CN102925809A - Low-alloy steel preparation method capable of simultaneously obtaining reversed austenite and nanometer precipitate - Google Patents
Low-alloy steel preparation method capable of simultaneously obtaining reversed austenite and nanometer precipitate Download PDFInfo
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- CN102925809A CN102925809A CN2012105002127A CN201210500212A CN102925809A CN 102925809 A CN102925809 A CN 102925809A CN 2012105002127 A CN2012105002127 A CN 2012105002127A CN 201210500212 A CN201210500212 A CN 201210500212A CN 102925809 A CN102925809 A CN 102925809A
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Abstract
The invention provides a low alloy steel preparation method capable of simultaneously obtaining reversed austenite and nanometer precipitate, belonging to the field of metal material. The alloy steel comprises the following components by weight percent: 0.06-0.20% of C, 1.0-3.5% of Mn, 0.5-1.5% of Si, 0.5-1.5% of Al, 0.02-0.10% of Nb, 0.5-1.50% of Cu, 0.5-1.50% of Ni, 0.10-0.30% of Mo and the balance of Fe. The specific technology comprises the following steps of: smelting and rolling to obtain an alloy plate, heating the alloy plate to (AC1+ 50) DEG C to (AC1+100) DEG C, carrying out heat preservation to redistribute alloy elements, heating to a temperature between Ac1' and Ac3 and tempering to obtain retained austenite and nanometer scale precipitate. The steel plate prepared according to the invention has a complex phase tissue which consists of ferrite, bainite/martensite, secondary bainite/martensite and retained austenite, wherein the retained austenite content is more than 20%; and as for the nanometer precipitated phase the size of which is 5-30nm the yield strength reaches 700MPa, the tensile strength reaches to 850MPa, the even elongation rate reaches 20%, the total elongation rate reaches 30%, the product of strength and elongation reaches 29000MPa%, and the low temperature impact toughness at the temperature of -40 DEG C and the thickness of 0.75 reaches 70J. The preparation method is simple in technology, low in cost, and high in practical applicability.
Description
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Technical field
The invention belongs to metal material field, is a kind of alloy designs and thermal treatment process that high strength, high-ductility, high tenacity construction(al)steel adopt that have.
Background introduction
Low alloy steel is widely used in the fields such as Architectural Equipment, petroleum conveying pipeline.At home, 1st generation low alloy steel (ferrite of yield strength 300-500MPa level/pearlitic structure carbon manganese steel, silicon manganese steel etc.) and 2nd generation low alloy steel (bainitic steel of yield strength 500-900MPa level, martensitic steel etc.) are the main raws of producing and using at present.Yet the development need of ever-increasing Architectural Equipment has the more high-strength material of high-ductility and toughness, and the 2nd generation low alloy steel of low intensive 1st generation low alloy steel and low toughness and plasticity can not meet the demands.Therefore, need development have high strength, high-ductility and high tenacity the 3rd generation low alloy steel.(Dong Han, Wang Maoqiu, Weng Yuqing. M3 tissue regulation and control theory and the technology of high-performance steel. iron and steel, 2010,45:1-7)
Yield strength and tensile strength that the general easy acquisition of histioid steel is high, but yield tensile ratio is higher, and toughness and plasticity are bad.If there are two or more different phases in the tissue, then soft mutually first surrender in deformation process can improve tensile strength firmly mutually, thereby make steel have good tough coupling.(healthy, Zhou Xiaoguang, Wang Guodong. the research and development of high-strength low-yield ratio steel plate for building. steel rolling, 2009,26:31-35) in general, the rising of the intensity of steel can bring the reduction of toughness and plasticity.The phase-change induced plastic of residual austenite in deformation process can improve simultaneously the intensity of steel and plasticity (Zhang Yinghui, Zhao Hongjin, Kang Yonglin. the progress of TRIP Steel. heat processing technique, 2006,35,61-65).Therefore, the acquisition of residual austenite is development key.Add microalloy element in steel, improving intensity by alloying element separating out of tempering stage is schedule of reinforcement commonly used in the steel.Nb separates out in the tempering of differing temps more than 500 ℃ can improve yield strength to some extent, in the drawing process of Cu between 450-700 ℃ with the effect that also can play precipitation strength of separating out of the form of fcc-Cu.Simultaneously, compound the separating out of Cu and Nb also has obvious precipitating reinforcing effect.
