CN106086647B - A kind of low-alloy high-strength steel Q460C and its production method - Google Patents

A kind of low-alloy high-strength steel Q460C and its production method Download PDF

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CN106086647B
CN106086647B CN201610548906.6A CN201610548906A CN106086647B CN 106086647 B CN106086647 B CN 106086647B CN 201610548906 A CN201610548906 A CN 201610548906A CN 106086647 B CN106086647 B CN 106086647B
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steel
temperature
control
rolling
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CN106086647A (en
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贾国生
杨雄
范佳
成慧梅
郝宾宾
马有辉
姚宙
李朝辉
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Hebei Iron And Steel Co Ltd Handan Branch
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Abstract

A kind of low-alloy high-strength steel Q460C and its production method, the weight/mass percentage composition of each element is respectively in steel：C：0.11~0.15, Si：0.20~0.40, Mn：1.30~1.50, Nb：0.01~0.02, Ti：0.050~0.070, Als：0.020~0.040；Slab heating time >=3.5h, 1100~1190 DEG C of heating end of a period moment temperature；Rolled using CR modes, more than 3 times that treat that temperature thickness is steel plate finished product thickness during open rolling, finish rolling adds up reduction ratio >=66%, 810~850 DEG C of finishing temperature；Using the ACC types of cooling, steel plate final cooling temperature is 630 ± 20 DEG C.The present invention uses the high Ti microalloys component systems of low Nb, and toughness is not reduced on the premise of proof strength, optimizes temperature-controlled rolling and ACC Controlled cooling process, obtains preferable F+P tissues, and low production cost.

Description

A kind of low-alloy high-strength steel Q460C and its production method
Technical field
The present invention relates to a kind of high-strength steel and its production method, more particularly to a kind of low-alloy high-strength steel Q460C and its life Production method.
Background technology
Q460C is a kind of middle high intensity levels steel grade, is mainly used in the engineering machinery fields such as Coal Mechanical hydraulic support. At present, market is concentrated mainly on the middle panel products that thickness specification is 12~16mm, accounts for Q460C aggregate demands to Q460C demand More than 75%.According to investigation, domestic many steel mills have all possessed the ability for producing the steel grade relevant thickness specification, but these steel To ensure Q460C mechanical property, i.e., factory owner will employ the high V- of high Nb- low Ti or the high V of high Nb- composition design mode： Nb elements are normally controlled in the range of 0.03wt%~0.06wt% in steel, and V element is controlled in 0.025wt%~0.25wt% models In enclosing, Ti control of element is in 0.007wt%~0.03wt%；It is mainly based upon using this composition design mode：First, it is theoretical On, carbon, the nitridation precipitate of Nb, V, Ti element can play crystal grain in refinement steel, improve the effect of steel grade mechanical property, but From practical application effect, Nb grain refining capability is most strong, and V, Ti grain refining capability are suitable；Secondly, V control is cold Validity is best, and secondly, and Ti is poor by Nb；3rd, from alloying difficulty, because Ti ten divides vivaciously, easily with steel The element such as C, O, S react, therefore during smelting molten steel, effective control of Ti element recovery rates will be difficult to Nb, V member Element.Although this composition design mode disclosure satisfy that mechanical property requirements of the GB/T1591-2009 to Q460C, but still exist Following some problems：
(1), production cost is higher：It is well known that Nb, V, Ti are the microalloy elements of current main lift properties of product, But Nb is added into steel, the production cost of V element will be far above the production cost that Ti elements are added into steel；According to statistics, in steel Nb contents often increase 0.01wt%, then production cost will increase by 28~30 yuan/ton of steel；V content often increases 0.01wt%, production Cost will increase by 9~11 yuan/ton of steel；And the Ti contents in steel often increase 0.01wt%, production cost will only 2~4 yuan/ton of increase Steel.Therefore, Nb is relied primarily on, the production cost of method of V element lifting Q460C mechanical properties is higher than and relies primarily on Ti elements Lift the production cost of the method for Q460C mechanical properties.
