CN101550514A - Hot-rolling transformation-induced plasticity steel plate and preparation method thereof - Google Patents
Hot-rolling transformation-induced plasticity steel plate and preparation method thereof Download PDFInfo
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Abstract
A hot-rolling transformation-induced plasticity steel plate and a preparation method thereof belong to the field of metallurgical technology. The steel plate comprises the following components by weight percentage: 0.18 to 0.20 percent of C, 1.30 to 1.45 percent of Mn, 0.60 to 0.70 percent of Si, 0.50 to 0.60 percent of Al, 0.009 percent or less than 0.009 percent of P, 0.007 percent or less than 0.007 percent of S, 0 to 0.040 percent of Nb and the balance of Fe. The preparation method thereof comprises the steps of: smelting low-silicon and low-carbon steel into steel ingot; heating the steel ingot to 1200 plus/minus 10 DEG C to obtain billet through forging; loading the billet into a heating furnace, heating the billet to 1200 plus/minus 10 DEG C and keeping temperature for 1 to 2 hours; carrying out rough rolling and precision rolling; air cooling till the temperature reaches 700 to 760 DEG C; accelerating cooling at a speed of reducing 40 to 50 DEG C per second; and adopting a reeling machine for reeling. The hot-rolling transformation-induced plasticity steel plate prepared by the method has high intensity of tension and better impact ductility.
Description
Technical field
The invention belongs to metallurgical technology field, particularly a kind of hot-rolling transformation-induced plasticity steel plate and preparation method thereof.
Background technology
Country releases the fuel oil tax policy and makes human consumer's automobile that more the more options oil consumption is few, discharge capacity is little, and the upgrading of automotive industry must be accelerated.TRIP (Transformation Induced Plasticity) steel claims phase change induction plasticity steel again, is a kind of high-strength high-plasticity steel that grew up in recent years.Can alleviate car weight as autobody sheet, reduce oil consumption, stronger energy absorption capability is arranged simultaneously, can resist the viscous deformation when clashing into, significantly improve the safe class of automobile, have obvious superiority.This steel plate becomes a big focus of recent automotive sheet.Along with production technique improve constantly and perfect, the large-scale industrial production of TRIP steel plate has become possibility, application prospect will be more wide also.
Typical silicomanganese is that the TRIP steel contains 1.3%～2.0% silicon, and having of silicon is beneficial to the acquisition more austenite, thereby obtains big phase change induction plasticity.But there is the problem of following several respects in the too high TRIP of the making steel of silicone content in industrial production: (a) continuously cast bloom toughness is relatively poor, is difficult for producing; (b) easily produce very thick iron scale during hot rolling, be difficult for pickling, the surface quality of influence band steel; (c) when pot galvanize, high Si content makes the wettability variation of zinc layer and very easily forms brittle alloy layer, thereby weakens the bonding force of coating and substrate.The mode of action and the silicon of aluminium are similar, and the interpolation of aluminium can not worsen plating performance, and aluminium can be used as the substitute element of silicon.But the aluminium too high levels can reduce the heat resistanceheat resistant crackle ability and the anti-erosional competency of galvanizing production of steel.The adding of microalloy element Nb plays significant effect to carbon enrichment in grain refining, transformation behavior, the austenite and martensite forming core, technology controlling and process is become be easier to, and can further increase the intensity of steel under the situation of the not obvious decline of toughness.
Produce the typical operational path of TRIP steel plate and mainly be divided into two kinds of hot rolling and cold rolling thermal treatments.Nearly 20, what the research field of Chinese scholars mainly concentrated on cold rolling thermal treatment TRIP steel rolling back critical annealing and bainite isothermal processes aspect.And having more practical significance aborning for the research of hot rolling TRIP steel, relevant report is rare.This is that this has certain difficulty in production operation because hot rolling TRIP steel, need finish cooling in order to obtain a certain amount of and stable residual austenite in certain temperature range, needs to improve operative technique and determines cooling temperature exactly.And the production of hot rolling TRIP steel does not need processing steps such as thermal treatment after cold rolling and cold rolling with respect to the production of cold rolling thermal treatment TRIP steel, thereby reduced production cost.And the silicone content of existing TRIP steel is too high, makes that the continuously cast bloom toughness of steel plate is relatively poor, the hot rolling performance and the plating performance of deterioration steel.
