CN102517496A - Hot rolled ferrite/martensite double phase steel and production method thereof - Google Patents
Hot rolled ferrite/martensite double phase steel and production method thereof Download PDFInfo
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Abstract
The invention relates to hot rolled ferrite/martensite double phase steel and a production method thereof. The double phase steel comprises the following components, by mass, 0.06-0.10% of C, 1.00-2.00% of Mn, 0.40-0.60% of Si, equal to or less than 0.02% of P, equal to or less than 0.02% of S, 0.08-0.12% of Ti, and the balance Fe and inevitable impurities. The double phase steel provided in the invention contains less than 0.5% of Si, so the surface quality of the steel can be easily controlled; and additionally, the low cost Ti element is added to improve the strength of the steel as a precipitation strengthening element, so costs of steel products are reduced.
Description
Technical field
The present invention relates to the steel rolling field, particularly a kind of hot-rolled dual-phase steel of tensile strength 780MPa level and working method thereof.
Background technology
In recent years; Along with the direction of automobile to energy-conservation, loss of weight and safety develops; Hot-rolled dual-phase steel has been widely used in making members such as automobile reinforcing plate, wheel, chassis, collision bumper, the various frameworks of car body with its HS, resistance to fatigue, high reaming performance and high formability ability.According to ULSAB plan, most of high-strength vehicle plate adopts is dual phase steel.
At present, the composition of patent documentation of having delivered and the disclosed ferrito-martensite dual phase steel of other document has following characteristics: more Si element and Al element are added in (1), and effect comprises expansion ferrite transformation district and reinforced ferrite matrix; (2) add alloying elements such as Cr, Mo, effect is to improve the hardening capacity of steel, thereby reduces when producing this product the requirement to water cooling equipment and taking-up equipment.Si content is higher than at 0.5% o'clock in the characteristics (1), and hot-rolled sheet surface quality control difficulty strengthens, and Al content is higher than at 0.5% o'clock, has increased the smelting difficulty of steel; The interpolation of Cr, Mo alloying element has increased the cost of steel undoubtedly in the characteristics (2).
Summary of the invention
The invention provides a kind of hot rolled ferrite/martensite dual-phase steel, adapted to the developing of automobile industry demand, solved that hot rolled ferrite/martensite dual-phase steel production cost is high, the problem of complex process.
Hot rolled ferrite/martensite dual-phase steel provided by the invention, its composition quality percentage ratio is:
C:0.06%～0.10%, Si:0.40%～0.60%, Mn:1.00%～2.00%, P: S≤0.02%: Ti:0.08%～0.12%≤0.02%,, all the other are Fe and inevitable impurity.
The present invention also provides a kind of working method that solves the problems of the technologies described above, and may further comprise the steps:
Step 1: will (C:0.06%～0.10%, Si:0.40%～0.60%, Mn:1.00%～2.00%, P: S≤0.02%: Ti:0.08%～0.12%≤0.02%,, all the other are Fe and inevitable impurity by the mentioned component scheme.) design, smelt good steel and cast blank, again with blank heating to 1180 ℃～1250 ℃, and under this temperature, be incubated;
Step 2: the blank to obtaining after handling through step 1 carries out the controlled rolling of two stages, and promptly the austenite recrystallization district is rolling rolling with the non-recrystallization zone of austenite, wherein recrystallization zone deflection＞60%;
Step 3: adopt segmentation refrigerative method to cool off to the steel plate that after step 2 controlled rolling, obtains, the finishing temperature scope of corresponding steel plate is 750～850 ℃, adopts the cooling rate cooling of water-cooled with >=30 ℃/s;
Step 4: after cooling, steel plate is batched to steel plate completing steps 3.
Further, 750～800 ℃ of the finishing temperature scopes of the steel plate that the segmentation method of cooling that above-mentioned steps 3 adopts is corresponding are treated temperature to 550～600 ℃ in air after the finish to gauge, adopt the cooling rate cooling of water-cooled with >=40 ℃/s subsequently.
Further; 800～850 ℃ of the finishing temperature scopes of the steel plate that the segmentation method of cooling that above-mentioned steps 3 adopts is corresponding, 30～50 ℃/s of first section water-cooled cooling rate is cooled to 650～700 ℃; In air, treat temperature 8～15s subsequently, subordinate phase water-cooled cooling rate >=40 ℃/s.
Further, rolling temperature interval, above-mentioned steps 2 said austenite recrystallization district is 950～1200 ℃, and rolling reduction is 50～70%.