(2), casting billet surface is more prone to transverse crack and transverse corner crack defect：Transverse crack, angle are horizontal caused by casting billet surface The High Temperature Ductility of crackle and steel grade is closely related, the High Temperature Ductility of the steel grade under a certain temperature range can it is poorer or compared with Temperature range corresponding to the High Temperature Ductility energy of difference is bigger, then corresponding casting billet surface more easily crack, angle it is horizontal Crack defect；Conversely, High Temperature Ductility of the steel grade under a certain temperature range can be stronger or poor High Temperature Ductility energy Corresponding temperature range is narrower, then corresponding casting billet surface be just less susceptible to crack, transverse corner crack defect.Experiment knot Fruit shows：After the Nb constituent contents in steel reach more than 0.02wt%, easily cause the III brittle temperature zone of steel more common Steel is significantly more to high temperature Directional Extension, it is easier to reduces the High Temperature Ductility of steel；Because the nitride and carbon of Nb elements After nitride separates out from steel at high temperature, its small precipitation particles can be attached to the γ crystal boundaries of steel, and each particle periphery Stress raisers can be produced, so as to promote γ Grain Boundary Slidings, cause intercrystalline failure；Further, since stress concentration phenomenon, can lead Cause to produce cavity around the Nb compound particles near crystal boundary, and cavity polymerization development can cause to prolong the cracking of metallic grain boundaries.Examination Result is tested also to show：V nitride and carbonitride can be distributed on austenite grain boundary during slab cooling, so that can be right Q460C High Temperature Ductility causes stronger deterioration to act on.In addition, the V element in steel is also easy to the III fragility temperature for causing steel Area is spent compared with ordinary steel significantly more to low temperature Directional Extension.Therefore the III of steel can be made if containing higher Nb and V in steel Brittle temperature range substantially broadens, so that casting billet surface produces transverse crack, the increased risk of transverse corner crack.
The content of the invention
The technical problems to be solved by the invention are to provide a kind of low-alloy high-strength steel Q460C and its production method, are having While effect ensures that finished product mechanical property meets GB/T1591-2009 requirement, production cost is greatly reduced；Solves the back of the body simultaneously The cold validity of Ti elements control is poor in scape technology, smelts the uppity technical problem of recovery rate.
Solve above-mentioned technical problem technical scheme be：
A kind of low-alloy high-strength steel Q460C, the weight/mass percentage composition of each element is respectively in steel：C：0.11~0.15, Si： 0.20~0.40, Mn：1.30~1.50, Nb：0.01~0.02, Ti：0.050~0.070, Als：0.020~0.040.
A kind of low-alloy high-strength steel Q460C production method, the weight/mass percentage composition difference of each element in the Q460C steel For：C：0.11~0.15, Si：0.20~0.40, Mn：1.30~1.50, Nb：0.01~0.02, Ti：0.050~0.070, Als：0.020~0.040.
A kind of above-mentioned low-alloy high-strength steel Q460C production method, using molten iron pre-desulfurization, converter smelting, LF refining, Continuous casting, heating stove heat, controlled rolling, ACC cooling technique steps, wherein：
Heat time >=3.5h of the slab in heating furnace, the surface temperature control at heating end of a period moment is 1100~1190 In the range of DEG C；
Rolled in controlled rolling technique using CR modes, start rolling temperature is 930~1020 DEG C；One stage finishing temperature ＞ 980℃；Two-stage start rolling temperature≤920 DEG C, more than 3 times that treat that temperature thickness is steel plate finished product thickness during open rolling, finish rolling adds up Reduction ratio >=66%, finishing temperature control is in the range of 810~850 DEG C；
Controlled and cooled down using the ACC types of cooling, the final cooling temperature of steel plate is 630 ± 20 DEG C.
A kind of above-mentioned low-alloy high-strength steel Q460C production method, the O in steel is controlled to contain in the converter smelting process Measure in below 600ppm, it is less than the 0.01% of molten steel amount to control the lower quantity of slag of tapping, it is ensured that the cleanliness factor of molten steel；
In more than 35min, refining terminates preceding 10~15min and adds ferrotianium to carry out micro- conjunction for refining time control in LF refining technique Aurification, effectively steel inclusion rank summation is controlled to be no more than 1.5 grades；
The control of molten steel overtemperature is in the range of 10~35 DEG C in continuous casting process, and pulling rate whole-process control is in 0.8~1.0m/ In the range of min；The offline stacking slow cooling processing of strand.