Develop the 3rd generation high strength, high tenacity and high-ductility steel, it is a kind of feasible way that the precipitation strength of the TRIP effect of residual austenite and alloying element is combined.Yet paralympic and precipitate generally form in the different temperature stages: paralympic by obtaining in the isothermal process of middle temperature or low thermophase, precipitate generally obtains in the drawing process more than 500 ℃.Therefore, designing a kind of new thermal treatment process is very necessary at same temperature window to the high plastic-steel of development high-strength and high ductility with the acquisition regulation and control of paralympic formation and precipitate.
Summary of the invention
The present invention is intended to propose a kind of Composition Design and thermal treatment process that obtains at the same time the low alloy steel of residual austenite and nanoscale precipitate, by this thermal treatment process obtain having high strength, the low alloy steel of high-ductility and high tenacity.Hot rolling becomes sheet material to steel through smelting also, then steel plate is reheated air cooling or quenching behind the Ac1-Ac3 two-phase region temperature isothermal 10-60min, reheat air cooling or quenching behind the Ac1'-Ac3 two-phase region tempering 10-60min, acquisition is by the polyphase structure of ferrite, tempering bainite/martensite, new bainite/martensite and residual austenite, obtain simultaneously the precipitate of a large amount of nanoscales, so that steel plate has the feature of high-strength high-ductility high-ductility.
Technical scheme of the present invention is: a kind of Composition Design and thermal treatment process that obtains simultaneously the low alloy steel of residual austenite and nanoscale precipitate proposed, develop have high strength, the low alloy steel of high-ductility and high tenacity:
A kind of preparation method who obtains simultaneously the low alloy steel of residual austenite and nanoscale precipitate, steel alloy composition weight percent is: C:0.06 ~ 0.20%, Mn:1.0 ~ 3.5%, Si:0.5 ~ 1.5%, Al:0.5 ~ 1.5 %, Nb:0.02 ~ 0.10%, Cu:0.5 ~ 1.50%, Ni:0.5 ~ 1.50%, Mo:0.10 ~ 0.30%, surplus is Fe and inevitable impurity.
Its preparation process is as follows:
Step 1: smelting also according to designed chemical ingredients, hot rolling becomes sheet material;
Step 2: the described hot rolled plate of step 1 is reheated to a certain temperature Ac1+50-100 of two-phase region ℃, and quench or air cooling after the time of insulation 10-60min, obtain the reverse tissue of ferrite, tempering bainite/martensitic stucture and alloy part enrichment of element;
Step 3: a certain temperature in reheating the described steel plate of step 2 to the Ac1' temperature of steel plate to the Ac3 temperature range, be incubated 15-60 minute time, make again enrichment of alloying element, form residual austenite and nanometer precipitate, the heterogeneous structure that last air cooling is comprised of ferrite, tempering bainite/martensite, secondary bainite/martensite and residual austenite to the room temperature acquisition.
The steel plate of thermal treatment process processing has the heterogeneous structure that is comprised of ferrite, bainite/martensite, secondary bainite/martensite and residual austenite thus, and the feature that high strength, high-ductility and high tenacity are arranged: more than the Yield strength 700 MPa, more than the tensile strength 850MPa, uniform elongation is more than 20%, breaking elongation is more than 30%, more than the strength and ductility product 29000MPa%, more than-40 ℃ of 0.75 thick low-temperature impact toughness 70J.Wherein, it is about 30% to obtain residual austenite content in the tempering of step 3 stage, and the size of Nb precipitate is at 5nm-20nm, and the size of Cu precipitate is at 10nm-30nm.
The A that relates among the present invention
C1 'After temperature refers to process through step 2, because after the redistributing the Ac1 temperature (bcc begins temperature to the transformation of fcc) that causes steel and reduce of alloying element, new bcc begins temperature to the transformation of fcc.
Characteristics of the present invention are: adopt the low-carbon and low-alloy design, guaranteed that steel plate has good weldability and high intensity.The characteristics of the diffusion enrichment reduction transformation temperature of critical drawing process interalloy element have been utilized, regulate and control to same temperature the formation temperature that reverses austenitic formation temperature and precipitate interval, when obtaining heterogeneous structure, reversed in a large number change austenite and nanoscale precipitate.And alloying constituent and thermal treatment process are simple, and production cost is low, are easy to produce in enormous quantities.
