CN102965568B - Phase toughness Low Alloy Steel Plate and preparation method thereof - Google Patents
Phase toughness Low Alloy Steel Plate and preparation method thereof Download PDFInfo
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Abstract
A kind of phase toughness Low Alloy Steel Plate and preparation method thereof, belongs to technical field of alloy steel.Chemical composition is: C:0.04 ~ 0.12wt.%, Si:0.10 ~ 0.50wt.%, Mn:2.6 ~ 3.8wt.%, P:< 0.02wt.%, S:< 0.01wt.%; On this basis, one or more alloying elements following can be added: Cr:0 ~ 0.50wt.%, Ni:0 ~ 1.0wt.%, Mo:0 ~ 0.50wt.%, Cu:0 ~ 0.60wt.%, Nb:0 ~ 0.05wt.%, V:0 ~ 0.15wt.%; Ti:0 ~ 0.12wt.%, B:0 ~ 0.003wt.%, Al:0.01 ~ 0.06wt.%, the total addition level of steel interalloy element is not more than 5%.Advantage is, adopts the cheap elements such as C, Mn as main alloy element, is obtained the metastable austenite phase of Dispersed precipitate, can significantly improve the low-temperature flexibility of steel by C, Mn bis-partition techniques in martensite.Compared with containing Ni low-temperature steel with tradition, low-cost advantage is obvious, can be applied to the fields such as low-temperature (low temperature) vessel, oceanographic engineering, engineering machinery.<!--1-->
Description
Technical field
The invention belongs to technical field of alloy steel, in particular, provide a kind of phase toughness Low Alloy Steel Plate and preparation method thereof.
Background technology
Along with socioeconomic development, the demand of high-strength and high-toughness steel is increasing.The technical way of current raising steel obdurability is structure refinement, but simple structure refinement also can make that the uniform plastic of steel reduces while raising obdurability, yield tensile ratio increase, is difficult to meet the service safety requirement under high intensified condition comprehensively; On the other hand, when structure refinement to a certain extent time (effective particle size is about 5 microns), the difficulty of further refinement enlarges markedly, more and more harsher to the requirement of processing condition, as large in needs low temperature pressure distortion etc., and this is difficult to realize for the larger steel of some specification.Therefore, tissue modulation principle and the process means of other raising steel obdurability except structure refinement is needed to explore.Existing research work shows, metastable austenite appropriate in steel has vital role for the toughness improving steel, its principle is that metastable austenite, under the stress field effect of crackle forward position, martensitic transformation occurs, this phase transformation will alleviate the stress concentration in crackle forward position, improve crack growth resistance, thus significantly reduce the ductile-brittle transition temperature of steel, improve the low-temperature flexibility of steel.Utilize this principle, Japan successfully develops steel used at ultra-low temperature-9Ni steel and production technique thereof at the end of the sixties in last century.From the end of the seventies in last century, the J.W.Morris of California, USA Berkeley university teaches the feasibility of study group's systematic study 5Ni steel replacement 9Ni steel, and explore the feasibility of 5Mn steel replacement 5Ni steel further, have extensively studied the toughness reinforcing principle of metastable austenite on this basis (see document: J.W.Morris, Jr., Z.Guo, C.R.KrennandY.-H.Kim.TheLimitsofStrengthandToughnessinSt eel.ISIJInternational, Vol.41 (2001), No.6, pp.599-611.).Use for reference the title of " transformation plasticity (TransformationInducedPlasticity; the TRIP) steel " widely applied in automotive industry, be called toughness reinforcing for above-mentioned metastable austenite steel " phase toughness (TransformationInducedToughening) steel " here.It should be noted that, the research work of current phase toughness steel mainly concentrates on the high interalloy of a few ni content or high quality steel, as 9Ni steel, 5Ni steel and maraging steel etc., and because the alloying cost of steel is high, complex manufacturing, their application is only confined to some specific area, as low-temperature (low temperature) vessel, undercarriage etc., be difficult to apply in other field.Therefore, phase toughness low alloy steel is significant for the upgrading promoting low alloy steel more widely for the cheap and Application Areas of cost of development.