The present invention is based primarily upon considered below using the high Ti of low Nb- composition design thinking：
First, using the high Ti of low Nb- composition design thinking, two kinds of elements pair of Nb, Ti can be played to greatest extent Q460C mechanical property castering action, it is ensured that Q460C mechanical property meets GB/T1591-2009 requirement；
Secondly, using the high Ti composition designs of low Nb-, Q460C production cost can effectively be reduced；
3rd, using the high Ti composition designs of low Nb-, without adding V element, it can effectively reduce the production of Q460C casting billet surfaces Raw transverse crack, the risk of transverse corner crack defect, because, in steel Ti containing high level different from Nb, V microalloy element The High Temperature Ductility energy of steel can be improved：A, Ti and N has strong affinity, and TiN can be under the solidus temperature of slightly below steel Generation, thus size is thicker, can in steel random distribution, and Nb nitride and carbonitride size are compared with TiN more refinements It is small, so as to which larger harm can be caused to the High Temperature Ductility of steel；B, the TiN amount of precipitations generated during high temperature are more, and TiN is separated out in steel The volume fraction of thing is high, and crystal grain is grown up when can suppress high temperature, improves the High Temperature Ductility of steel, simultaneously as size is thicker Greatly, the nitride with tiny Nb, compared with carbonitride, TiN pinnings crystal boundary can only maintain the very short time, the one of casting billet surface Crackle has little time to assemble slightly, new intra-die will be wrapped in by crystal boundary migration by growing up；C, the thick TiN generated during high temperature Can be as the core of the precipitates such as Nb nitride, carbonitride, the precipitate such as Nb nitride, carbonitride is attached to The upper forming cores of TiN are grown up, and are reduced so as to significantly reduce the precipitates such as the nitride for the small Nb that can be generated originally, carbonitride The effect of the High Temperature Ductility of steel；D, the N in steel preferentially can be reacted with Ti, so as to reduce the N with the element reaction such as Nb The precipitate growing amount such as amount, small Nb nitride, carbonitride is reduced therewith, so as to improve the High Temperature Ductility of steel Energy；Result of study shows：As the Ti that more than 0.02% is added in steel, the III brittle temperature range of steel can be obviously reduced, steel RA values bring up to more than 60% by 30%；E, higher Ti contents are remarkably improved Q460C transverse impact toughness, this be because For：Ti and S affinity is better than Mn and S affinity；Thus with the increase of Ti contents in steel, the Ti in steel4C2S2Chemical combination Thing, which gradually increases and instead of MnS, to be mingled with, i.e. the addition of Ti has been captured the S in MnS and generated therewith more stable Ti4C2S2, so as to reduce MnS precipitation, alleviate the enrichment that MnS is mixed in strand central area；Because MnS is mixed in casting The enrichment of base central area be produce strand segregation the main reason for, and strand segregation be reduction impact flexibility it is main because Element, so the reduction of MnS amount of precipitations can obviously reduce the possibility for producing center segregation, and harder Ti4C2S2Compound is being rolled Process processed is unlikely to deform, and is in spherical, so as to improve Q460C transverse impact toughness.
The control of Nb elements of the present invention and Ti additions is based primarily upon following principle：
Nb：The element has extremely strong affinity in steel with nitrogen, carbon, can form stable Nb (C, N) therewith and (refer to Nb's Carbide and carbonitride) compound, induce and separate out during controlled rolling, along austenite grain boundary Dispersed precipitate, Ke Yizuo For the equiax crystal of phase transformation, so as to fining ferrite grains；In this steel grade, Nb effect is mainly crystal grain thinning.Producing Find in practice, the thickness segregation position of the unqualified steel plate of elongation percentage has free simple substance Nb, and can deteriorate the property of steel plate Can, while when Nb contents are more than 0.02wt%, easily casting billet surface is cracked defect, influence finish to gauge product quality, therefore, Nb contents are designed as 0.01wt%~0.02wt% by the present invention.
Ti：Ti addition can reduce cracks influence caused by Nb elements, and form resistant to elevated temperatures particle with C, N element and follow closely Prick in original austenite crystal boundary, prevent growing up for original grain, and improve the welding performance of steel plate.Research shows, works as Ti content During≤0.02wt%, intensity increase unobvious, the precipitation hardening effect very little of titanium；Ti content be 0.02wt%~ During 0.04wt%, because separating out stable TiN, Austenite Grain Growth is effectively prevented, Ferrite Grain Size can be by 14.8um 8.5um, and TiC precipitation strength effect are down to, yield strength and tensile strength significantly raise；When Ti content is less than During 0.11wt%, with the increase of Ti content, tensile strength, yield strength are linearly increasing, when Ti content be more than 0.11wt% with Afterwards, intensity increase very unobvious；In steel the relation of Ti content and elongation can also approximate representation be linear relationship, with titanium The increase of content, plasticity reduce.When Ti content is 0.05wt%~0.12wt%, showing material has optimal intensity and modeling Property coordinate, while yield tensile ratio is relatively low；In addition, higher Ti contents, reduce the MnS inclusion contents in steel；Therefore, in order to ensure The intensity of steel plate meets standard, designs the minimum 0.050wt% of Ti contents, in order to ensure the elongation percentage of steel plate and consider steel plate into This, design Ti contents are up to 0.070wt%.