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Description of drawings
Fig. 1 is the thermal treatment process synoptic diagram of production high strength, high-ductility and high-ductility steel among the present invention.T
1=A
C1+ 60～120 ℃, T
2=Ac1' ~ A
C3, t
1=10～60min, t
2=10～60min; A
C1 'It is the critical temperature that the new bcc after the critical processing changes mutually to fcc; t
1, t
2It is isothermal time.
Fig. 2 is that the scanning electron microscope of steel under the heat treatment condition of this invention of embodiment 1 composition organized synoptic diagram.
Fig. 3 is the residual austenite X-ray diffraction result schematic diagram of steel under the heat treatment condition of this invention of embodiment 1 composition.
Fig. 4 is that the microalloy element of steel under the heat treatment condition of this invention of embodiment 1 composition separated out synoptic diagram.
Fig. 5 is that the scanning electron microscope of steel under the heat treatment condition of this invention of embodiment 2 compositions organized synoptic diagram.
Fig. 6 is the residual austenite X-ray diffraction result schematic diagram of steel under the heat treatment condition of this invention of embodiment 2 compositions.
Fig. 7 is that the microalloy element of steel under the heat treatment condition of this invention of embodiment 2 compositions separated out synoptic diagram.
Embodiment
The below will in the embodiment of the invention technical scheme carry out clear, complete description, obviously, described embodiment only is a part very little among the present invention, rather than whole embodiment.Based on the embodiment among the present invention, those of ordinary skills belong to the scope of protection of the invention not making the every other embodiment that obtains under the creative work prerequisite.
Embodiment 1
The low alloy steel composition (massfraction) of table 1 embodiment 1
| C | Mn | Si | Al | Nb | Cu | Ni | Mo | Surplus |
| 0.1% | 1.5~2.5% | 0.8% | 0.78% | 0.04-0.10% | 0.5-2.5% | 1.0% | 0.25 | Fe |
Adopting alloying element content is the low alloy hot rolling steel plate shown in the table 1 in above-described embodiment 2, and putting it into furnace temperature is A
C3More than 100 ℃ of (T
1=780 ℃) chamber type electric resistance furnace in be incubated t
1For air cooling behind the 30min to room temperature, then putting again such as furnace temperature is A
C1～A
C3Between T
2Be incubated t in the chamber type electric resistance furnace of (660 ℃)
2For air cooling behind the 30min to room temperature.Obtain the mechanical property shown in the table 2 among the embodiment 2.As can be known, the uniform elongation of expansion tubing steel plate all reaches more than 25%, and yield strength is 482MPa, and tensile strength is 665MPa, ,-40 ℃ of half thick v-notch Charpy-V impact power reaches 36.6J, satisfies API Spec 5CT standard to the performance requriements of J55 grade of steel.
The mechanical property of the low alloy steel of table 2 embodiment 1
| Yield strength (Mpa) | Tensile strength (Mpa) | Uniform elongation (%) | Elongation after fracture (%) | -40 ℃ of 0.75 thick Charpy-V impact power (J) |
| 707 | 845 | 22.8 | 35 | 91 |
Embodiment 2
Adopting alloying element content is the low alloy hot rolling steel plate shown in the table 3, and putting it into furnace temperature is A
C3More than 80 ℃ of (T
1=760 ℃) chamber type electric resistance furnace in be incubated t
1For air cooling behind the 30min to room temperature, then putting again such as furnace temperature is A
C1 '～A
C3Between T
2Be incubated t in the chamber type electric resistance furnace of (660 ℃)
2For air cooling behind the 30min to room temperature.Obtain mechanical property as shown in table 4.As known from Table 2, the uniform elongation of low alloy steel all reaches 20%, and yield strength is 807MPa, and tensile strength is 965MPa, and-40 ℃ of 0.75 thick v-notch Charpy-V impact power reaches 90J, has good strength and toughness and plasticity coupling.