Summary of the invention
The object of the present invention is to provide a kind of phase toughness low alloy steel and steel plate preparation method thereof, adopt the austenite stabilizer element such as cheap C and Mn as main alloy element, secondary isothermal process is carried out under differing temps within the scope of (γ+α) two-phase region of steel, there is C, Mn element in isothermal and diffuse to " partition " process γ phase from α matrix, the metastable austenite phase of final acquisition some amount Dispersed precipitate in the base, thus increase substantially the low-temperature flexibility of steel.
Chemical composition and the content of phase toughness low alloy steel provided by the invention are: C:0.04 ~ 0.12wt.%, Si:0.10 ~ 0.50wt.%, Mn:2.6 ~ 3.8wt.%, P:< 0.02wt.%, S:< 0.01wt.%, and surplus is Fe and inevitable impurity; On this basis, can add one or more alloying elements following in addition: Cr:0 ~ 0.50wt.%, Ni:0 ~ 1.0wt.%, Mo:0 ~ 0.50wt.%, Cu:0 ~ 0.60wt.%, Nb:0 ~ 0.05wt.%, V:0 ~ 0.15wt.%, Ti:0 ~ 0.12wt.%, B:0 ~ 0.003wt.%, Al:0.01 ~ 0.06wt.%, the total addition level of steel interalloy element should be not more than 5%.
The effect of each element of the present invention and proportioning are according to as follows:
Carbon: carbon is austenite stabilizer element, during (γ+α) two-phase region isothermal, it will be enriched in austenite, improve stabilization of austenite, be conducive to the final acquisition of metastable austenite; In addition, carbon also significantly improves hardening capacity and the intensity of steel.The carbon content scope of steel of the present invention is 0.04 ~ 0.12wt.%, and carbon content is lower than 0.04wt.%, and the metastable austenite quantity obtained is very few, is difficult to play phase toughness effect; Higher than 0.12wt.%, then may there is cementite in carbon content, unfavorable to toughness.
Silicon: one of deoxidant element in steel, has stronger solution strengthening effect simultaneously, but excessive Si will worsen toughness and the welding property of steel.Comprehensive above-mentioned consideration, the silicone content scope of steel of the present invention is 0.1 ~ 0.50wt.%.
Manganese: manganese is the key alloying elements that steel of the present invention obtains metastable austenite.Identical with carbon effect, manganese is also austenite stabilizer element, will enrichment in austenite when (γ+α) two-phase region isothermal, improves stabilization of austenite, is conducive to finally obtaining metastable austenite; In addition, manganese significantly improves the hardening capacity of steel, has certain solution strengthening effect simultaneously.The Fe content scope of steel of the present invention is 2.6 ~ 3.8.wt.%, and Fe content is lower than 2.6wt.%, and the metastable austenite quantity obtained is few, is difficult to play phase toughness effect; Fe content is higher than 3.8wt.%, then strand heart portion quality obviously reduces, and plate property worsens.
Molybdenum: the hardening capacity significantly improving steel, reduces temper brittleness, improves the resistance for delayed fracture of steel.Also can improve the high temperature dimensional stability of microalloy precipitated phase when Mo and microalloy element add jointly, reduce its alligatoring speed, be conducive to improving precipitation hardening effect.When molybdenum content is more than 0.50wt.%, above-mentioned action effect reaches capacity, and cost is higher.Therefore, steel molybdenum content of the present invention should control within 0.50wt.%.
Chromium: the hardening capacity and the atmospheric corrosion resistance that improve steel, but higher Cr content is unfavorable to welding property, should control within 0.50wt.%.
