CN103194676A - 1,000MPa super ferritic steel and preparation method thereof - Google Patents
1,000MPa super ferritic steel and preparation method thereof Download PDFInfo
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- CN103194676A CN103194676A CN201310119753XA CN201310119753A CN103194676A CN 103194676 A CN103194676 A CN 103194676A CN 201310119753X A CN201310119753X A CN 201310119753XA CN 201310119753 A CN201310119753 A CN 201310119753A CN 103194676 A CN103194676 A CN 103194676A
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Abstract
The invention relates to 1,000MPa super ferritic steel and a preparation method thereof. According to the microstructure of the super ferritic steel, a large number of nano-scale second-phase carbide particles are uniformly distributed on a matrix structure of single-phase ferrite, and the nano-scale particles have a strong precipitation strengthening role, so that the steel has ultrahigh strength while the steel has good extensibility and ultrahigh reaming ratio of the single-phase ferrite. Molten steel meeting a set ingredient control range is smelted through a vacuum induction furnace, and casting blanks are formed through casting. The casting blanks are subjected to forging and heating and are then subjected to hot-rolling, water-cooling and coiling, and the prepared nanoparticle-strengthened ultrahigh-strength steel has the final properties that the tensile strength is 950-1,050 MPa, the extensibility is 18-21% (A50 gage length), and the reaming ratio is over 50%. According to the 1,000MPa super ferritic steel and the preparation method thereof, the production process is simple, and the operation is feasible, so that the 1,000MPa super ferritic steel can be applied to the production of structural members, such as automobile side-face middle columns, edge reinforcements, suspension arms, bumper beams and the like.
Description
Technical field
Present technique relates to super ferritic steel of a kind of 1000MPa and preparation method thereof, it is mainly concerned with a kind of superstrength of preparation, the single-phase ferritic steel of hot rolling that has higher hole expansibility simultaneously, interpolation Ti and Mo element can guarantee that single-phase ferritic steel under the condition with good processability, possesses the intensity of superelevation in soft steel.
Background technology
It is the inexorable trend of following ferrous materials development that the nanometer technology of ferrous materials is used with control, and this nanometer technology had both comprised the nanometer of tissue, also refers to the nanometer control of other phase in the ferrous materials simultaneously.Be the seminar that the Harry K.D.H. Bhadeshia of Cambridge University leads what aspect the nanometer control of ferrous materials prominent achievement is arranged at present, successfully develop the strong nanometer bainitic steel of superelevation with India Tata iron and steel cooperation, be successfully applied to panzer.Secondly National Taiwan University poplar sage leader's seminar and Sinosteel Corporation's cooperative development nanoparticle are separated out the hot rolling super-high strength steel.In actual applications then with Nano-Hiten 780 steel grades of 05 year JFE exploitation, it reaches more than 300 ton/month in initial hot rolling output, and its output is also in constantly increasing.
And at home, Shoudu Iron and Steel Co 2012 has launched the research of the nanoparticle precipitation strength steel of joint study exploitation 780MPa hot rolling with leaders' such as metallurgical engineering research institute of University of Science ﹠ Technology, Beijing Tang Di, Zhao Aimin seminar.Other domestic steel mill organizes the research of steel grade not report as yet for hot rolling 780MPa pure ferrite.In the nano particle reinforced steel of cooperation research and development 780MPa, also other super ferrite steel grade of 980MPa level has been carried out development research.
The present invention is by adding titanium and molybdenum element in the single-phase ferritic steel of low-carbon (LC), and at high-temperature final rolling, the high temperature isothermal batches and makes the carbide particle of separating out a large amount of nano-scales at ferrite matrix after the water-cooled, thereby guaranteeing that single-phase ferrite has under the condition of good processability, can obtain other intensity of 1000MPa level.So just can obtain to have the super ferritic steel of 1000MPa of superstrength and good processability.
Summary of the invention
The objective of the invention is to utilize the method for nano-scale carbide precipitation strength, produce a kind of hot rolled ferrite super-high strength steel with good processability.
For achieving the above object, technical scheme of the present invention is:
The super ferritic steel of a kind of 1000MPa, its chemical ingredients mass percent is:
C 0.06～0.15%；
Si 0.01～0.30%；
Mn 0.1～2.0%；
P ≤0.001%；
S ≤0.001%；
N ≤0.001%；
Ti 0.10~0.30%；
Mo 0.10~0.60%。
The preparation method that the present invention adopts high temperature soaking, high-temperature final rolling and high temperature to batch, it comprises the steps:
1) a kind of low-carbon (LC) hot rolling pure ferrite based ultra-high strength superelevation hole expansibility steel, its chemical ingredients mass ratio is: C%:0.01～0.2, Si%:0.01～0.3, Mn%:0.1～2, P% :≤0.01, S% :≤0.01, N% :≤0.01, Ti%:0.01 ~ 0.3, Mo%:0.01 ~ 0.6; All the other are Fe and unavoidable impurities; Smelt, cast and forge into steel billet by mentioned component;
2) steel billet is through 1250 ~ 1300 ℃ of heating, be incubated soaking in 1～2 hour after, at A
R3The finish to gauge of above high-temperature zone, finishing temperature is at 880 ℃～950 ℃, then water-cooled, cooling rate is cooled to 600 ℃-700 ℃ at 30 ~ 50 ℃/s, batches subsequently, coiling temperature cools to room temperature at 600 ℃～700 ℃ with the furnace behind insulation 1 ~ 2h, can obtain the soak strand;
3) with step 2) the soak strand that obtains carries out hot rolling, and the hot rolling draft obtains the super ferritic steel of superstrength between 80%～90%, and its tensile strength reaches more than the 980MP, and total elongation after fracture reaches more than 19%;
Further, described step 2) in, steel billet is through 1250 ℃ of heating of high temperature, and after the insulation 1.5h soaking, the high-temperature final rolling temperature is 950 ℃, coiling temperature is 600 ℃.
