CN105525213A - High-strength-toughness and high-temperature hot rolled steel plate and preparation method thereof - Google Patents
High-strength-toughness and high-temperature hot rolled steel plate and preparation method thereof Download PDFInfo
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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
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
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Abstract
The invention discloses a high-strength-toughness and high-temperature hot rolled steel plate and a preparation method thereof. The high-strength-toughness and high-temperature hot rolled steel plate is prepared from the following chemical components in percentage by weight: 0.04-0.15 percent of C, 0.05-0.35 percent of Si, 0.5-2.5 percent of Mn, 0.005-0.025 percent of Ti, smaller than or equal to 1.0 percent of Cr, smaller than or equal to 0.5 percent of Mo, smaller than or equal to 1.0 percent of Ni, smaller than or equal to 0.5 percent of Cu, smaller than or equal to 0.003 percent of B, smaller than or equal to 0.02 percent of P, smaller than or equal to 0.01 percent of S, smaller than or equal to 0.007 percent of N, 0.001-0.006 percent of O, smaller than or equal to 0.03 percent of the total content of elements including Al, Zr, Mg, Ca and rare earth and the balance of Fe and inevitable impurity elements. The preparation method of the steel plate comprises the following steps: smelting and casting according to the components, carrying out high-temperature continuous rolling by adopting an austenite, carrying out accelerated cooling by watering the steel plate after being rolled, and then air cooling to room temperature, wherein the heating temperature of a steel billet is 1150-1260 DEG, the cooling temperature is larger than or equal to 5 DEG C/s. and the finish cooling temperature is 550-650 DEG C . As a microscopic structure of the steel plate is a fined acicular ferrite type structure, the steel plate is good in strength and toughness properties. The preparation method of the steel plate is flexible in process and simple in operation, saves the cost and improves the production efficiency.
Description
Technical field
The present invention relates to steel products technical field, particularly a kind of high-strong toughness high-temperature hot rolled steel plate and preparation method thereof.
Background technology
Controlled rolling and controlled cooling technique are the important means improving hot-strip comprehensive mechanical property.Traditional controlled rolling technique comprises austenite recrystallization district and Unhydrated cement two-phase control rolling.First the austenite crystal making alligatoring in heat-processed by recrystallization zone rolling deformation recrystallize and size refinement repeatedly, then treat that temperature enters austenite Unhydrated cement, through enough distortion accumulation, the remarkable refinement of austenite effective particle size also maintains work-hardened condition.Therefore can obtain the phase-change organization of refinement in controlled cooling model process subsequently, improve steel performance.In order to realize sufficient Unhydrated cement rolling deformation, generally need to carry out Nb microalloying to improve austenite non-recrystallization temperature, and need to carry out treating temperature at a certain interior thickness of steel plate, complete heavy reduction rolling distortion at relatively low temperature.Adopt the defect of this technique to be reduction of production efficiency and increased the weight of the loss of mill load and associated components, and improve the cost of alloy of steel plate.Therefore, do not adopt Traditional control rolling and adopt high temperature austenite rolling but the phase-change organization that simultaneously can obtain refinement is one of important research direction of iron and steel technical field.
Publication number is that the patent of invention of CN103343209A discloses a kind of cooling controlling and rolling controlling process improving Q235 plate property, be characterized in avoiding in the middle of steel plate and treat warm link, and directly adopt high temperature rolling, start rolling temperature 1000-1100 DEG C, finishing temperature control is at 900-950 DEG C, ultrafast cooling is carried out immediately, speed of cooling > 100 DEG C/s after rolling.Publication number is the reduce production method that the patent of invention of CN101597673A discloses a kind of low-alloy high-strength thick steel plate, its feature is for adopting the rolling of high temperature austenite recrystallization zone, finishing temperature 950-1050 DEG C, after completing rolling, rolled piece enters ACC water-cooled fast and is cooled to 650-750 DEG C with 3-10 DEG C/s, realizes grain refining.Publication number is that the patent of invention of CN104232868A discloses a kind of optimal control rolling method adopting ultra-rapid cooling to control austenite structure, its feature is for be rolled in steel billet austenite recrystallization district completely, precise rolling control temperature and percentage pass reduction simultaneously, carry out ultra-rapid cooling immediately after rolling, speed of cooling is 50-80 DEG C/s.
