CN102732786A - Economical-type 540MPa-grade ferrite bainite hot-rolled dual-phase steel and production method thereof - Google Patents
Economical-type 540MPa-grade ferrite bainite hot-rolled dual-phase steel and production method thereof Download PDFInfo
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- CN102732786A CN102732786A CN2012102037853A CN201210203785A CN102732786A CN 102732786 A CN102732786 A CN 102732786A CN 2012102037853 A CN2012102037853 A CN 2012102037853A CN 201210203785 A CN201210203785 A CN 201210203785A CN 102732786 A CN102732786 A CN 102732786A
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Abstract
The invention relates to an economical-type 540MPa-grade ferrite bainite hot-rolled dual-phase steel and a production method thereof. The steel comprises the components of, by mass: no more than 0.20% of C, no more than 1.80% of Si, no more than 2.00% of Mn, no more than 0.050% of P, no more than 0.015% of S, no more than 0.10% of Nb, and balance of Fe. The steel is produced through the steps of: molten iron pretreatment, converter smelting, alloy fine-tuning station processing, LF refining, continuous casting, and hot continuous rolling.
Description
Technical field
The present invention relates to hot continuous rolling process and produce advanced high-strength steel field, mainly be applicable to 540MPa level hot-rolled ferrite-bainite dual-phase steel, also can use the production of other HSLAs and similar advanced high-strength steel.
Background technology
Dual phase steel is used the matrix material notion and is carried out alloy designs.Its ultimate principle is to utilize a mixture, relies on this mixture to make the advantage of each phase obtain performance as far as possible, and the shortcoming that makes them simultaneously is owing to the existence of other phase reduces or eliminates.When dynamic deformation, dual phase steel is compared with other steel grades of same static yield strength, has high energy absorption.Utilize this performance of dual phase steel, can be applied to trolley part.As be widely used in the manufacturing of car body and chassis punch, can improve component strength significantly, alleviate the member own wt.
Ferritic+martensite dual-phase steel had been widely used in automobile industry already, but at present also less to the research and development of dual phase steel of ferrite and bainite.Research shows, and as second mutually the martensitic phase ratio, bainite structure all has favorable influence to flange tensile property and fracture toughness property, has high hole expansibility-strength matching.Therefore, dual phase steel of ferrite and bainite is applicable to the especially flange tensile property automobile support component of having relatively high expectations of thicker and plasticity, like automotive wheel.
Hot-rolled dual-phase steel is owing to saved the additional heat treatment operation, and its weldableness and fatigability are also good than the thermal treatment dual phase steel, and cost is low, industrial scale is bigger.Its difficult point is how accurately to control the biphase ratio and obtain consistent performance on steel total length and the width along being with.Because bainite phase transition window is narrow, phase transformation control difficulty is big.In the board rolling production process, realize accurate control to phase transformation, be the key of producing dual phase steel of ferrite and bainite.
At present, both at home and abroad for the working method of dual phase steel of ferrite and bainite, the basic transformation of adopting noble metal elements such as adding chromium, molybdenum with the control supercooled austenite combines constant speed rolling and segmentation to cool off simultaneously and controls the transformation amount of rolling back ferritic and bainite.The interpolation of noble metal can significantly cause cost to rise; Segmentation cooling meeting significantly reduces production efficiency after adopting constant speed rolling simultaneously and rolling.
Summary of the invention
In order to guarantee under the product quality premise; Economize on resources as much as possible and enhance productivity; Thereby reduction manufacturing cost; The present invention has developed a kind of noble metal elemental chromium, molybdenum of not adding, and only adopts the trace niobium alloying, and cools off the method for producing dual phase steel of ferrite and bainite continuously through rolling the back.The 540MPa level hot-rolled ferrite-bainite dual-phase steel of producing has good intensity-plasticity-hole expansibility coupling, can satisfy the especially needs of the automobile support component of flange tensile property requirement of higher weldableness, fatigability, plasticity preferably.
Concrete technical scheme is following:
A kind of economical 540MPa level ferrite-bainite hot-rolled dual-phase steel, according to mass percent, contain C :≤0.20%, Si :≤1.80%, Mn :≤2.00%, P :≤0.050%, S :≤0.015%, Nb :≤0.10%, and surplus Fe.
Further, its ys is: 460～510MPa, and tensile strength is: 540～580MPa, unit elongation is: >=28%, hole expansibility is >=80%.
The method of manufacture of above-mentioned economical 540MPa level ferrite-bainite hot-rolled dual-phase steel, adopt following steps:
1) hot metal pretreatment;
2) converter smelting;
3) alloy fine setting station;
4) LF refining;
5) continuous casting;
6) hot continuous rolling.
Further, the chemical ingredients of the strand after step 1) is handled according to mass ratio is: C:0.06 ~ 0.10%; Si:0.05 ~ 0.15%; Mn:1.30 ~ 1.50%; P≤0.015%; S≤0.010%; Nb:0.015 ~ 0.025%.
Further, the slab thickness specification after step 1) is handled is 220mm.