It is cold to employ controlled rolling+ACC to ensure the requirement that mechanical property of steel plate meets GB/T1591-2009 by the present invention But technological process, the parameter setting scope of each technological process is mainly on the basis of with reference to related metallurgy principle, by existing Field experiment obtains：
A. the surface temperature control after the heated stove heat of slab can be reduced between 1100-1190 DEG C heated The generation of iron scale in journey, is easy to De-scaling box de-scaling；And in this temperature range, original austenite grains size will not be anxious Play is grown up, and is easy to crystal grain thinning；
B, first stage rolling temperature is controlled at 980 DEG C above is in order to ensure the deformation of steel plate in austenite recrystallization temperature Area is carried out, and passes through recrystallization softening crystal grain repeatedly；It is to ensure its change that the start rolling temperature of two-stage is scheduled on into less than 920 DEG C Shape is carried out in non-recrystallization warm area, so as to avoid partial, re-crystallization warm area, reduces mixed crystal phenomenon；The control steel plate two-stage rolls Thickness when processed is more than 3 times of finished product thickness, can accumulate reduction ratio >=66% to obtain, be enough in order to obtain with this Phase deformed nucleus point (dislocation) and driving force (deformation energy)；Finishing temperature control is that steel plate can be ensured relatively low at 810-850 DEG C At a temperature of deformed, reducing reply etc. that hot stage occurs reduces the phenomenon of dislocation density；And in this finishing temperature It (is about the A of this steel that the temperature that condition lower steel plate enters when ACC equipment is controlled cooling, which can be controlled at 750 DEG C,r3Point) with On, now the tissue of steel plate is still austenite, it is ensured that the effect of cooling is controlled, by controlling cold reduction austenite transformation temperature Degree, crystal grain thinning, and ferrite is hardened, improve armor plate strength.
C, actual production illustrates that final cooling temperature when steel plate goes out ACC is controlled near 630 DEG C, and the tissue of steel plate is still F+P, It is not in the strong phase of the middle temperature transformations such as B.The F+P tissues of refinement, it is ensured that the intensity of steel plate meets Standard, and Plasticity and toughness can also be guaranteed.Final cooling temperature is too high to reduce intensity, too low to damage plasticity and toughness.
Beneficial effects of the present invention are：
Low-alloy high-strength steel Q460C of the present invention, by rational composition design, using the high Ti microalloys of low Nb- into split System, does not reduce toughness on the premise of proof strength, using pure molten steel, optimization temperature-controlled rolling and ACC Controlled cooling process, obtains Organized to preferable F+P, and crystal grain is uniformly tiny, mechanical property meets GB/T1591-2009 requirement, while production cost is low In domestic other iron and steel enterprises for producing Q460C, there is stronger competitive advantage.
Brief description of the drawings
1000 × micro-organization chart for the Q460C that Fig. 1 is produced by embodiment 1；
1000 × micro-organization chart for the Q460C that Fig. 2 is produced by embodiment 2；
1000 × micro-organization chart for the Q460C that Fig. 3 is produced by embodiment 3.
Embodiment
A kind of low-alloy high-strength steel Q460C of the present invention, the weight/mass percentage composition of each element is respectively in steel：C：0.11~ 0.15, Si：0.25~0.35, Mn：1.35~1.45, Nb：0.01~0.02, Ti：0.050~0.070, Als：0.020~ 0.040。
A kind of low-alloy high-strength steel Q460C production method, using molten iron pre-desulfurization, converter smelting, LF refining, continuous casting, Stove heat, controlled rolling, ACC cooling technique steps are heated, wherein：
The O content in steel is controlled in converter smelting process, and in below 600ppm, control taps the lower quantity of slag in molten steel amount Less than 0.01%, it is ensured that the cleanliness factor of molten steel；
In more than 35min, refining terminates preceding 10~15min and adds ferrotianium to carry out micro- conjunction for refining time control in LF refining technique Aurification, effectively steel inclusion rank summation is controlled to be no more than 1.5 grades；
The control of molten steel overtemperature is in the range of 10~35 DEG C in continuous casting process, and pulling rate whole-process control is in 0.8~1.0m/ In the range of min；The offline stacking slow cooling processing of strand；
Heat time >=3.5h of the slab in heating furnace, the surface temperature control at heating end of a period moment is 1100~1190 In the range of DEG C；
Rolled in controlled rolling technique using CR modes, start rolling temperature is 930~1020 DEG C；One stage finishing temperature ＞ 980℃；Two-stage start rolling temperature≤920 DEG C, more than 3 times that treat that temperature thickness is steel plate finished product thickness during open rolling, finish rolling adds up Reduction ratio >=66%, finishing temperature control is in the range of 810~850 DEG C；
Controlled and cooled down using the ACC types of cooling, the final cooling temperature of steel plate is 630 ± 20 DEG C.