Summary of the invention
At above technical problem, the invention provides a kind of hot-rolling phase change induction plasticity steel steel plate and preparation method thereof.
The composition of hot-rolling transformation-induced plasticity steel plate of the present invention (TRIP steel plate) is by weight percentage for containing C0.18～0.20%, Mn1.30～1.45%, Si0.60～0.70%, Al0.50～0.60%, P≤0.009%, S≤0.007%, Nb0～0.040%, surplus are Fe.The yield strength of this hot-rolled steel sheet is not less than 535MPa, and tensile strength is not less than 639MPa, and strength and ductility product is greater than 18000MPa%.
The preparation method of hot rolling TRIP steel plate of the present invention carries out according to the following steps:
1, low-carbon (LC) silicon steel is smelted into steel ingot, its composition is C0.18～0.20% by weight percentage, Mn1.30～1.45%, and Si0.60～0.70%, Al0.50～0.60%, P≤0.009%, S≤0.007%, Nb0～0.040%, surplus is Fe.Then this steel ingot is heated to 1200 ± 10 ℃, insulation 1.5～2hr forges into steel billet.
2, adopt the mode of hot charging stove, under 750～800 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 1～2hr, insulation finishes the back and adopts milling train to carry out roughing and finish rolling, and start rolling temperature is 1060～1120 ℃, and roughing is 3～5 passages, rolling temperature is 900～1120 ℃, and the roughing total deformation is 40～50%; Finish rolling is 2 passages, and rolling temperature is 760～870 ℃, and the finish rolling total deformation is 40～50%, and finishing temperature is 760～800 ℃, obtains rolled piece.
3, with rolled piece air cooling to 700～760 ℃, quicken cooling with the speed of 40～50 ℃/s again after finish rolling finishes, adopt reeling machine to batch when being cooled to 350～550 ℃, the back air cooling that curls is to room temperature.
The present invention replaces silicon with aluminum portions makes the massfraction of the silicon in the steel reduce, and the principle that adds or do not add the microalloy element niobium has simultaneously designed the chemical ingredients of novel TRIP steel.When containing Nb in the TRIP steel, the adding of Nb makes the tissue of TRIP steel obtain refinement, and remained austenite content slightly reduces.Along with the increase of Nb content, yield strength and tensile strength raise, yet the Nb too high levels makes when Financial cost increases, increase with Nb content, the size of TRIP steel ferrite grain size and bainite structure reduces, and the bainite amount increases, and elongation and strength and ductility product but reduce.Therefore the content of Nb is controlled within limits (about 0.010～0.020%) better effects if.
The present invention is solving when the too high meeting of silicone content makes that continuously cast bloom toughness is relatively poor, worsens problems such as the hot rolling performance of steel and plating performance, has determined to obtain the composition range of TRIP steel optimum performance.Open cold temperature and coiling temperature by accurate control final rolling temperature, finish rolling deflection, the type of cooling, water-cooled, utilize controlled rolling and controlled cooling method successfully to develop hot rolling TRIP steel plate of new generation, its tensile strength is up to and is 739MPa, breaking elongation is 37.5% to the maximum, strength and ductility product can surpass more than the 25000MPa%, has realized TRIP armor plate strength and the good coupling of plasticity; All below-80 ℃, the normal temperature ballistic work reaches 120J to its brittle transition temperature, shows good impelling strength.
Description of drawings
Fig. 1 is the tension specimen and the impact specimen dimensioned drawing of the hot rolling TRIP steel sheet product in the embodiment of the invention 1, and (A) is the tension specimen dimensioned drawing among the figure, (B) is the impact specimen dimensioned drawing, (C) is (B) side-view.
Fig. 2 is the ballistic work-thetagram of hot rolling TRIP steel plate in the embodiment of the invention, and No.1-2 is a 2# hot rolling TRIP steel plate among the figure, and No.2-2 is a 5# hot rolling TRIP steel plate, and No.3-2 is a 8# hot rolling TRIP steel plate.