Further, Heating temperature is 1150～1250 ℃ in the step 6), and finishing temperature is 800～900 ℃.
Further, also comprise the steps
7) roll the back and adopt leading portion
ContinuouslyThe type of cooling;
8) batch.
Further, coiling temperature is 400～500 ℃ in the step 8).
Further, be rolled into the thick intermediate blank of 30mm through roughing earlier before the finish to gauge.
Compare with present prior art, the present invention (1) does not add noble metal elemental chromium, molybdenum, greatly reduces the alloy usage quantity, has practiced thrift resource effectively, can reduce cost of alloy significantly; (2) adopt pair rolling and roll the postcooling control device, the production efficiency of avoiding constant speed rolling and segmentation cooling to cause descends, and can reduce rolling cost preferably; (3) through suitable technology controlling and process, realize ferrite-bainite biphase accurately control and proportioning, product has excellent intensity-plasticity-hole expansibility coupling.
Description of drawings
Fig. 1 is a 540MPa level dual phase steel of ferrite and bainite microstructure picture picture involved in the present invention
Fig. 2 is a 540MPa level dual phase steel of ferrite and bainite ream forming picture involved in the present invention
Embodiment
Describe the present invention according to accompanying drawing below, it is a kind of preferred embodiment in the numerous embodiments of the present invention.
(1) technical process of this process using is: hot metal pretreatment-converter smelting-alloy fine setting station-LF-continuous casting-hot continuous rolling;
(2) chemical Composition Control is following: C: Si≤0.20%: Mn≤1.80%: P≤2.00%: S≤0.050%: Nb≤0.015% :≤0.10%;
(3) hot continuous rolling process is: Heating temperature is 1150～1250 ℃; Finishing temperature is 800～900 ℃; Roll back cooling continuously; Coiling temperature is 400～500 ℃.
Subordinate list is mechanical property of the present invention and reaming performance data table.Table 1 is the mechanical performance data table, and table 2 is a reaming performance data table.
Table 1
| Reel number | R el?/MPa | R m?/MPa | A 50/% | Clod wash |
| H100386160 | 515 | 560 | 31.0 | Qualified |
| H100386170 | 515 | 560 | 30.5 | Qualified |
| H100386190 | 495 | 560 | 31.5 | Qualified |
| H100386200 | 505 | 550 | 32.5 | Qualified |
| H100386210 | 505 | 560 | 30.5 | Qualified |
| Technical requirements | ≥365 | ≥540 | ≥22.0 | Qualified |
Table 2
(1) strand chemical ingredients (wt%) is: C:0.06 ~ 0.10%; Si:0.05 ~ 0.15%; Mn:1.30 ~ 1.50%; P≤0.015%; S≤0.010%; Nb:0.015 ~ 0.025%;
(2) the slab thickness specification by this composition is 220mm;
(3) Heating temperature is 1200 ~ 1250 ℃;
(4) be rolled into the thick intermediate blank of 30mm through roughing;
(5) finish rolling finishing temperature is controlled to be 800 ~ 850 ℃;
(6) roll the back and adopt the continuous type of cooling of leading portion;
(7) coiling temperature is controlled to be 400 ~ 500 ℃.
The 540MPa level hot-rolled ferrite-bainite dual-phase steel ys that adopts this method to produce is: 460～510MPa, and tensile strength is: 540～580MPa, unit elongation is: >=28%, hole expansibility is >=80%.Product is through the Hyundai Motor authentication.
Implementing this method produces: chemical ingredients is simple, stable easily control; The rolling rhythm and the type of cooling can be produced compatibility with routine, can realize the scale stably manufactured.
Combine accompanying drawing that the present invention has been carried out exemplary description above; Obviously the concrete realization of the present invention does not receive the restriction of aforesaid way; As long as the various improvement of having adopted method design of the present invention and technical scheme to carry out; Or directly apply to other occasion without improvement, all within protection scope of the present invention.
Claims (9)
1. an economical 540MPa level ferrite-bainite hot-rolled dual-phase steel is characterized in that, according to mass percent, contains C :≤0.20%; Si :≤1.80%, Mn :≤2.00%, P :≤0.050%; S :≤0.015%, Nb :≤0.10%, and surplus Fe.
2. economical 540MPa level ferrite-bainite hot-rolled dual-phase steel as claimed in claim 1 is characterized in that its ys is: 460～510MPa, and tensile strength is: 540～580MPa, unit elongation is: >=28%, hole expansibility is >=80%.
3. the method for manufacture of economical according to claim 1 or claim 2 540MPa level ferrite-bainite hot-rolled dual-phase steel is characterized in that, adopts following steps:
1) hot metal pretreatment;
2) converter smelting;
3) alloy fine setting station;
4) LF refining;
5) continuous casting;
6) hot continuous rolling.
4. like the method for manufacture of the said economical 540MPa level ferrite-bainite hot-rolled dual-phase steel of claim 3, it is characterized in that the chemical ingredients of the strand after step 1) is handled according to mass ratio is: C:0.06 ~ 0.10%; Si:0.05 ~ 0.15%; Mn:1.30 ~ 1.50%; P≤0.015%; S≤0.010%; Nb:0.015 ~ 0.025%.
