CN104388820A - High-strength hot-rolled strip steel having favorable stretch-flangeability and production method thereof - Google Patents
High-strength hot-rolled strip steel having favorable stretch-flangeability and production method thereof Download PDFInfo
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- CN104388820A CN104388820A CN201410651313.3A CN201410651313A CN104388820A CN 104388820 A CN104388820 A CN 104388820A CN 201410651313 A CN201410651313 A CN 201410651313A CN 104388820 A CN104388820 A CN 104388820A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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Abstract
The invention relates to high-strength hot-rolled strip steel having favorable stretch-flangeability, which comprises the following components in percentage by weight: 0.03%-0.05% of C, 0.01%-0.50% of Si, 0.40%-1.00% of Mn, no more than 0.015% of P, no more than 0.005% of S, no more than 0.006% of N, 0.030-0.10% of Als, 0.10-0.25% of Ti and 0.0010-0.0035% B. The production method comprises the following CSP production steps: smelting and continuously casting to obtain slabs; heating the continuous casting slabs; rolling; performing laminar cooling; coiling; naturally cooling to room temperature; and finishing. According to the invention, the tensile strength is no less than 780 MPa, the metallurgical structure is 95-100% ferrite, the elongation percentage is no less than 15%, and the hole expansion rate is no less than 80%; a proper amount of cheap Ti microalloy is used to reduce use of expensive alloys of Mo, Ni, Cu and the like, thus lowering the manufacturing cost of steel; and thin slabs are used instead of thick slabs, and hot rolling is adopted instead of cold rolling, thus further lowering the manufacturing cost of steel for automobiles. The production of molding-complicated automobile components and parts can be satisfied, the existing equipment can be utilized without adopting ultra-fast cooling equipment or the like, the production efficiency is high, and less investment is needed.
Description
Technical field
The present invention relates to a kind of automobile steel and production method, belong to one particularly and have the high-strength hot-rolled band steel of good stretch flangeability and production method, being specially adapted to produce thickness is 1.2 ~ 4.0mm hot rolled strip.
Background technology
In recent years, along with the propelling of energy-saving and emission-reduction technology of vehicles, automotive light weight technology becomes a kind of development trend, more and more urgent to the demand of the high-strength automobile steel of Thin Specs thus.When manufacturing for comparatively complicated parts such as wheel spokes, except needing higher intensity, simultaneously more and more higher to the requirement of steel stretch flangeability, but the stretch flangeability of steel generally increases along with steel strength and reduces, therefore there is high strength and the excellent High Strength Steel Plate of Extending flange Perfor is badly in need of exploitation simultaneously.The stretch flangeability of steel is relevant to the tissue in steel, usually controls to be organized as ferrite-bainite tissue in steel.
As the document that China Patent Publication No. is CN 102409245A, it discloses a kind of high Extending flange Perfor hot-rolled dual-phase steel thin plate and manufacture method thereof, its metallographic structure is ferrite+bainite structure, tensile strength >=580MPa, unit elongation >=26%, the high Extending flange Perfor hot-rolled dual-phase steel of hole expansibility >=75%, its chemical composition is, C:0.05 ~ 0.10%, Si:0.20 ~ 0.60%, Mn:1.00 ~ 1.70%, Al:0.01 ~ 0.06%, P:0.05 ~ 0.10%, Cr:0.20 ~ 0.80%, S≤0.005%, main technologic parameters is for adopting two-phase control rolling, roughing draft >=70%, finish rolling draft >=75%, finish rolling start rolling temperature 1000 ~ 1100 DEG C, finishing temperature 800 ~ 880 DEG C, section cooling takes the type of cooling of water-cooled+air cooling+water-cooled, coiling temperature 350 ~ 500 DEG C, finished product thickness 2 ~ 10mm.Also have China Patent Publication No. to be the document of CN 102918173A, it discloses a kind of stretch flangeability and the excellent high tensile steel plate of resistance to fatigue and manufacture method thereof.Which propose the manufacture method that a kind of more than tensile strength 780MPa has excellent stretch flangeability and high-fatigue strength High Strength Steel Plate concurrently, its chemical composition is C:0.05 ~ 0.15%, Si:0.20 ~ 1.20%, Mn:1.00 ~ 2.00%, Al:0.005 ~ 0.10%, P :≤0.04%, Ti:0.05 ~ 0.15%, N≤0.007%, S≤0.005%, main technologic parameters Heating temperature 1150 ~ 1350 DEG C, finishing temperature 850 ~ 950 DEG C, 30 DEG C/s is cooled to 530 DEG C, is then cooled to 300 ~ 500 DEG C with 100 DEG C/s, and batches.Tensile strength >=the 780MPa of products obtained therefrom, unit elongation >=12%, hole expansibility is greater than 60%.