Fig. 3 be in the embodiment of the invention 2 5# hot rolling TRIP steel sheet product the impact fracture shape appearance figure, the impact fracture shape appearance figure when (D) is-25 ℃ among the figure, the impact fracture shape appearance figure when (E) being-50 ℃, the impact fracture shape appearance figure when (F) being-110 ℃.
Fig. 4 is the hot rolling TRIP steel sheet product optical microstructure figure in the embodiment of the invention, and (a) and (b), (c), (d), (e), (f), (g), (h) and the optical microstructure that (i) is respectively 1#, 2#, 3#, 4#, 5#, 6#, 7#, 8# and 9# hot rolling TRIP steel plate scheme among the figure.
Fig. 5 is the electron-diffraction diagram before and after the 5# hot rolling TRIP steel sheet product distortion in the embodiment of the invention 2, among the figure (j) for distortion before tissue topography, (k) with (l) for distortion back tissue topography, (m) be martensitic electron diffraction pattern; F among the figure is a ferrite, and B is a bainite, and AR is a residual austenite, and M is a martensite.
Embodiment
The process furnace that adopts in the embodiment of the invention is a 50kW electrically heated box-type furnace.
The milling train that adopts in the embodiment of the invention is the hot rolling unit of φ 450mm * 450mm of designing voluntarily of Northeastern University's rolling technique and tandem rolling automatization National Key Laboratory, maximum rolling force 4000kN, roll speed 0～1.5m/s, main motor current 400kW.
The speed of cooling of the water cooling equipment that adopts in the embodiment of the invention is 5～400 ℃/s.
The measurement of rolled piece surface temperature adopts Japan to produce the portable infrared thermometer of ICON in the embodiment of the invention, and the scope that pyroscope is measured temperature is 600～3000 ℃, and the useful range of low temperature instrument is-50～1000 ℃.
Low-carbon (LC) silicon steel is smelted into steel ingot, and its composition is by weight percentage for containing C0.19%, Mn1.37%, and Si0.68%, Al0.54%, P0.0068%, S0.0068%, surplus is Fe.This steel ingot is heated to 1200 ± 10 ℃, and insulation 1.5hr forges into steel billet.
Adopt the mode of hot charging stove, under 750 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 1hr, insulation finishes the back and is sent in the milling train by rollgang, adopt milling train to carry out roughing and finish rolling, roughing is 3 passages, and start rolling temperature is 1060 ℃, and rolling temperature is 980 ℃ for the second time, rolling temperature is 900 ℃ for the third time, and the roughing total deformation is 47%.
Finish rolling is 2 passages, and final rolling temperature is 870 ℃ for the first time, and finishing temperature is 800 ℃.The finish rolling total deformation is 41%.Obtain rolled piece.
With rolled piece air cooling to 700 ℃, be sent in the water cooling equipment by rollgang, utilize pipe stream water spray cooling rolled piece, by the flow of adjusting water coolant and the group numerical control system water-cooled speed of water cooling equipment is 40～50 ℃/s, adopt reeling machine to batch when water-cooled to 375 ℃, 420 ℃ and 460 ℃ respectively, air cooling obtains 1#, 2# and 3# hot rolling TRIP steel plate to room temperature.
According to GB/T 228-2002 " metallic substance tensile test at room temperature method " this hot rolling TRIP steel plate is processed into tension specimen, concrete size is shown in Fig. 1 (a), tension test is carried out on SANSCMT5000 electric mechanical experimental machine, the crossbeam translational speed is 2.5mm/min, and drawing process is controlled automatically by computer program.According to GB/T229-1994 the TRIP steel has been carried out impact experiment.The thickness of steel band is 3.8mm, and impact specimen adopts the nonstandard sample of V-notch, and concrete size is shown in Fig. 1 (b).Carry out serial impact experiment on the apparent shock-testing machine of JBW-500 screen, sample is incubated in foam plastics container, uses the mercurythermometer thermometric.0 ℃ to-60 ℃ is adopted the dry ice alcohol mixt, is lower than-60 ℃ to-110 ℃ and adopts the liquid nitrogen alcohol mixt, and-190 ℃ are adopted liquid nitrogen to control specimen temperature.Sample is incubated 5min during operation under experimental temperature, takes out the back and thrusts in 3～5s.Every group of 3 samples read and calculate the mean value (A of ballistic work and impelling strength
k), carry out temperature compensation by standard code after, experimental data is depicted as impelling strength-temperature curve and determines the brittle transition temperature of TRIP steel.The mechanical property of steel plate is got the mean value of 3 samples.