To utilize high temperature to batch to separate out a large amount of nano-scale carbide are the present invention is guaranteeing that ferritic steel itself well under the prerequisite of formability, improves the principal character of its intensity.
The content requirement of each element and effect:
C:Cization thing forming element, with Ti and Mo element when the high temperature isothermal batches so that (Ti, Mo) form of C is separated out, and plays strong precipitation strength effect.The content of carbon can not be too high, and the too high alligatoring that then has perlite generation and carbide can make the formability variation.
Si:Si is a kind of effective solution strengthening element, and when the Si too high levels, separating out of meeting accelerated carbonation thing makes the carbide alligatoring, makes the processability variation.
Mn:Mn is strong molten strengthening element, when the Mn too high levels, has segregation or hard forms mutually, makes the formability variation.
P:P is the solution strengthening element, when the P too high levels, has segregation and occurs, and makes the formability variation.
S:S is harmful element, and S content is more low more good, when S content is higher, can make the formability variation.
N:N content is more low more good, when N content is higher, can make the nitride alligatoring, makes the formability variation.
Ti:Ti and C play the effect of strong precipitation strength in conjunction with forming tiny carbide, when greatly improving the intensity of steel, can not influence the formability of steel.
Mo:Mo can suppress growing up of the second phase carbide particle when separating out with Ti and C formation carbide, make that the carbide precipitate particle is more tiny, makes the effect of precipitation strength more remarkable.
Beneficial effect of the present invention:
1) possesses excellent comprehensive mechanical properties.The tensile strength of the steel grade that the present invention relates to is 950 ~ 1050MPa, and unit elongation is at 18%-23%, and hole expansibility is more than 50%.Because the massfraction of C is 0.01%～0.1%, does not specially add Si, therefore also possesses good weldability.
2) operation feasible, equipment is simple.The present invention adopts conventional smelting and steel rolling equipment, and the hot rolling technology simple and feasible, and present most of industrial production line all can be produced at existing equipment.
3) application prospect is extensive.The high hole expansibility hot rolled ferrite steel that the present invention prepares has high intensity when guaranteeing good processability, it is applied on the structural parts such as automobile side center pillar, limit portion stiffener, suspension arm and collision prevention girders, and prospect is considerable.
Description of drawings
Fig. 1 is the thermal treatment process synoptic diagram;
Fig. 2 is the stress-strain(ed) curve synoptic diagram;
Fig. 3 separates out the topographic profile synoptic diagram for the nano-scale carbide.
Embodiment
The chemical ingredients given according to table 1 adopts electromagnetic induction furnace vacuum melting, the blank forging of casting become steel billet, to carry out subsequent technique.Fig. 1 is the thermal treatment process synoptic diagram.
Table 1 is the mass percent of each composition
Table 1
| Numbering | C | Si | Mn | Ti | Mo | S | P | N | Surplus |
| 1# | 0.090 | 0.21 | 1.70 | 0.19 | 0.37 | 0.0050 | 0.0080 | 0.0050 | Fe and inevitable impurity |
| 2# | 0.090 | 0.21 | 1.70 | 0.17 | 0.38 | 0.0078 | 0.0053 | 0.0043 | Fe and inevitable impurity |
| 3# | 0.085 | 0.23 | 1.74 | 0.14 | 0.55 | 0.0130 | 0.0065 | 0.0041 | Fe and inevitable impurity |
Hot rolling technology is for being heated to forging stock 1250 ℃ of insulations 1.5 hours, hot rolling on 350mm two roller hot rollss, 6 passages of hot rolling obtain thickness and are the latten about 2～6mm, total deformation is 80%～90%, and its open rolling and finishing temperature are respectively 1150 ℃ and 950 ℃.
Cooling rate water-cooled with 30 ~ 50 ℃/s after the finish to gauge arrives coiling temperature, and the present invention has adopted three kinds of different coiling temperatures, 600 ℃, 650 ℃ and 700 ℃.Batch isothermal 1 ~ 2h, furnace cooling then at process furnace.Fig. 2 is the stress-strain(ed) curve synoptic diagram; Fig. 3 separates out the topographic profile synoptic diagram for the nano-scale carbide.