Further, rolling temperature interval, the non-recrystallization zone of above-mentioned steps 2 said austenites is 750～930 ℃, and rolling reduction is 30～50%.
Further, the above-mentioned steps 4 described coiling temperatures that batch correspondence are 200～300 ℃.
Hot-rolled dual-phase steel provided by the invention because Si content is lower in its composition, only adds alloying element Ti, has reduced the cost of product made from steel surface quality control difficulty, smelting difficulty and steel, makes product have good comprehensive mechanical property.
Description of drawings
Fig. 1 is the typical gold phase constitution photo after 780MPa level ferrite/martensite dual phase sheet steel corrodes through l epera reagent for tensile strength provided by the invention, and wherein, white is martensitic stucture, and grey is a ferritic structure.
Embodiment:
Below principle of the present invention and characteristic are described, institute gives an actual example and only is used to explain the present invention, is not to be used to limit scope of the present invention.
The chemical composition of hot-rolled dual-phase steel provided by the invention and corresponding content are referring to table 1:
Table 1 (massfraction %, surplus is Fe and inevitable impurity)
| Become offshoot program | C | Si | Mn | P | S | Ti |
| Composition 1 | 0.09 | 0.50 | 1.78 | 0.010 | 0.005 | 0.08 |
| Composition 2 | 0.10 | 0.47 | 1.72 | 0.009 | 0.005 | 0.10 |
| Composition 3 | 0.08 | 0.43 | 1.65 | 0.011 | 0.004 | 0.12 |
| Composition 4 | 0.082 | 0.45 | 1.70 | 0.008 | 0.003 | 0.11 |
| Composition 5 | 0.085 | 0.46 | 1.75 | 0.011 | 0.003 | 0.12 |
| Composition 6 | 0.099 | 0.41 | 1.68 | 0.009 | 0.005 | 0.09 |
Embodiment 1
Cast blank with smelting the good molten steel that meets composition 1 said one-tenth offshoot program in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1180 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 65%; It is 930 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 35%, finishing temperature are 800 ℃.Steel plate is accomplished the rolling back temperature, temperature in air, treated and is treated after 600 ℃, to begin water-cooled, and the water-cooled cooling rate is 45 ℃/s, is chilled to 300 ℃, reaches coiling temperature, batches.
Embodiment 2
Cast blank with smelting the good molten steel that meets composition 2 said one-tenth offshoot programs in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1150 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 60%; It is 910 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 40%, finishing temperature are 780 ℃.Steel plate is accomplished the rolling back temperature, temperature in air, treated and is treated after 580 ℃, to begin water-cooled, and the water-cooled cooling rate is 50 ℃/s, is chilled to 250 ℃, reaches coiling temperature, batches.
Embodiment 3
Cast blank with smelting the good molten steel that meets composition 3 said one-tenth offshoot programs in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1100 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 50%; It is 910 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 50%, finishing temperature are 750 ℃.Steel plate is accomplished the rolling back temperature, temperature in air, treated and is treated after 550 ℃, to begin water-cooled, and the water-cooled cooling rate is 60 ℃/s, is chilled to 210 ℃, reaches coiling temperature, batches.
Embodiment 4
Cast blank with smelting the good molten steel that meets composition 4 said one-tenth offshoot programs in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1180 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 65%; It is 930 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 35%, finishing temperature are 850 ℃.At first carry out water-cooled after the steel plate completion is rolling, 30 ℃/s of water-cooled cooling rate is chilled to 700 ℃, in air, treats warm 8s subsequently, treats to begin water-cooled after the temperature, and the water-cooled cooling rate is 45 ℃/s, is chilled to 300 ℃, reaches coiling temperature, batches.
Embodiment 5
Cast blank with smelting the good molten steel that meets composition 5 said one-tenth offshoot programs in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1150 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 60%; It is 910 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 40%, finishing temperature are 830 ℃.At first carry out water-cooled after the steel plate completion is rolling, 40 ℃/s of water-cooled cooling rate is chilled to 680 ℃, in air, treats warm 12s subsequently, treats to begin water-cooled after the temperature, and the water-cooled cooling rate is 55 ℃/s, is chilled to 250 ℃, reaches coiling temperature, batches.