Cut sample along rolling direction, the sample that downcuts is polished with sand paper; On mechanical polisher, polish rumbling compound Cr then
2O
3, up to till can not see cut on the metaloscope; It is clean and dry up to wipe away sassafras with the raw spirit cotton balls at last.Adopt 4% nital to carry out etching pit.Etch the back and use alcohol wash rapidly, dry up then.On the multi-functional metaloscope of OLYMPUSGX51 inversion type, observe metallographic structure.Use OLYCIA
TMThe ferritic percent by volume of M3 metallograph picture analysis software measurement, the sample of each technology correspondence is selected 20 visual fields for use, gets its mean value.Impact fracture impact fracture on the SSX550 scanning electron microscope is observed.Cut the 0.3mm thin slice at the metallographic specimen of hot rolling attitude with near the fracture after the tensile deformation, be milled to 0.05mm with sand paper, adopt two spray forensic chemistry attenuates, electrolytic solution is 9% perchloric acid and 91% ethanol.Temperature is controlled between-28～-23 ℃ during attenuate, electric current 45mA, voltage 50V.The tem sample of making carries out the observation and the analysis of microtexture under the TEMCAIG2-20 transmission electron microscope.
Remove with the oxide film of sand paper with the metallographic specimen surface, it is carried out mechanical polishing till no marking, it is clean and dry up to wipe away sassafras with the raw spirit cotton balls.The D/Max-RaX x ray diffractometer x that utilizes Japan of metal institute of the Chinese Academy of Sciences to produce is measured the remained austenite content in the tissue, and wherein ray is Cu target K
αLine, the X ray incident direction is perpendicular to rolling the plate surface.Use the Ni filter plate, step-scan speed is 1/min, and voltage is 56KV, and electric current is 182MA.Calculate respectively (200)
α, (211)
α, (220)
γ(311)
γThe integrated intensity of diffraction peak is by the volume fraction of direct ratio method calculating residual austenite.Carbon content a by formula in the residual austenite
0=0.3578+0.0033C γ determines, wherein C γ be residual austenite carbon content (massfraction, %), a
0Lattice constant (nm) for (220) crystal face.
After carrying out three experiments under the different coiling temperatures, the mechanical property of 1#, 2# and 3# hot rolling TRIP steel plate is as shown in table 1.
Table 1
Wherein ballistic work-the temperature curve of 2#TRIP hot rolling TRIP steel plate as shown in Figure 2.The brittle transition temperature of 1#, 2# and 3# hot rolling TRIP steel plate is all about-80 ℃.
Optical microstructure's structure of 1#, 2# and 3# hot rolling TRIP steel plate is as the (a) and (b) of Fig. 4 with (c).
The tissue volume mark of 1#, 2# and 3# hot rolling TRIP steel plate is as shown in table 2.
Table 2
As can be seen from Table 2, the ferritic volume fraction of 1#, 2# and 3# hot rolling TRIP steel plate is less, and the volume fraction of bainite and residual austenite is more, and the carbon content of residual austenite is also higher.
Embodiment 2
Low-carbon (LC) silicon steel is smelted into steel ingot, and its composition is by weight percentage for containing C0.18%, Mn1.38%, and Si0.67%, Al0.56%, P0.0075%, S0.0048%, Nb0.014%, surplus is Fe.This steel ingot is heated to 1200 ± 10 ℃, and insulation 2hr forges into steel billet.
Adopt the mode of hot charging stove, under 780 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 1.5hr, insulation finishes the back and is sent in the milling train by rollgang, adopt milling train to carry out roughing and finish rolling, roughing is 3 passages, and start rolling temperature is 1080 ℃, and rolling temperature is 1000 ℃ for the second time, rolling temperature is 930 ℃ for the third time, and the roughing total deformation is 45%.
Finish rolling is 2 passages, and final rolling temperature is 850 ℃ for the first time, and finishing temperature is 780 ℃.The finish rolling total deformation is 43%.Obtain rolled piece.