Below by way of specific embodiment 1~3, the present invention will be further described：
For embodiment 1~3 from 260mm big cross sections continuous casting billet to ensure compression ratio, production thickness specification is 12~16mm's Q460C finished steels, refining time control prevents in more than 35min, whole micro-pressure operation in LF refining technique in production process Molten steel inhales nitrogen；White slag desulfurization, rapid slagging are made using lime, aluminum steel, aluminum shot etc., sweetening process rationally controls tolerance, forbids to adopt Stirred with atm number；Composition adjustment is carried out using ferromanganese, ferrosilicon, aluminum steel, ferrotianium, in the LF later stages into carrying out Als after white slag desulfurization Adjustment, refining terminate preceding 10~15min and add ferrotianium to carry out microalloying, and the soft blow time is not less than before sampling after the completion of composition adjustment 3min；Below outbound S≤0.010%, Ca >=25ppm, effectively steel grade inclusion behavior summation is controlled to be no more than 1.5 grades；Continuous casting Whole process protection is cast in casting process in technique, and using two chill space electromagnetic stirrings and dynamic soft-reduction, molten steel overtemperature is steady Control calmly in the range of 10~35 DEG C, pulling rate whole-process control is in the range of 0.8~1.0m/min；The offline stacking slow cooling of strand, it is cold But the time is more than 24h；
Table 1 lists each element mass percent and thickness specification in the steel of embodiment 1~3, and table 2 lists embodiment 1~3 Controlled rolling+ACC cooling technique parameters；Table 3 lists the Q460C mechanical performance indexs that embodiment 1~3 is produced.
The main chemical compositions mass percent (wt%) of the embodiment 1~3 of table 1
Embodiment Thickness specification/mm C Si Mn Als Nb Ti
1 12 0.11 0.25 1.35 0.020 0.011 0.051
2 14 0.13 0.30 1.40 0.030 0.015 0.059
3 16 0.15 0.35 1.45 0.040 0.019 0.068
Controlled rolling+ACC the techniques of the embodiment 1~3 of table 2
The mechanical property of the embodiment 1~3 of table 3
Table 3 shows that the Q460C finished product steel mechanical properties that the embodiment of the present invention 1~3 is produced fully meet national standard GB/ T1591-2009 requirement.

Claims (2)

  1. A kind of 1. low-alloy high-strength steel Q460C production method, it is characterised in that：The quality hundred of each element in the Q460C steel Point content is respectively：C：0.11~0.15, Si：0.20~0.40, Mn：1.30~1.50, Nb：0.01~0.02, Ti：0.050 ~0.070, Als：0.020~0.040, using molten iron pre-desulfurization, converter smelting, LF refining, continuous casting, heating stove heat, control Rolling, ACC cooling technique steps, heat time >=3.5h of the continuous casting steel billet in heating furnace, the surface temperature at heating end of a period moment Degree control is in the range of 1100~1190 DEG C；
    Rolled in controlled rolling technique using CR modes, start rolling temperature is 930~1020 DEG C；One 980 DEG C of stage finishing temperature ＞； Two-stage start rolling temperature≤920 DEG C, more than 3 times that treat that temperature thickness is steel plate finished product thickness during open rolling, finish rolling adds up reduction ratio >=66%, finishing temperature control is in the range of 810~850 DEG C；
    Controlled and cooled down using the ACC types of cooling, the final cooling temperature of steel plate is 630 ± 20 DEG C.
  2. A kind of 2. low-alloy high-strength steel Q460C production method as claimed in claim 1, it is characterised in that：The converter smelting The O content in steel is controlled in sweetening process in below 600ppm, it is less than the 0.01% of molten steel amount control the lower quantity of slag of tapping, it is ensured that steel The cleanliness factor of water；
    In more than 35min, refining terminates preceding 10~15min and adds ferrotianium to carry out microalloy for refining time control in LF refining technique Change, effectively control steel inclusion rank summation to be no more than 1.5 grades；
    The control of molten steel overtemperature is in the range of 10 ~ 35 DEG C in continuous casting process, and pulling rate whole-process control is in 0.8 ~ 1.0m/min scopes It is interior；The offline stacking slow cooling processing of strand.
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CN1238548C (en) * 2003-09-23 2006-01-25 东北大学 Production method of yield strongth 460 MPa grade low alloy high strength structure steel plate
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