5. like the method for manufacture of claim 3 or 4 said economical 540MPa level ferrite-bainite hot-rolled dual-phase steels, it is characterized in that the slab thickness specification after step 1) is handled is 220mm.
6. like the method for manufacture of each said economical 540MPa level ferrite-bainite hot-rolled dual-phase steel among the claim 3-5, it is characterized in that Heating temperature is 1150～1250 ℃ in the step 6), finishing temperature is 800～900 ℃.
7. like the method for manufacture of each said economical 540MPa level ferrite-bainite hot-rolled dual-phase steel among the claim 3-6, it is characterized in that, also comprise the steps:
7) roll the back and adopt the continuous type of cooling of leading portion;
8) batch.
8. like the method for manufacture of the said economical 540MPa level ferrite-bainite hot-rolled dual-phase steel of claim 7, it is characterized in that coiling temperature is 400～500 ℃ in the step 8).
9. like the method for manufacture of each said economical 540MPa level ferrite-bainite hot-rolled dual-phase steel among the claim 6-8, it is characterized in that, be rolled into the thick intermediate blank of 30mm through roughing earlier before the finish to gauge.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103088258A (en) * | 2013-01-23 | 2013-05-08 | 马鞍山钢铁股份有限公司 | Five hundred and ninety Mpa-grade dual-phase steel and production method thereof |
| CN103088255A (en) * | 2013-01-02 | 2013-05-08 | 河北钢铁股份有限公司邯郸分公司 | Manufacturing process of automobile low-alloy high-strength steel cold-rolled sheet with high product of strength and elongation |
| CN103103439A (en) * | 2013-01-23 | 2013-05-15 | 马鞍山钢铁股份有限公司 | Double-phase steel and production method thereof |
| CN106167875A (en) * | 2016-09-29 | 2016-11-30 | 马钢(集团)控股有限公司 | A kind of strength and ductility product economical high strength cold-rolled TRIP steel more than 20GPa % and preparation method thereof |
| CN107747042A (en) * | 2017-11-06 | 2018-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of high reaming steel of the economical great surface quality of 690MPa levels and preparation method thereof |
| CN107868909A (en) * | 2017-11-06 | 2018-04-03 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of high reaming steel of the economical great surface quality of 580MPa levels and preparation method thereof |
| CN109536845A (en) * | 2019-02-01 | 2019-03-29 | 本钢板材股份有限公司 | A kind of tensile strength 590MPa grades of wheels hot-rolled ferrite-bainite dual-phase steel steel band and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102400038A (en) * | 2011-12-06 | 2012-04-04 | 首钢总公司 | Hot-rolled dual-phase steel and production method thereof |
-
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- 2012-06-19 CN CN201210203785.3A patent/CN102732786B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102400038A (en) * | 2011-12-06 | 2012-04-04 | 首钢总公司 | Hot-rolled dual-phase steel and production method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 谷海容等: "铁素体/贝氏体双相钢的延伸凸缘性能研究", 《上海金属》 * |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103088255A (en) * | 2013-01-02 | 2013-05-08 | 河北钢铁股份有限公司邯郸分公司 | Manufacturing process of automobile low-alloy high-strength steel cold-rolled sheet with high product of strength and elongation |
| CN103088255B (en) * | 2013-01-02 | 2014-12-03 | 河北钢铁股份有限公司邯郸分公司 | Manufacturing process of automobile low-alloy high-strength steel cold-rolled sheet with high product of strength and elongation |
| CN103088258A (en) * | 2013-01-23 | 2013-05-08 | 马鞍山钢铁股份有限公司 | Five hundred and ninety Mpa-grade dual-phase steel and production method thereof |
| CN103103439A (en) * | 2013-01-23 | 2013-05-15 | 马鞍山钢铁股份有限公司 | Double-phase steel and production method thereof |
| CN106167875A (en) * | 2016-09-29 | 2016-11-30 | 马钢(集团)控股有限公司 | A kind of strength and ductility product economical high strength cold-rolled TRIP steel more than 20GPa % and preparation method thereof |
| CN106167875B (en) * | 2016-09-29 | 2017-09-19 | 马钢(集团)控股有限公司 | A kind of strength and ductility product is more than 20GPa% economical high strength cold-rolled TRIP steel and preparation method thereof |
| CN107747042A (en) * | 2017-11-06 | 2018-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of high reaming steel of the economical great surface quality of 690MPa levels and preparation method thereof |
| CN107868909A (en) * | 2017-11-06 | 2018-04-03 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of high reaming steel of the economical great surface quality of 580MPa levels and preparation method thereof |
| CN109536845A (en) * | 2019-02-01 | 2019-03-29 | 本钢板材股份有限公司 | A kind of tensile strength 590MPa grades of wheels hot-rolled ferrite-bainite dual-phase steel steel band and preparation method thereof |
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