With rolled piece air cooling to 730 ℃, be sent in the water cooling equipment by rollgang, utilize pipe stream water spray cooling rolled piece, by the flow of adjusting water coolant and the group numerical control system water-cooled speed of water cooling equipment is 40～50 ℃/s, adopt reeling machine to batch when water-cooled to 400 ℃, 450 ℃ and 500 ℃ respectively, air cooling obtains 4#, 5# and 6# hot rolling TRIP steel plate to room temperature.
Mechanic property test method is with embodiment 1.The mechanical property of 4#, 5# and 6# hot rolling TRIP steel plate is as shown in table 3.
Table 3
Wherein ballistic work-the temperature curve of 5#TRIP hot rolling TRIP steel plate as shown in Figure 2.The brittle transition temperature of 4#, 5# and 6# hot rolling TRIP steel plate is all about-80 ℃.
Optical microstructure's structure of 4#, 5# and 6# hot rolling TRIP steel plate is as Fig. 4 (d), (e) with (f).
The tissue volume mark of 4#, 5# and 6# hot rolling TRIP steel plate is as shown in table 4.
Table 4
As can be seen from Table 4, the volume fraction of ferritic volume fraction, bainite and the residual austenite of 4#, 5# and 6# hot rolling TRIP steel plate is moderate, and the carbon content of residual austenite is moderate.
The impact fracture pattern of 5#TRIP hot rolling TRIP steel plate when-25 ℃ ,-50 ℃ and-110 ℃ is respectively as Fig. 3 (D) (E) shown in (F).The pattern of impact fracture is corresponding with the value of ballistic work.Fig. 3 (D) is-25 ℃ a fracture apperance, and dimple such as is at axle or parabola shaped, and dimple is darker, size evenly, the HI high impact absorption merit part that it is little for impact absorbing energy changes belongs to tough break; When impact temperature drops to-50 ℃, there is large-area river pattern to occur in the impact fracture photo, also has the tiny dimple band (Fig. 3 (E)) of small area, it is impact absorbing energy variation middle portion greatly, fracture apperance is crystalloid and fibrous mixed fracture, and the TRIP steel changes brittle rupture into from ductile rupture; Further reduction along with temperature, Fig. 3 (F) is-110 ℃ a port pattern, it changes little low impact absorbing energy part for impact absorbing energy, gradually few gradually last disappearance of dimple in the impact fracture, fracture apperance is a crystalloid, be typical brittle rupture fracture, this moment, the TRIP steel became brittle rupture.
TEM before and after the tensile deformation of 5#TRIP hot rolling TRIP steel plate organizes as shown in Figure 5.Wherein Fig. 5 (j) has shown the preceding tissue topography of tensile deformation, wherein little island is organized as residual austenite (AR), Fig. 5 (k) and (l) be tissue topography after the tensile deformation of TRIP steel, wherein the lath-shaped tissue can determine that it is martensite (M) through calculating, and Fig. 5 (m) is the electron diffraction pattern and the demarcation of martensitic stucture.Metallographic structure in conjunction with hot rolling TRIP steel plate, X-ray analysis and tem analysis can determine that hot rolling TRIP steel plate is through behind the controlled rolling and controlled cooling, and tissue mainly contains ferrite, bainite and residual austenite and forms, the carbon of residual austenite obtains enrichment, has guaranteed the stability that residual austenite is certain.After the stretched distortion of hot rolling TRIP steel plate, ferrite and bainite do not change, and have martensite to occur in the tissue, and the tissue after the distortion is mainly ferrite, bainite, residual austenite and martensite.The volume fraction of residual austenite behind the hot rolling TRIP steel plate deformed reduces, fraction of martensite volume increases, and this shows in deformation process, strain-induced residual austenite to martensitic transformation, guaranteed the generation of TRIP steel phase change induction plasticity, i.e. the appearance of TRIP effect.
Embodiment 3
Low-carbon (LC) silicon steel is smelted into steel ingot, and its composition is by weight percentage for containing C0.18%, Mn1.39%, and Si0.66%, Al0.58%, P0.0083%, S0.0050%, Nb0.036%, surplus is Fe.This steel ingot is heated to 1200 ± 10 ℃, and insulation 1.5hr forges into steel billet.
