above speed shrend of 500 ℃/s again, behind 220～280 ℃ of tempering 200～300s, 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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| CN102864377A (en) * | 2012-09-10 | 2013-01-09 | 山西太钢不锈钢股份有限公司 | Hot rolled strip steel and manufacturing method thereof |
| CN102943206A (en) * | 2012-12-09 | 2013-02-27 | 新余钢铁集团有限公司 | High-strength hot rolled steel strip with improved zonal structure by manganese reduction and manufacturing method thereof |
| CN107354376A (en) * | 2017-05-27 | 2017-11-17 | 唐山钢铁集团有限责任公司 | Roll-forming yield strength 550MPa levels cold-rolled steel sheet and production method |
| CN108977726A (en) * | 2017-05-31 | 2018-12-11 | 宝山钢铁股份有限公司 | A kind of the martensite super-high strength cold rolled steel band and its manufacturing method of anti-delayed fracture |
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| JP2004292939A (en) * | 2003-03-28 | 2004-10-21 | Nisshin Steel Co Ltd | Cold rolled steel sheet having excellent punching workability |
| CN101871078A (en) * | 2009-04-24 | 2010-10-27 | 宝山钢铁股份有限公司 | Super-high strength cold rolled steel and manufacturing method thereof |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2004292939A (en) * | 2003-03-28 | 2004-10-21 | Nisshin Steel Co Ltd | Cold rolled steel sheet having excellent punching workability |
| CN101871078A (en) * | 2009-04-24 | 2010-10-27 | 宝山钢铁股份有限公司 | Super-high strength cold rolled steel and manufacturing method thereof |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102864377A (en) * | 2012-09-10 | 2013-01-09 | 山西太钢不锈钢股份有限公司 | Hot rolled strip steel and manufacturing method thereof |
| CN102864377B (en) * | 2012-09-10 | 2015-05-20 | 山西太钢不锈钢股份有限公司 | Hot rolled strip steel and manufacturing method thereof |
| CN102943206A (en) * | 2012-12-09 | 2013-02-27 | 新余钢铁集团有限公司 | High-strength hot rolled steel strip with improved zonal structure by manganese reduction and manufacturing method thereof |
| CN102943206B (en) * | 2012-12-09 | 2014-10-22 | 新余钢铁集团有限公司 | High-strength hot rolled steel strip with improved zonal structure by manganese reduction and manufacturing method thereof |
| CN107354376A (en) * | 2017-05-27 | 2017-11-17 | 唐山钢铁集团有限责任公司 | Roll-forming yield strength 550MPa levels cold-rolled steel sheet and production method |
| CN107354376B (en) * | 2017-05-27 | 2019-05-28 | 唐山钢铁集团有限责任公司 | Roll-forming 550MPa grades of cold-rolled steel sheets of yield strength and production method |
| CN108977726A (en) * | 2017-05-31 | 2018-12-11 | 宝山钢铁股份有限公司 | A kind of the martensite super-high strength cold rolled steel band and its manufacturing method of anti-delayed fracture |
| CN108977726B (en) * | 2017-05-31 | 2020-07-28 | 宝山钢铁股份有限公司 | Delayed-cracking-resistant martensite ultrahigh-strength cold-rolled steel strip and manufacturing method thereof |
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| CN102534373B (en) | 2014-07-23 |
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