The corresponding composition 1# of different technical parameters performance is as shown in table 2:
Table 2 is the 1# mechanical property of main technologic parameters correspondence
Table 2
| Coiling temperature/℃ | Yield strength/Mpa | Tensile strength/Mpa | Yield tensile | Unit elongation | |
| 600 | 935 | 985 | 0.95 | 19.4 | |
| 650 | 835 | 870 | 0.96 | 20.2 | |
| 700 | 670 | 720 | 0.93 | 21.6 |
Claims (3)
1. super ferritic steel of 1000MPa, its main chemical quality per-cent is as follows:
C 0.06～0.15%；
Si 0.01～0.30%；
Mn 0.1～2.0%；
P ≤0.001%；
S ≤0.001%；
N ≤0.001%；
Ti 0.10~0.30%；
Mo 0.10~0.60%。
2. the preparation method of the super ferritic steel of 1000MPa as claimed in claim 1, it comprises the steps:
1) a kind of low-carbon (LC) hot rolling pure ferrite based ultra-high strength superelevation hole expansibility steel, its chemical ingredients mass ratio is: C%:0.06～0.15, Si%:0.01～0.30, Mn%:0.1～2, P% :≤0.001, S% :≤0.001, N% :≤0.001, Ti%:0.10 ~ 0.30, Mo%:0.10 ~ 0.60; All the other are Fe and unavoidable impurities; Smelt, cast and forge into steel billet by mentioned component;
2) steel billet is through 1250 ~ 1300 ℃ of heating, be incubated soaking in 1～2 hour after, at A
R3The finish to gauge of above high-temperature zone, finishing temperature is at 880 ℃～950 ℃, then water-cooled, cooling rate is cooled to 600 ℃-700 ℃ at 30 ~ 50 ℃/s, batches subsequently, coiling temperature cools to room temperature at 600 ℃～700 ℃ with the furnace behind insulation 1 ~ 2h, can obtain the soak strand;
3) with step 2) the soak strand that obtains carries out hot rolling, and the hot rolling draft obtains the super ferritic steel of superstrength between 80%～90%, and its tensile strength reaches more than the 980MP, and total elongation after fracture reaches more than 19%.
3. as the preparation method of the super ferritic steel of right 2 desired 1000MPa, its principal character is: described step 2), steel billet is through 1250 ℃ of heating of high temperature, and after the insulation 1.5h soaking, the high-temperature final rolling temperature is 950 ℃, coiling temperature is 600 ℃.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104148410A (en) * | 2014-07-30 | 2014-11-19 | 东北大学 | Control method of titanium micro-alloyed steel nano precipitate |
| CN106222550A (en) * | 2016-08-03 | 2016-12-14 | 宁波宏协承汽车部件有限公司 | A kind of high-strength automotive anti-collision beam and preparation method thereof |
| CN108277434A (en) * | 2018-03-19 | 2018-07-13 | 武汉钢铁有限公司 | The precipitation enhancement type ferritic steel and production method that a kind of yield strength is 900MPa grades |
| CN110747322A (en) * | 2019-09-26 | 2020-02-04 | 中国电力科学研究院有限公司 | 1180MPa nanoparticle reinforced ferrite steel and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1756853A (en) * | 2003-04-21 | 2006-04-05 | 杰富意钢铁株式会社 | High strength hot rolled steel sheet and method for manufacturing the same |
| CN102080192A (en) * | 2011-01-07 | 2011-06-01 | 南京钢铁股份有限公司 | Low-yield ratio, high-plasticity, ultrafine-grain and high-strength steel and manufacturing method thereof |
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2013
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1756853A (en) * | 2003-04-21 | 2006-04-05 | 杰富意钢铁株式会社 | High strength hot rolled steel sheet and method for manufacturing the same |
| CN102080192A (en) * | 2011-01-07 | 2011-06-01 | 南京钢铁股份有限公司 | Low-yield ratio, high-plasticity, ultrafine-grain and high-strength steel and manufacturing method thereof |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104148410A (en) * | 2014-07-30 | 2014-11-19 | 东北大学 | Control method of titanium micro-alloyed steel nano precipitate |
| CN104148410B (en) * | 2014-07-30 | 2016-06-29 | 东北大学 | A kind of control method of titanium micro-alloyed steel nano-scaled precipitate |
| CN106222550A (en) * | 2016-08-03 | 2016-12-14 | 宁波宏协承汽车部件有限公司 | A kind of high-strength automotive anti-collision beam and preparation method thereof |
| CN108277434A (en) * | 2018-03-19 | 2018-07-13 | 武汉钢铁有限公司 | The precipitation enhancement type ferritic steel and production method that a kind of yield strength is 900MPa grades |
| CN108277434B (en) * | 2018-03-19 | 2020-08-04 | 武汉钢铁有限公司 | Precipitation strengthening ferritic steel with yield strength of 900MPa and production method thereof |
| CN110747322A (en) * | 2019-09-26 | 2020-02-04 | 中国电力科学研究院有限公司 | 1180MPa nanoparticle reinforced ferrite steel and preparation method thereof |
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