Adopt the mode of hot charging stove, under 800 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 2hr, insulation finishes the back and is sent in the milling train by rollgang, adopt milling train to carry out roughing and finish rolling, roughing is 3 passages, and start rolling temperature is 1120 ℃, and rolling temperature is 1020 ℃ for the second time, rolling temperature is 960 ℃ for the third time, and the roughing total deformation is 43%.
Finish rolling is 2 passages, and final rolling temperature is 820 ℃ for the first time, and finishing temperature is 760 ℃.The finish rolling total deformation is 45%.Obtain rolled piece.
With rolled piece air cooling to 760 ℃, be sent in the water cooling equipment by rollgang, utilize pipe stream water spray cooling rolled piece, by the flow of adjusting water coolant and the group numerical control system water-cooled speed of water cooling equipment is 40～50 ℃/s, adopt reeling machine to batch when water-cooled to 420 ℃, 480 ℃ and 525 ℃ respectively, air cooling obtains 7#, 8# and 9# hot rolling TRIP steel plate to room temperature.
Mechanic property test method is with embodiment 1.The mechanical property of 7#, 8# and 9# hot rolling TRIP steel plate is as shown in table 5.
Table 5
Wherein ballistic work-the temperature curve of 8#TRIP hot rolling TRIP steel plate as shown in Figure 2.The brittle transition temperature of 7#, 8# and 9# hot rolling TRIP steel plate is all about-80 ℃.
Optical microstructure's structure of 7#, 8# and 9# hot rolling TRIP steel plate is as Fig. 4 (g), (h) with (i).
The tissue volume mark of 7#, 8# and 9# hot rolling TRIP steel plate is as shown in table 6.
Table 6
As can be seen from Table 6, the ferritic volume fraction of 7#, 8# and 9# hot rolling TRIP steel plate is less, and the volume fraction of bainite and residual austenite is less, and the carbon content of residual austenite is also lower.
Embodiment 4
Low-carbon (LC) silicon steel is smelted into steel ingot, and its composition is by weight percentage for containing C0.18%, Mn1.38%, and Si0.67%, Al0.56%, P0.0075%, S0.0048%, Nb0.014%, surplus is Fe.This steel ingot is heated to 1200 ± 10 ℃, and insulation 2hr forges into steel billet.
Adopt the mode of hot charging stove, under 750 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 1.5hr, insulation finishes the back and is sent in the milling train by rollgang, adopts milling train to carry out roughing and finish rolling, and roughing is 5 passages, start rolling temperature is 1080 ℃, and the roughing total deformation is 50%.Finish rolling is 2 passages, and finishing temperature is 780 ℃.The finish rolling total deformation is 41%, obtains rolled piece.
With rolled piece air cooling to 730 ℃, be sent in the water cooling equipment by rollgang, utilize pipe stream water spray cooling rolled piece, by the flow of adjusting water coolant and the group numerical control system water-cooled speed of water cooling equipment is 40～50 ℃/s, adopt reeling machine to batch during water-cooled to 450 ℃, air cooling obtains hot rolling TRIP steel plate to room temperature.
Claims (2)
1, a kind of hot-rolling transformation-induced plasticity steel plate: it is characterized in that: the composition of this steel plate is by weight percentage for containing C0.18～0.20%, Mn1.30～1.45%, Si0.60～0.70%, Al0.50～0.60%, P≤0.009%, S≤0.007%, Nb0～0.040%, surplus are Fe, and the yield strength of this hot-rolled steel sheet is not less than 535MPa, tensile strength is not less than 639MPa, and strength and ductility product is greater than 18000MPa%.
2, the preparation method of the described a kind of hot-rolling transformation-induced plasticity steel plate of claim 1, it is characterized in that carrying out (1) according to the following steps smelts into steel ingot with low-carbon (LC) silicon steel, its composition is by weight percentage for containing C0.18～0.20%, Mn1.30～1.45%, Si0.60～0.70%, Al0.50～0.60%, P≤0.009%, S≤0.007%, Nb0～0.040%, surplus is Fe; This steel ingot is heated to 1200 ± 10 ℃, and insulation 1.5～2hr forges into steel billet; (2) under 750～800 ℃ of conditions, steel billet packed in the process furnace, be heated to 1200 ± 10 ℃, insulation 1～2hr, insulation finishes the back and adopts milling train to carry out roughing and finish rolling, start rolling temperature is 1060～1120 ℃, roughing is 3～5 passages, and rolling temperature is 900～1120 ℃, and the roughing total deformation is 40～50%; Finish rolling is 2 passages, and rolling temperature is 760～870 ℃, and the finish rolling total deformation is 40～50%, and finishing temperature is 760～800 ℃, obtains rolled piece; (3) with rolled piece air cooling to 700～760 ℃, quicken cooling with the speed of 40～50 ℃/s again after finish rolling finishes, adopt reeling machine to batch when being cooled to 350～550 ℃, the back air cooling that curls is to room temperature.