Nickel: nickel is austenite stabilizer element, when (γ+α) two-phase region isothermal, it will enrichment in austenite, improves stabilization of austenite, is conducive to finally obtaining metastable austenite; In addition, nickel improves hardening capacity and the atmospheric corrosion resistance of steel, but its price is high, should control within 1.0wt.%.
Copper: the hardening capacity and the atmospheric corrosion resistance that improve steel, the nano level Cu phase particle of Precipitation has certain precipitation strength effect, but is easy to produce hot-short problem due to surperficial selective oxidation containing Cu steel.Therefore Cu content controls within 0.60wt.%.
Boron: strong segregation is in austenite grain boundary and other lattice defect place, add micro-B and can significantly improve hardening capacity, but above-mentioned effect is saturated afterwards more than 0.003% for Boron contents, but also may be formed various to hot workability and toughness disadvantageous containing B precipitated phase, therefore Boron contents should control within 0.003wt.%.
Niobium: the effect organized after there is stronger refinement phase transformation.By solid solution Nb and deformation-induced precipitation Nb (C, N), strongly inhibited effect is produced to austenite recrystallization, thus obtain the non-recrystallization austenite with higher defect concentration, improve follow-up Nucleation rate and organize after refinement phase transformation.In addition, be solid-solution in Nb in austenite and improve hardening capacity successful.Steel content of niobium of the present invention is within 0.05wt.%, and higher than 0.05wt.%, it organizes further thinning effect to become not obvious and cost raising.
Vanadium: the VC particle dispersion of Precipitation is tiny from martensite or ferrite matrix, has significant precipitation strength effect.Steel V content of the present invention controls within 0.15%, and too high then precipitation strength effect improves not obvious, and cost is higher.
Titanium: when adding trace Ti in steel (Ti content is less than 0.04wt.%), Ti is mainly combined with N, Precipitation from solid steel, form the TiN particle of nano-grade size, its Main Function is austenite grain size in refinement 2 Mo Steel Slab during Heating Process; When Ti content is greater than 0.04wt.%, except forming TiN (at this moment part TiN also will separate out from molten steel), residue Ti will be combined with C and form TiC particle, and it has stronger precipitation hardening effect.Steel Ti content of the present invention should control within 0.12wt.%, and adding its precipitation strength effect of too much Ti increases not obvious, and macrobead liquation TiN increasing number, the toughness plasticity of grievous injury steel.
Aluminium: aluminium is strong deoxidant element, also can be combined with N and form AlN, can play Grain refinement.The aluminium content range of steel of the present invention is 0.01 ~ 0.06wt.%.
P and s: impurity element in steel, significantly reduce plasticity and toughness and welding property, its content should control within 0.02wt.% and 0.01wt.% respectively.
Phase toughness Low Alloy Steel Plate manufacturing process involved in the present invention is as follows:
Adopt converter or electrosmelting, casting adopts continuous casting or die casting.
Heat in process furnace after continuously cast bloom or ingot formation, Heating temperature is 1100 ~ 1250 DEG C, time is 1-5 hour, plate mill is adopted to be rolled after heating, rolling technology is: roughing rolling 3-8 passage, finish rolling rolling 5-14 passage, finishing temperature is 750 ~ 950 DEG C, rolls rear direct quenching (DQ) and obtains martensitic stucture or air cooling (AC) to room temperature.
Steel plate hot process, this is the critical process that steel of the present invention obtains excellent low temperature toughness.For DQ steel plate, thermal treatment process comprises intercritical annealing (L) and tempering (T) two procedures, both all carry out in (γ+α) two-phase region, namely Heating temperature higher than Ar1 lower than Ar3, difference is that L operation is carried out under the comparatively high temps of two-phase region, corresponding austenite volume fraction is 50%-70%, and T operation is carried out under the lesser temps of two-phase region, and corresponding austenite volume fraction is 8%-20%.Concrete technology parameter is: intercritical annealing Heating temperature is 720 ~ 780 DEG C, and soaking time is 0.5-2 hour, shrend after steel plate heating.Tempering temperature is 620 ~ 680 DEG C, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after tempering.