Two sections of above-mentioned patent documentations, common deficiency is: because the difference of hardness existed in steel between ferrite and bainite causes more greatly steel stretch flangeability not high, especially for the high-strength stretch flangeability dual phase steel of more than 590MPa; In addition, in both steel, C content is too high, has a negative impact to stretch flangeability, and causes disadvantageous effect to the welding property of steel; Mn content too high in steel also easily causes being formed centrally Mn segregation in steel plate, has a negative impact to the stretch flangeability of steel.
Summary of the invention
The present invention is directed to prior art exist deficiency, provide one not only tensile strength >=780MPa, and metallographic structure is the ferrite of 95% ~ 100%, unit elongation >=15%, hole expansibility >=80% there is the high-strength hot-rolled band steel of good stretch flangeability and production method.
Realize the measure of above-mentioned purpose:
One has the high-strength hot-rolled band steel of good stretch flangeability, its component and weight percent content are: C:0.03% ~ 0.05%, Si:0.01% ~ 0.50%, Mn:0.40% ~ 1.00%, P :≤0.015%, S :≤0.005%, N :≤0.006%, Als:0.030 ~ 0.10%, Ti:0.10 ~ 0.25 %, B:0.0010 ~ 0.0035%, all the other are Fe and inevitable impurity; Metallographic structure is the ferrite of 95% ~ 100%, tensile strength >=780MPa, unit elongation >=15%, hole expansibility >=80%.
Preferably: the weight percent content of Mn is 0.40% ~ 0.97%.
Preferably: the weight percent content of Ti is 0.15 ~ 0.20%.
CSP line is adopted to produce a kind of method with the high-strength hot-rolled band steel of good stretch flangeability, its step:
1) smelt also continuous casting and become base, wherein: control to water steel temperature at 1531 ~ 1570 DEG C, slab thickness is at 50 ~ 90mm;
2) strand is heated: control strand charging temperature at 850 ~ 1050 DEG C, tapping temperature at 1100 DEG C ~ 1250 DEG C, strand time inside furnace 10 ~ 40min;
3) be rolled: control finishing temperature at 880 ~ 940 DEG C; Carry out 7 passes altogether, rolling first and second passage draft separately 50% ~ 70%, the 6th and the 7th passage separately rolling draft 5% ~ 20%;
4) segmentation laminar flow is cooled to coiling temperature, and controls leading portion rate of cooling at 50 ~ 200 DEG C/s, and back segment rate of cooling is at 3.0 ~ 30 DEG C/s;
5) batch, oiler temperature control is at 550 DEG C ~ 650 DEG C;
6) room temperature is naturally cooled to;
7) finishing is carried out.
Preferably: it is characterized in that: finishing temperature 910 ~ 940 DEG C.
Preferably: back segment rate of cooling is at 10 ~ 30 DEG C/s.
The mechanism of each component and main technique and effect in the present invention
C: carbon is main in steel plays solution strengthening effect, and forms TiC fine particle with the Ti in steel, plays the effect of solution strengthening and precipitation strength, effectively improves intensity and the fatigue performance of steel.Carbon content lower than 0.03 time, the amount separating out TiC is less, strengthening effect is not obvious, carbon content higher than 0.05 time, in steel, ferrite content reduces, and perlite increases, and reduces plasticity and the stretch flangeability of steel, the too high welding property that also can affect steel of carbon content in addition, the C content therefore in steel is chosen as 0.030% ~ 0.050%.
Mn:Mn plays solution strengthening effect in steel, and content is too low, and strengthening effect is too little, and therefore minimum Mn content is that 0.10%, Mn too high levels easily forms segregation at strip mid-depth, reduces product stretch flangeability, and therefore most high Mn content is 1.00%.
Si:Si plays solution strengthening effect in steel, and is conducive to improving the toughness of steel, and Si content is too low, and toughness improves DeGrain, and therefore minimum Si content is 0.01%, but Si too high levels, easily causes surface imperfection, and therefore most high Si content is 0.50%.
P:P is the impurity element in steel, is easy at Grain Boundary Segregation, affects the toughness of product, and therefore its content is more low better.According to working control level, should control below 0.015%, preferably control below 0.010%.
S:S is the impurity element in steel, easily produces segregation at crystal boundary, and forms the FeS of low melting point with the Fe in steel, reduces the toughness of steel, fully should remove, should control 0.005%, preferably control below 0.002% during steel-making.