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| CN108531811A (en) * | 2018-05-16 | 2018-09-14 | 东北大学 | A kind of preparation method of casting TRIP steel strips |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
| CN110806725A (en) * | 2019-11-07 | 2020-02-18 | 山西太钢不锈钢股份有限公司 | Method and device for processing tensile sample |
| CN115181899A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 980 MPa-grade low-carbon low-alloy TRIP steel and rapid heat treatment manufacturing method thereof |
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2009
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| CN101942601B (en) * | 2010-09-15 | 2012-11-14 | 北京科技大学 | Manufacturing method of transformation induced plasticity steel containing V hot rolling |
| CN101942601A (en) * | 2010-09-15 | 2011-01-12 | 北京科技大学 | Manufacturing method of transformation induced plasticity steel containing V hot rolling |
| CN102140609A (en) * | 2011-01-29 | 2011-08-03 | 首钢总公司 | Composite silicon and aluminum-added 590MPa-level transformation-induced plasticity steel and preparation method |
| CN102952998A (en) * | 2011-08-19 | 2013-03-06 | 鞍钢股份有限公司 | 800 MPa-level hot-rolled phase-change induced plasticity steel plate and manufacturing method thereof |
| CN102952998B (en) * | 2011-08-19 | 2015-05-06 | 鞍钢股份有限公司 | 800 MPa-level hot-rolled phase-change induced plasticity steel plate and manufacturing method thereof |
| CN104169444B (en) * | 2012-03-30 | 2017-03-29 | 奥钢联钢铁有限责任公司 | The method of high strength cold rolled steel plate and this steel plate of production |
| CN104169444A (en) * | 2012-03-30 | 2014-11-26 | 奥钢联钢铁有限责任公司 | High strength cold rolled steel sheet and method of producing such steel sheet |
| CN103143563A (en) * | 2013-04-03 | 2013-06-12 | 河北联合大学 | Method for preventing 65 Mn hot rolled steel coil from collapsing by phase-change thermal expansion |
| CN104233092A (en) * | 2014-09-15 | 2014-12-24 | 首钢总公司 | Hot-rolled TRIP steel and preparation method thereof |
| CN105695851A (en) * | 2016-04-19 | 2016-06-22 | 常州市蓝勖化工有限公司 | Method for decreasing silicon content of transformation induced plasticity (TRIP) steel during phase transformation process |
| CN106521335A (en) * | 2016-10-28 | 2017-03-22 | 东北大学 | High tensile strength and elongation TRIP steel bar material and equa-channel angular pressing preparation method |
| CN106521335B (en) * | 2016-10-28 | 2018-01-19 | 东北大学 | A kind of high strength and ductility TRIP Steel Bars and equal channel corner extrusion preparation method |
| CN108531811A (en) * | 2018-05-16 | 2018-09-14 | 东北大学 | A kind of preparation method of casting TRIP steel strips |
| CN108531811B (en) * | 2018-05-16 | 2020-05-01 | 东北大学 | Preparation method of cast-rolled TRIP steel thin strip |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
| CN110806725A (en) * | 2019-11-07 | 2020-02-18 | 山西太钢不锈钢股份有限公司 | Method and device for processing tensile sample |
| CN115181899A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 980 MPa-grade low-carbon low-alloy TRIP steel and rapid heat treatment manufacturing method thereof |
| CN115181899B (en) * | 2021-04-02 | 2023-07-07 | 宝山钢铁股份有限公司 | 980 MPa-level low-carbon low-alloy TRIP steel and rapid heat treatment manufacturing method thereof |
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