Publication number is that the patent of invention of CN1092470A discloses low temperature controlled rolling in the replacement of a kind of titanium treated steel plate high temperature re-crystallization rolling accelerating cooling, be characterized in that adopting the Ti process of 0.005-0.025% in steel, form TiN, Ti (CN) precipitated phase carrys out crystal grain thinning, adopt high temperature re-crystallization rolling and accelerating cooling, finishing temperature requires to control at 900-1000 DEG C.Publication number is that the patent of invention of CN102828115A discloses a kind of Q345B steel plate and production method thereof, be characterized in adopting v n micro alloying and high temperature rolling technique, utilize the VN particle induced synthesis Intragranular Acicular Ferrite of separating out in high temperature rolling process, refinement grain-size.It requires that in steel, N content is 0.008-0.018%, finishing temperature 1070-1100 DEG C, and cooling rate is 18-22 DEG C/s, and final cooling temperature is at 650-750 DEG C.Publication number is that the patent of invention of CN104561792A discloses a kind of V-N alloying High Strength Steel Plate and manufacture method, is characterized in adopting V-N alloying and high temperature rolling technique, improves production efficiency.It requires Ti content 0.002-0.008% in steel, N content 0.008-0.012%, finishing temperature 900-950 DEG C, speed of cooling 15-45 DEG C/s, final cooling temperature 370-550 DEG C.Publication number is a kind of method that the patent of invention of CN103966410A discloses that high temperature rolling produces Q420 rank slab, be characterized in cancelling adding of Nb, Ti, adopt the VN microalloying ingredient design of low cost, adopt high temperature rolling mode to cancel intermediate blank and treat warm process, roughing and final rolling temperature are all more than 1000 DEG C, roller repairing adopts stacking slow cooling, and the polygonal ferrite that is organized as obtained adds pearlitic structure.
Publication number is steel plate and the manufacture method thereof that the patent of invention of CN102409230A discloses a kind of Large Heat Input Welding heat affected zone good-toughness, its feature is that smelting process adopts Ti-Mg complex deoxidization, rolling technology adopts recrystallization zone and the rolling of Unhydrated cement two-stage control, facilitates welded heat affecting zone structure refinement containing titanyl compound.Publication number is the production method that the patent of invention of CN102242309A discloses a kind of high heat-input welding boron-containing petroleum storage tank steel plate for ultra, its feature is that adding Ti and B in smelting process controls inclusion type, size and the quantity in steel, and adopting controlled rolling and controlled cooling and quenching-and-tempering process to produce, this inclusion facilitates intragranular acicular ferrite in welded heat affecting zone and is formed.Publication number is the manufacture method that the patent of invention of CN102330020A discloses that a kind of yield strength is 345-390MPa ductility steel plate, its feature is to adopt silicomanganese pre-deoxidation, adopt Ti iron alloy final deoxygenation, being formed in steel with titanium oxide is the inclusion of core, impel intragranular acicular ferrite forming core, improve steel plate toughness and welding property, add Nb element in steel plate and adopt the rolling of austenite two-stage control and normalizing to add rapid cooling technique.
From existing public technology, adopt high temperature austenite rolling and the process routes obtaining fine grained texture mainly contains two kinds.A kind of process routes is that recrystallization zone rolling and ultra-rapid cooling combine, and be cooled between phase change zone with large cooling rate immediately by the austenite after high temperature deformation, austenite crystal has little time alligatoring, so can obtain the phase-change organization of refinement.But this technique still needs to control austenite finishing temperature, and require to there is higher quick cooling power, so higher to the technical requirements of production unit.Another kind of process routes makes to there is equally distributed fine Second Phase Particles in steel and the phase deformed nucleus that can promote Intragranular Acicular Ferrite, even if so also can obtain the phase-change organization of refinement under thicker austenite grain size by special Composition Design.This technique adopts v n micro alloying usually, promotes that Intragranular Acicular Ferrite is formed, so need to add higher V and N element by rolling and separating out of process of cooling V (CN).In addition, adopt Ti or be evenly distributed in steel with the microinclusions that other elements compounding deoxidations are formed the ability also having and promote that Intragranular Acicular Ferrite is formed, but existing technology utilizes this inclusion to improve the tissue of welded heat affecting zone usually, and cannot the matrix of direct refinement hot-rolled steel sheet, still need to adopt UFG and thermal treatment process to improve the performance of steel plate.