N:N is the impurity element in steel, reduces the toughness of steel, and Al, Ti form AlN and TiN, too high levels easily and in steel, AlN and TiN that easily formation is thick, therefore reduces its content as far as possible, should control below 0.006%, preferably control below 0.003%.
Al:Al plays solution strengthening effect in steel, and Al plays the effect of deoxidation in steelmaking process, therefore in steel, the minimum content of Al is 0.030%, but the N of Al too high levels easily and in steel forms thick AlN particle, cause the toughness of steel to reduce, therefore the most high-content of Al is 0.10%.
Ti:Ti plays solution strengthening effect in steel, and the C in Ti and steel forms nano TiC on ferrite matrix, improves intensity and the fatigue resistance of ferrite matrix.Ti can also form TiN with the N in steel, organizes grain growth during heat steel.Therefore the minimum content of Ti is 0.10%.But Ti too high levels easily forms thick TiC particle, and thick TiN, thus reduce the toughness of steel, and Ti too high levels increases cost.Preferably Ti content is 0.15 ~ 0.20%.
B:B plays solution strengthening effect in steel, improves the intensity of steel, and B can play the effect stoping TiC to grow up, and therefore the minimum content of B is 0.0010%, but B too high levels can reduce ferritic toughness, and therefore most high-content is 0.0030%.
In the present invention, why control the first and second passages draft separately 50% ~ 70%, be take to depress greatly rolling due to high temperature section to be conducive to the original continuous casting billet structure of refinement, and make continuous casting billet structure homogenizing.Owing to limiting by capacity of equipment, therefore maximum depression rate is 70%.
Control the 6th and the 7th passage separately rolling draft 5% ~ 20%, be the refinement being unfavorable for tissue because draft is too little, and draft is unfavorable for too greatly the control of Thin Specs plate shape.
Carrying out in section cooling, why control leading portion rate of cooling at 50 ~ 200 DEG C/s, back segment rate of cooling 3.0 ~ 30 DEG C/s be due to leading portion speed of cooling larger time be conducive to obtaining tiny ferritic structure, suppress the precipitation of thick TiC particle, promote the precipitation of the tiny TiC of nano level, improve intensity and the plasticity of steel, when speed of cooling is too large, easily there is bainite and martensite tissue in steel, reduce the plasticity of steel.
The present invention compared with prior art, not only tensile strength >=780MPa, and metallographic structure is the ferrite of 95% ~ 100%, unit elongation >=15%, hole expansibility >=80%; And adopt appropriate cheap Ti microalloy, decrease the use of expensive alloys Mo, Ni, Cu etc., reduce the manufacturing cost of steel, and realize with Bao Daihou, with hot Dai Leng, reduce the manufacturing cost of automobile steel material further.It can meet the production of the automobile component of shaping complexity, and the present invention utilizes existing installation, and without the need to adopting ultrafast cold equipment such as grade, production efficiency is high, less investment.
Embodiment
Below the present invention is described in detail:
Table 1 is the value list of various embodiments of the present invention and comparative example;
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example;
Table 3 is various embodiments of the present invention and the list of comparative example Performance Detection situation.
Various embodiments of the present invention are produced according to following steps:
1) smelt also continuous casting and become base, wherein: control to water steel temperature at 1531 ~ 1570 DEG C, slab thickness is at 50 ~ 90mm;
2) strand is heated: control strand charging temperature at 850 ~ 1050 DEG C, tapping temperature at 1100 DEG C ~ 1250 DEG C, strand time inside furnace 10 ~ 40min;
3) be rolled: control finishing temperature at 880 ~ 940 DEG C; Carry out 7 passes altogether, rolling first and second passage draft separately 50% ~ 70%, the 6th and the 7th passage separately rolling draft 5% ~ 20%;
4) segmentation laminar flow is cooled to coiling temperature, and controls leading portion rate of cooling at 50 ~ 200 DEG C/s, and back segment rate of cooling is at 3.0 ~ 30 DEG C/s;
5) batch, oiler temperature control is at 550 DEG C ~ 650 DEG C;
6) room temperature is naturally cooled to;
7) finishing is carried out.