For rolling rear air cooling steel plate, because its original structure is not martensite, needing before intercritical annealing, add primary quenching operation, namely adopting QLT technique.Quenching temperature is higher than the Ar3 temperature of steel, after guaranteeing complete austenitizing and quenching, obtain complete martensitic stucture.Concrete technology parameter is as follows: quenching (Q) Heating temperature is 800 ~ 880 DEG C, and soaking time is 0.5-2 hour, shrend after heating; Intercritical annealing Heating temperature is 720 ~ 780 DEG C, and soaking time is 0.5-2 hour, shrend after steel plate heating; Tempering temperature is 620 ~ 680 DEG C, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after tempering.Fig. 1 is Heat Treatment Of Steel process schematic representation of the present invention.
The technology controlling and process principle of phase toughness low alloy steel involved in the present invention is:
The main purpose that steel of the present invention is heat-treated is the metastable austenite phase obtaining Dispersed precipitate in martensitic matrix and have high thermal stability, thus improves the low-temperature flexibility of steel.The effect of DQ or Q obtains martensitic stucture, and martensite lath block (Block) size that usual DQ technique obtains is more tiny than Q technique, is thus conducive to obdurability and improves.In intercritical annealing process (L) subsequently, partial martensite lath changes austenite into, and partition occurs the austenite stabilizer element such as C, Mn between martensite and austenite, causes C, Mn content in austenite to increase gradually.In shrend process after annealing, above-mentioned austenite changes martensite into again, but new C, Mn constituent content that to be formed in martensite is higher than matrix martensite.And for the micro-alloyed steel containing microalloy elements such as Nb, V, Ti, also can there is microalloy carbonitride in intercritical annealing heat-processed from the Precipitation martensitic matrix, it is of a size of nano level, can provide obvious precipitation strength effect.In drawing process, the new martensite that formed of part will change austenite into again, between austenite and martensite, there is the second time partition of C, Mn element simultaneously, make the rich Mn of the richer C of austenite, its thermostability significantly improves, and when cooling after tempering, these austenites no longer undergo phase transition and remain.
The invention has the advantages that:
Adopt the cheap elements such as C, Mn as main alloy element, in martensite, obtained the metastable austenite phase of Dispersed precipitate by secondary partition technique, the low-temperature flexibility of steel can be significantly improved; Meanwhile, metastable austenite causes fracture property also have certain effect relative to improving the plasticity of steel, fatigue property and resistant to hydrogen.
Plate mill is adopted to be rolled into steel plate, critical zone thermal treatment process is adopted to heat-treat again, steel plate has the cooperation of excellent intensity, toughness and plasticity: yield strength is that-100 DEG C of ballistic works of 500MPa level steel plate can reach more than 200J, unit elongation is about 34%, and the product (strength and ductility product) of tensile strength and unit elongation is more than 20GPa%; Yield strength 750MPa level steel plate-100 DEG C of ballistic works are more than 100J, and unit elongation is 23%.
Compared with containing Ni low-temperature steel with tradition, the low-cost advantage of steel of the present invention is obvious, can be applied to the fields such as low-temperature (low temperature) vessel, oceanographic engineering, engineering machinery.
Accompanying drawing explanation
Fig. 1 is steel plate hot rolling process schematic representation of the present invention.
Fig. 2 is steel plate heat treatment process schematic diagram of the present invention.
Fig. 3 is the XRD figure spectrum of 2# steel.
Fig. 4 is the XRD figure spectrum of 4# steel.
Fig. 5 is 2# transmission electron microscope bright field image, shows pattern and the distribution of metastable austenite.
Fig. 6 is 4# steel transmission electron microscope dark field image, shows pattern and the distribution of metastable austenite and precipitated phase.