Embodiment 6
Cast blank with smelting the good molten steel that meets composition 6 said one-tenth offshoot programs in the table 1, be incubated 0.5h after then blank being warming up to 1200 ℃ with stove, be rolled.Wherein, it is 1100 ℃ that the austenite recrystallization district begins rolling temperature, and deflection is 50%; It is 910 ℃ that the non-recrystallization zone of austenite begins rolling temperature, and blank deformation amount 50%, finishing temperature are 800 ℃.At first carry out water-cooled after the steel plate completion is rolling, 50 ℃/s of water-cooled cooling rate is chilled to 650 ℃, in air, treats warm 15s subsequently, treats to begin water-cooled after the temperature, and the water-cooled cooling rate is 60 ℃/s, is chilled to 200 ℃, reaches coiling temperature, batches.
Hot-rolled dual-phase steel provided by the invention because Si content is lower in its composition, only adds alloying element Ti, has reduced the cost of product made from steel surface quality control difficulty, smelting difficulty and steel, makes product have good comprehensive mechanical property.Simultaneously, the hot rolled ferrite martensite dual-phase steel that the present invention obtains, ys scope are 490～600MPa; Tensile strength 780～950MPa, unit elongation are 15%～25%, yield tensile ratio＜0.7; Have the good intensity and the coupling of plasticity, and good fracture property.
The mechanical property of the hot-rolled dual-phase steel of the present invention that table 2 obtains for each embodiment.
Table 2 (unit is MPa)
| Sequence number | Rp 0.2 | Rm | Rp 0.2/Rm | A 80，％ | The n value |
| Embodiment 1 | 490 | 780 | 0.63 | 25 | 0.21 |
| Embodiment 2 | 530 | 820 | 0.65 | 23 | 0.20 |
| Embodiment 3 | 600 | 880 | 0.68 | 19 | 0.19 |
| Embodiment 4 | 585 | 850 | 0.68 | 25 | 0.19 |
| Embodiment 5 | 590 | 887 | 0.66 | 23 | 0.16 |
| Embodiment 6 | 593 | 950 | 0.62 | 18 | 0.15 |
The above is merely preferred embodiment of the present invention, and is in order to restriction the present invention, not all within spirit of the present invention and principle, any modification of being done, is equal to replacement, improvement etc., all should be included within protection scope of the present invention.
Claims (8)
1. a hot rolled ferrite/martensite dual-phase steel is characterized in that, the composition weight percentage is:
C:0.06%～0.10%, Si:0.40%～0.60%, Mn:1.00%～2.00%, P: S≤0.02%: Ti:0.08%～0.12%≤0.02%,, all the other are Fe and inevitable impurity.
2. hot-rolled dual-phase steel as claimed in claim 1 is characterized in that, contains ferritic and martensite duplex structure.
3. the working method of hot-rolled dual-phase steel as claimed in claim 2 is characterized in that, comprises following steps:
All thermal treatment of step 1: select to meet the blank of the described hot-rolled dual-phase steel composition of claim 1,, and under this temperature, be incubated with blank heating to 1180 ℃～1250 ℃;
Step 2 liang stage rolling: the blank to after handling through step 1 carries out the controlled rolling of two stages, and promptly the austenite recrystallization district is rolling rolling with the non-recrystallization zone of austenite, wherein recrystallization zone deflection＞60%;
Step 3 segmentation cooling: to carry out the segmentation cooling through the steel plate that obtains after step 2 controlled rolling, the finishing temperature scope that steel plate is corresponding is 750～850 ℃, adopts the cooling rate cooling of water-cooled with >=30 ℃/s;
Step 4 is batched: after the cooling to steel plate completing steps 3, steel plate is batched.
4. the working method of hot-rolled dual-phase steel as claimed in claim 3; It is characterized in that; The finishing temperature scope of the steel plate that said segmentation method of cooling is corresponding is 750～800 ℃, in air, treats temperature after the steel plate finish to gauge to 550～600 ℃, adopts the cooling rate cooling of water-cooled with >=40 ℃/s subsequently.
5. the working method of hot-rolled dual-phase steel as claimed in claim 3; It is characterized in that the finishing temperature scope of the steel plate that said segmentation method of cooling is corresponding is 800～850 ℃, first section water-cooled; 30～50 ℃/s of cooling rate; Be cooled to 650～700 ℃, in air, treat temperature 8～15s subsequently, subordinate phase water-cooled cooling rate >=40 ℃/s.
6. like the working method of the arbitrary described hot-rolled dual-phase steel of claim 3 to 5, it is characterized in that rolling temperature interval, described austenite recrystallization district is 950～1200 ℃, rolling reduction is 50～70%.