The chemical composition list (wt%) of table 1 embodiment of the present invention and comparative example
Table 2 various embodiments of the present invention and comparative example technique significant parameter control list ()
The main technologic parameters list (two) of table 2 various embodiments of the present invention and comparative example
Table 3 is various embodiments of the present invention and the list of comparative example Performance Detection situation
| Embodiment | Ferrite fraction % | Tensile strength MPa | Unit elongation % | Hole expansibility/% |
| 1 | 100 | 830 | 25 | 100 |
| 2 | 99 | 840 | 21 | 95 |
| 3 | 100 | 810 | 18 | 110 |
| 4 | 98 | 832 | 20 | 96 |
| 5 | 97 | 810 | 20 | 86 |
| 6 | 99 | 790 | 21 | 98 |
| 7 | 97 | 806 | 18 | 100 |
| 8 | 100 | 835 | 19 | 105 |
| 9 | 100 | 828 | 23 | 110 |
| 10 | 96 | 835 | 24 | 90 |
| 11 | 95 | 850 | 18 | 87 |
| 12 | 99 | 860 | 18 | 85 |
| Comparative example 1 | 80 | 580 | 15 | 70 |
| Comparative example 2 | 90 | 630 | 25 | 55 |
As can be seen from Table 3, ferritic structure of the present invention is more than 95%, and tensile strength is at more than 780MPa, and unit elongation is more than 15%, and hole expansibility is more than 80%.
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (6)
1. one kind has the high-strength hot-rolled band steel of good stretch flangeability, its component and weight percent content are: C:0.030% ~ 0.050%, Si:0.01% ~ 0.50%, Mn:0.40% ~ 1.00%, P :≤0.015%, S :≤0.005%, N :≤0.006%, Als:0.030 ~ 0.10%, Ti:0.10 ~ 0.25 %, B:0.0010 ~ 0.0035%, all the other are Fe and inevitable impurity; Metallographic structure is the ferrite of 95% ~ 100%, tensile strength >=780MPa, unit elongation >=15%, hole expansibility >=80%.
2. one as claimed in claim 1 has the high-strength hot-rolled band steel of good stretch flangeability, it is characterized in that: the weight percent content of Mn is 0.40% ~ 0.97%.
3. one as claimed in claim 1 has the high-strength hot-rolled band steel of good stretch flangeability, it is characterized in that: the weight percent content of Ti is 0.15 ~ 0.20%.
4. adopt CSP line to produce a kind of method with the high-strength hot-rolled band steel of good stretch flangeability, its step:
1) smelt also continuous casting and become base, wherein: control to water steel temperature at 1531 ~ 1570 DEG C, slab thickness is at 50 ~ 90mm;
2) strand is heated: control strand charging temperature at 850 ~ 1050 DEG C, tapping temperature at 1100 DEG C ~ 1250 DEG C, strand time inside furnace 10 ~ 40min;
3) be rolled: control finishing temperature at 880 ~ 940 DEG C; Carry out 7 passes altogether, rolling first and second passage draft separately 50% ~ 70%, the 6th and the 7th passage separately rolling draft 5% ~ 20%;
4) segmentation laminar flow is cooled to coiling temperature, and controls leading portion rate of cooling at 50 ~ 200 DEG C/s, and back segment rate of cooling is at 3.0 ~ 30 DEG C/s;
5) batch, oiler temperature control is at 550 DEG C ~ 650 DEG C;
6) room temperature is naturally cooled to;
7) finishing is carried out.
5. a kind of method with the high-strength hot-rolled band steel of good stretch flangeability of production as claimed in claim 4, is characterized in that: finishing temperature 910 ~ 940 DEG C.
6. a kind of method with the high-strength hot-rolled band steel of good stretch flangeability of production as claimed in claim 4, is characterized in that: back segment rate of cooling is at 10 ~ 30 DEG C/s.