Fig. 7 is 4# steel transmission electron microscope bright field image, shows the pattern of precipitated phase.
Embodiment
Steel of the present invention is smelted by laboratory vacuum induction furnace, totally 5 stoves, wherein 3 stoves are C-Mn-Nb micro-alloyed steel (1#, 2#, 3#), and 2 stoves are add appropriate Ti and Mo again on C-Mn-Nb component base, object is improved the intensity of steel further.Concrete chemical composition is as shown in table 1.Above-mentioned steel ingot casting is become 50kg billet, then hammer cogging, is swaged into and is of a size of 50mm(thickness) * 60mm(width) * 80mm(length) steel billet.By above-mentioned steel billet after 1200 DEG C of insulation 2h, roll into through laboratory reversable mill the steel plate that thickness is 11mm.Adopt two-phase control rolling technique, roughing finishing temperature is 1020 DEG C, and rolling 2 passage, is compressed to 36mm from thickness 50mm; Finish rolling start rolling temperature is 920 DEG C, and finishing temperature is 850 DEG C, rolling 5 passage.Roll rear water-cooled to room temperature, obtain martensitic stucture.
Thermal treatment process is: after steel plate is incubated 1 hour at 750 DEG C, (L) completes the first time partition of C, Mn element in the process, after insulation, shrend is to room temperature, then steel plate was 650 DEG C of tempering 1 hour, completed the second time partition of C, Mn element, was cooled to room temperature after tempering.
Table 1 steel chemical composition of the present invention (wt.%), surplus is Fe
Determine summer under the tensile property of steel plate after thermal treatment and differing temps than v-notch ballistic work, result is as shown in table 2.From table, steel of the present invention shows the cooperation of excellent intensity, toughness and plasticity.For C-Mn-Nb component steel, its yield strength is about 500MPa, and-100 DEG C of ballistic works can reach more than 200J, and unit elongation is more than 30%, and the product (strength and ductility product) of tensile strength and unit elongation, more than 20GPa%, reaches TRIP Steel Properties level.It can also be seen that in addition, improving carbon content can damage toughness to a certain extent.For C-Mn-Nb-Mo-Ti component steel, due to the precipitation strength effect of (Ti, Mo) C particle, yield strength brings up to more than 750MPa, and-100 DEG C of ballistic works are still higher simultaneously, more than 100J.
The tensile property of table 2 steel of the present invention and differing temps lower summer are than v-notch ballistic work
Adopt X-ray diffraction to survey the XRD figure spectrum of 2# steel and 4# steel, as shown in Figures 2 and 3, occurred the diffraction peak of austenite phase in visible diffraction spectrum, quantitative analysis shows that its austenitic volume fraction is respectively 8.77% and 13.50% to result.Fig. 4 is the transmission electron microscope bright field image of 2# steel, and part metastable austenite marks with " A ", and visible austenite is sheet, and be distributed between former martensite lath, its thickness is approximately 0.1-0.2 micron; In addition, former martensite its dislocation desity after the thermal treatment of critical zone obviously reduces, but still substantially remains panel construction.Fig. 5 is the transmission electron microscope dark field image of 4# steel, and wherein metastable austenite is shown as light tone mutually, and its shape is similar to 2# steel to distribution characteristics.Can also see the precipitated phase of a large amount of Dispersed precipitate in addition, its size is about 10nm, and they are microalloy carbonitrides of Precipitation from martensitic matrix in intercritical annealing process.Fig. 6 gives 4# steel transmission electron microscope bright field image, show further the shape characteristic of nano level precipitated phase.