7. like the working method of the arbitrary described hot-rolled dual-phase steel of claim 3 to 5, it is characterized in that rolling temperature interval, the non-recrystallization zone of described austenite is 750～930 ℃, rolling reduction is 30～50%.
8. like the working method of the arbitrary described hot-rolled dual-phase steel of claim 3 to 5, it is characterized in that the said steel billet temperature that batches correspondence is 200～300 ℃.
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104451402A (en) * | 2014-12-19 | 2015-03-25 | 山东钢铁股份有限公司 | 700MPa-grade hot-rolled dual-phase steel and manufacturing method thereof |
| CN106521327A (en) * | 2016-12-27 | 2017-03-22 | 首钢总公司 | Hot-rolled pickled steel strip with high broaching performance and production method thereof |
| CN106702275A (en) * | 2016-12-06 | 2017-05-24 | 内蒙古包钢钢联股份有限公司 | 700 MPa grade hot rolling dual-phase steel 2 mm-4 mm in thickness and machining method of 700 MPa grade hot rolling dual-phase steel |
| CN107760996A (en) * | 2017-09-25 | 2018-03-06 | 武汉钢铁有限公司 | A kind of hot-rolled dual-phase steel and its processing method |
| CN108396225A (en) * | 2018-04-17 | 2018-08-14 | 马钢(集团)控股有限公司 | A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method |
| CN108467996A (en) * | 2018-03-27 | 2018-08-31 | 本钢板材股份有限公司 | The dual-phase hot-rolled acid-cleaning plate of wheel spoke ferrite-martensite and preparation method |
| CN109402355A (en) * | 2018-12-29 | 2019-03-01 | 首钢集团有限公司 | A kind of 600MPa grades of hot rolling TRIP type dual phase steel and preparation method thereof |
| CN109554616A (en) * | 2018-12-29 | 2019-04-02 | 首钢集团有限公司 | A kind of 700MPa grades of hot rolling TRIP auxiliary type dual phase steel and preparation method thereof |
| CN113005367A (en) * | 2021-02-25 | 2021-06-22 | 武汉钢铁有限公司 | 780 MPa-grade hot-rolled dual-phase steel with excellent hole expanding performance and preparation method thereof |
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104451402A (en) * | 2014-12-19 | 2015-03-25 | 山东钢铁股份有限公司 | 700MPa-grade hot-rolled dual-phase steel and manufacturing method thereof |
| CN106702275A (en) * | 2016-12-06 | 2017-05-24 | 内蒙古包钢钢联股份有限公司 | 700 MPa grade hot rolling dual-phase steel 2 mm-4 mm in thickness and machining method of 700 MPa grade hot rolling dual-phase steel |
| CN106521327A (en) * | 2016-12-27 | 2017-03-22 | 首钢总公司 | Hot-rolled pickled steel strip with high broaching performance and production method thereof |
| CN106521327B (en) * | 2016-12-27 | 2018-08-21 | 首钢集团有限公司 | A kind of hot rolling acid-cleaning strip and its production method with high reaming performance |
| CN107760996A (en) * | 2017-09-25 | 2018-03-06 | 武汉钢铁有限公司 | A kind of hot-rolled dual-phase steel and its processing method |
| CN108467996A (en) * | 2018-03-27 | 2018-08-31 | 本钢板材股份有限公司 | The dual-phase hot-rolled acid-cleaning plate of wheel spoke ferrite-martensite and preparation method |
| CN108467996B (en) * | 2018-03-27 | 2019-05-31 | 本钢板材股份有限公司 | The dual-phase hot-rolled acid-cleaning plate of wheel spoke ferrite-martensite and preparation method |
| CN108396225A (en) * | 2018-04-17 | 2018-08-14 | 马钢(集团)控股有限公司 | A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method |
| CN108396225B (en) * | 2018-04-17 | 2019-12-03 | 马钢(集团)控股有限公司 | A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method |
| CN109402355A (en) * | 2018-12-29 | 2019-03-01 | 首钢集团有限公司 | A kind of 600MPa grades of hot rolling TRIP type dual phase steel and preparation method thereof |
| CN109554616A (en) * | 2018-12-29 | 2019-04-02 | 首钢集团有限公司 | A kind of 700MPa grades of hot rolling TRIP auxiliary type dual phase steel and preparation method thereof |
| CN113005367A (en) * | 2021-02-25 | 2021-06-22 | 武汉钢铁有限公司 | 780 MPa-grade hot-rolled dual-phase steel with excellent hole expanding performance and preparation method thereof |
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Application publication date: 20120627 |