The composition of the low alloy steel of table 3 embodiment 1 (massfraction)
| C | Mn | Si | Al | Nb | Cu | Ni | Mo | Surplus |
| 0.2% | 1.5~2.5% | 0.8% | 0.78% | 0.04-0.10% | 0.5-2.5% | 1.0% | 0.25 | Fe |
The mechanical property of the low alloy steel of table 4 embodiment 1
| Yield strength (Mpa) | Tensile strength (Mpa) | Uniform elongation (%) | Elongation after fracture (%) | -40 ℃ of 0.75 thick Charpy-V impact power (J) |
| 807 | 965 | 20 | 30 | 70 |
Claims (1)
1. preparation method who to reverse simultaneously the low alloy steel of austenite and nanoscale precipitate, it is characterized in that steel alloy composition weight percentage is: C:0.06 ~ 0.20%, Mn:1.0 ~ 3.5%, Si:0.5 ~ 1.5%, Al:0.5 ~ 1.5 %, Nb:0.02 ~ 0.10%, Cu:0.5 ~ 1.50%, Ni:0.5 ~ 1.50%, Mo:0.10 ~ 0.30%, surplus is Fe and inevitable impurity, and concrete preparation process is as follows:
Step 1: smelting also according to designed chemical ingredients, hot rolling becomes sheet material;
Step 2: the described hot rolled plate of step 1 is reheated to a certain temperature Ac1+50-100 of two-phase region ℃, and quench or air cooling after the time of insulation 10-60min, obtain the reverse tissue of ferrite, tempering bainite/martensitic stucture and alloy part enrichment of element;
Step 3: a certain temperature in reheating the described steel plate of step 2 to the Ac1' temperature of steel plate to the Ac3 temperature range, the time of insulation 10-60min, make again enrichment of alloying element, form residual austenite and nanometer precipitate, the heterogeneous structure that last air cooling is comprised of ferrite, tempering bainite/martensite, secondary bainite/martensite and residual austenite to the room temperature acquisition.
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| CN103225045A (en) * | 2013-04-24 | 2013-07-31 | 北京科技大学 | Preparation method of high plasticity medium and heavy slab with 690 MPa yield strength |
| WO2016095665A1 (en) * | 2014-12-19 | 2016-06-23 | 宝山钢铁股份有限公司 | High-strength high-tenacity steel plate with tensile strength of 800 mpa and production method therefor |
| CN106498146A (en) * | 2016-10-13 | 2017-03-15 | 北京科技大学 | A kind of method for improving slab multi-pass welding welding point low-temperature flexibility |
| CN106755774A (en) * | 2016-12-06 | 2017-05-31 | 上海电机学院 | A kind of heat treatment method of low-carbon and low-alloy high-strength steel |
| CN106755769A (en) * | 2016-11-21 | 2017-05-31 | 南京钢铁股份有限公司 | A kind of Technology for Heating Processing of regulation and control medium managese steel yield tensile ratio |
| CN107794452A (en) * | 2016-08-30 | 2018-03-13 | 宝山钢铁股份有限公司 | A kind of thin strap continuous casting superelevation strength and ductility product continuously surrenders automobile steel and its manufacture method |
| CN108728727A (en) * | 2017-04-14 | 2018-11-02 | 天津大学 | A kind of secondary quenching heat treatment method of Hi-Stren steel and its application |
| CN109023124A (en) * | 2018-10-17 | 2018-12-18 | 东北大学 | LNG storage tank steel plate of high welding heat influence area toughness and preparation method thereof |
| CN109022693A (en) * | 2018-09-17 | 2018-12-18 | 四川易亨机械制造有限公司 | A kind of complex phase alloy steel and preparation method thereof of high intensity |
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| CN111936657A (en) * | 2018-03-30 | 2020-11-13 | 杰富意钢铁株式会社 | High-strength steel sheet and method for producing same |
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| CN113652612A (en) * | 2021-08-19 | 2021-11-16 | 北京理工大学 | Manganese steel in heterogeneous lamellar structure and preparation method thereof |
| CN114410896A (en) * | 2022-01-27 | 2022-04-29 | 北京科技大学 | Ultrahigh-strength medium-carbon spring steel, heat treatment process and high-speed train bogie spring |
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| WO2016095665A1 (en) * | 2014-12-19 | 2016-06-23 | 宝山钢铁股份有限公司 | High-strength high-tenacity steel plate with tensile strength of 800 mpa and production method therefor |
| US11319607B2 (en) | 2014-12-19 | 2022-05-03 | Baoshan Iron & Steel Co., Ltd. | High-strength high-tenacity steel plate with tensile strength of 800 MPa and production method therefor |
| CN107794452A (en) * | 2016-08-30 | 2018-03-13 | 宝山钢铁股份有限公司 | A kind of thin strap continuous casting superelevation strength and ductility product continuously surrenders automobile steel and its manufacture method |
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