Claims (2)
1. a phase toughness Low Alloy Steel Plate, it is characterized in that, adopt converter or electrosmelting, in steel plate, the weight percentage of each composition is: C:0.04 ~ 0.12wt.%, Si:0.10 ~ 0.50wt.%, Mn:2.6 ~ 3.49wt.%, P:< 0.02wt.%, S:< 0.01wt.%; On the basis of mentioned component, then add one or more alloying elements following: Cr:0 ~ 0.50wt.%, Ni:0 ~ 1.0wt.%, Mo:0 ~ 0.50wt.%; Cu:0 ~ 0.60wt.%, Nb:0 ~ 0.05wt.%, V:0 ~ 0.15wt.%; Ti:0 ~ 0.12wt.%, B:0 ~ 0.003wt.%, Al:0.01 ~ 0.06wt.%, the total addition level of alloying element should be not more than 5%; Surplus is Fe and inevitable impurity; Be weight percentage;
Based on above-mentioned alloying constituent, plate mill is adopted to be rolled into steel plate, critical zone thermal treatment process is adopted to heat-treat again, steel plate has the cooperation of excellent intensity, toughness and plasticity: yield strength is that-100 DEG C of ballistic works of 500MPa level steel plate can reach more than 200J, unit elongation is 34%, and the product of tensile strength and unit elongation is more than 20GPa%; Yield strength 750MPa level steel plate-100 DEG C of ballistic works are more than 100J, and unit elongation is 23%.
2. a manufacture method for phase toughness Low Alloy Steel Plate described in claim 1, is characterized in that:
(1) heat loading in process furnace after continuously cast bloom or ingot formation, Heating temperature is 1100-1250 DEG C, and the time is 1-5 hour, is rolled after heating;
(2) plate mill rolling
Plate mill rolling technology is: roughing rolling 3-8 passage, finish rolling rolling 5-14 passage, and finishing temperature is 750-950 DEG C, rolls rear direct quenching DQ and obtains martensitic stucture or air cooling AC to room temperature;
(3) steel plate hot process
For DQ steel plate, thermal treatment process comprises intercritical annealing L and tempering T two procedures, and wherein intercritical annealing Heating temperature is 720 ~ 780 DEG C, and soaking time is 0.5-2 hour, shrend after steel plate heating;
Tempering temperature is 620 ~ 680 DEG C, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after tempering;
For rolling rear air cooling steel plate, need before intercritical annealing, add primary quenching operation, namely adopt QLT technique, concrete technology parameter is as follows: quenching Q Heating temperature is 800 ~ 880 DEG C, and soaking time is 0.5-2 hour, shrend after heating; Intercritical annealing Heating temperature is 720 ~ 780 DEG C, and soaking time is 0.5-2 hour, shrend after steel plate heating; Tempering temperature is 620 ~ 680 DEG C, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after tempering.
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| CN103710622A (en) * | 2013-12-20 | 2014-04-09 | 钢铁研究总院 | 690MPa-yield-strength low-yield-tensile-ratio antiseismic steel and manufacturing method thereof |
| CN104120349A (en) * | 2014-07-23 | 2014-10-29 | 舞阳钢铁有限责任公司 | F-grade large-thickness weldable steel plate with high pureness and high low-temperature toughness and production method thereof |
| CN104195470B (en) * | 2014-07-29 | 2016-09-28 | 锐展(铜陵)科技有限公司 | A kind of alloy steel for automobile wheel hub and manufacturing process thereof |
| CN105422590A (en) * | 2015-11-18 | 2016-03-23 | 宁波金鹏高强度紧固件有限公司 | Nut plate |
| 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 |
| CN108385037B (en) * | 2018-03-23 | 2020-05-19 | 东北大学 | Ti microalloyed medium manganese steel medium plate for ocean platform and preparation method thereof |
| CN109609848B (en) * | 2018-12-24 | 2020-05-26 | 钢铁研究总院 | High-toughness anti-fatigue nano-precipitate reinforced martensite-austenite composite steel and preparation method thereof |
| CN111041165B (en) * | 2019-12-26 | 2021-06-29 | 钢铁研究总院 | Medium manganese oil well pipe steel and preparation method thereof |
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