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105154769A (en) * | 2015-09-18 | 2015-12-16 | 宝山钢铁股份有限公司 | 780 MPa hot-rolled high-strength steel with high hole expansion ratio and manufacturing method thereof |
| CN107815597A (en) * | 2017-11-17 | 2018-03-20 | 武汉钢铁有限公司 | A kind of high-intensity rim steel and production method with good flanging forming |
| CN107858598A (en) * | 2017-11-17 | 2018-03-30 | 武汉钢铁有限公司 | A kind of tensile strength is 490MPa level wheel rim steel and production method |
| CN107937815A (en) * | 2017-11-17 | 2018-04-20 | 武汉钢铁有限公司 | A kind of width cold-bending property good think gauge spoke steel and production method |
| CN109202028A (en) * | 2018-09-10 | 2019-01-15 | 武汉科技大学 | A kind of high stretch flange formability steel plate and preparation method thereof |
| CN109763065A (en) * | 2019-01-04 | 2019-05-17 | 武汉钢铁有限公司 | A kind of template pulling-on piece hot-rolled steel and production method |
| CN109778063A (en) * | 2019-01-04 | 2019-05-21 | 武汉钢铁有限公司 | A kind of cold rolled die pulling-on piece steel and method using CSP production |
| CN111286673A (en) * | 2020-03-27 | 2020-06-16 | 武汉钢铁有限公司 | High-formability boron-containing steel with tensile strength of more than or equal to 320MPa and production method thereof |
| WO2021052431A1 (en) * | 2019-09-19 | 2021-03-25 | 宝山钢铁股份有限公司 | Thin-strip continuous casting high hole expansion steel and manufacturing method therefor |
| CN113106219A (en) * | 2021-04-13 | 2021-07-13 | 攀钢集团西昌钢钒有限公司 | Method for improving thickness precision of ultrahigh-strength cold-rolled dual-phase steel |
| CN114086079A (en) * | 2021-11-04 | 2022-02-25 | 武汉钢铁有限公司 | 600 MPa-grade thick-specification automobile steel and production method thereof |
| CN115491589A (en) * | 2022-08-18 | 2022-12-20 | 武汉钢铁有限公司 | 800 MPa-grade CSP short-process hot-rolled high-strength structural steel and manufacturing method thereof |
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| CN105154769A (en) * | 2015-09-18 | 2015-12-16 | 宝山钢铁股份有限公司 | 780 MPa hot-rolled high-strength steel with high hole expansion ratio and manufacturing method thereof |
| CN105154769B (en) * | 2015-09-18 | 2017-06-23 | 宝山钢铁股份有限公司 | A kind of 780MPa grades of hot-rolled high-strength reaming steel high and its manufacture method |
| CN107815597A (en) * | 2017-11-17 | 2018-03-20 | 武汉钢铁有限公司 | A kind of high-intensity rim steel and production method with good flanging forming |
| CN107858598A (en) * | 2017-11-17 | 2018-03-30 | 武汉钢铁有限公司 | A kind of tensile strength is 490MPa level wheel rim steel and production method |
| CN107937815A (en) * | 2017-11-17 | 2018-04-20 | 武汉钢铁有限公司 | A kind of width cold-bending property good think gauge spoke steel and production method |
| CN109202028B (en) * | 2018-09-10 | 2020-03-10 | 武汉科技大学 | High-elongation flange steel plate and preparation method thereof |
| CN109202028A (en) * | 2018-09-10 | 2019-01-15 | 武汉科技大学 | A kind of high stretch flange formability steel plate and preparation method thereof |
| CN109763065A (en) * | 2019-01-04 | 2019-05-17 | 武汉钢铁有限公司 | A kind of template pulling-on piece hot-rolled steel and production method |
| CN109778063A (en) * | 2019-01-04 | 2019-05-21 | 武汉钢铁有限公司 | A kind of cold rolled die pulling-on piece steel and method using CSP production |
| WO2021052431A1 (en) * | 2019-09-19 | 2021-03-25 | 宝山钢铁股份有限公司 | Thin-strip continuous casting high hole expansion steel and manufacturing method therefor |
| JP2022549235A (en) * | 2019-09-19 | 2022-11-24 | 宝山鋼鉄股▲分▼有限公司 | Thin strip continuous cast high hole expanded steel and its manufacturing method |
| CN111286673A (en) * | 2020-03-27 | 2020-06-16 | 武汉钢铁有限公司 | High-formability boron-containing steel with tensile strength of more than or equal to 320MPa and production method thereof |
| CN111286673B (en) * | 2020-03-27 | 2021-05-25 | 武汉钢铁有限公司 | High-formability boron-containing steel with tensile strength of more than or equal to 320MPa and production method thereof |
| CN113106219A (en) * | 2021-04-13 | 2021-07-13 | 攀钢集团西昌钢钒有限公司 | Method for improving thickness precision of ultrahigh-strength cold-rolled dual-phase steel |
| CN113106219B (en) * | 2021-04-13 | 2022-05-24 | 攀钢集团西昌钢钒有限公司 | Method for improving thickness precision of ultrahigh-strength cold-rolled dual-phase steel |
| CN114086079A (en) * | 2021-11-04 | 2022-02-25 | 武汉钢铁有限公司 | 600 MPa-grade thick-specification automobile steel and production method thereof |
| CN115491589A (en) * | 2022-08-18 | 2022-12-20 | 武汉钢铁有限公司 | 800 MPa-grade CSP short-process hot-rolled high-strength structural steel and manufacturing method thereof |
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Application publication date: 20150304 |