Summary of the invention
The object of the invention is for the problems of the prior art, a kind of high-strong toughness high-temperature hot rolled steel plate and preparation method thereof is provided.
The present invention takes following technical scheme:
1. a high-strong toughness high-temperature hot rolled steel plate, is characterized in that, described steel plate chemical composition comprises by weight percentage: C0.04-0.15%, Si0.05-0.35%, Mn0.5-2.5%, Ti0.005-0.025%, Cr≤1.0%, Mo≤0.5%, Ni≤1.0%, Cu≤0.5%, B≤0.003%, P≤0.02%, S≤0.01%, N≤0.007%, O0.001-0.006%, total content≤0.03% of Al, Zr, Mg, Ca, rare earth element, surplus is Fe and inevitable impurity element.
2. a preparation method for high-strong toughness high-temperature hot rolled steel plate as claimed in claim 1, is characterized in that, said method comprising the steps of:
(1) in smelting casting operation, by each constituent content in mentioned component requirement adjustment molten steel, and be cast into continuously cast bloom or ingot casting, wherein in steel liquid deoxidation link, adopt Ti to carry out deoxidation;
(2) before rolling in heating process, by the steel billet smelted by mentioned component requirement or Heating Steel Ingots to 1150-1260 DEG C, insulation 30-240 minute;
(3) in hot-rolled process, one-phase high temperature continuous rolling is carried out to finished product thickness in the Austenite Dynamic Recrystallization district of steel or complete Static Recrystallization district;
(4) in roller repairing operation, speed of cooling requirement >=5 DEG C/s of accelerating cooling, the water-cooled of watering to steel plate, final cooling temperature is 550-650 DEG C, and steel plate air cooling is to room temperature subsequently.
3. preparation method according to claim 2, is characterized in that, in described step (1), steel liquid deoxidation link also adopted silicomanganese to carry out pre-deoxidation before employing Ti carries out deoxidation.
4. preparation method according to claim 2, is characterized in that, also adopts one or more elements in Al, Zr, Mg, Ca, rare earth to coordinate with Ti and carry out complex deoxidization in described step (1).
5. preparation method according to claim 2, it is characterized in that, in described step (3), hot rolling start rolling temperature is up to the Heating temperature of blank, the minimum need of start rolling temperature are satisfied ensures that finishing temperature is in austenite perfect recrystallization district, hot rolling finishing temperature >=1000 DEG C under this condition.
6. preparation method according to claim 2, is characterized in that, in described step (4), starts water-cooled immediately or first carry out treating that Wen Houzai carries out water-cooled after steel plate finish to gauge, treats that the minimum temperature of temperature is 750-850 DEG C.
Adopt the microinclusions being rich in titanium oxide formed in deoxidation process in the present invention, to be dispersed in steel matrix and in roller repairing process, to promote Intragranular Acicular Ferrite phase deformed nucleus, thus the microstructure of refinement steel plate.The organization type of steel plate of the present invention is the acicular ferrite type tissue of refinement, wherein volume fraction >=50% of acicular ferrite, all the other Main Tissues are bainite and polygonal ferrite, secondaryly be organized as perlite and Ma Ao (M/A) constituent element, the average grain size < of microstructure 10 μm.Because acicular ferrite is a kind of shear transformation tissue being similar to bainitic transformation, inside has the dislocation substructure of certain density, therefore has higher intensity.Meanwhile, because grain-size is tiny, and acicular ferrite lath is in being staggered, and significantly hinders bruise expansion, therefore has excellent impelling strength.
Steel plate preparation method in the present invention overcomes the defect of Traditional control rolling, solves existing high-temperature hot rolled steel plate technique Problems existing with not enough.The present invention, by deoxidation type inclusion usefulization harmful to plate property under normal condition, utilizes fine Titanium particles to carry out the tissue of refinement high-temperature hot rolled steel plate.Adopt high temperature continuous rolling, accelerate rhythm of production, reduce mill load, saved Nb alloying cost.Process for cooling requires flexibly, can adapt to different working conditions.Therefore, preparation method's technique of steel plate of the present invention is flexible, simple to operate, cost-saving, improves production efficiency, and obtains thinning microstructure and high-strong toughness energy.
Accompanying drawing explanation
Fig. 1 is the microstructure metallograph of embodiment 1.
Embodiment
The chemical composition of a kind of high-strong toughness high-temperature hot rolled steel plate of the present invention comprises by weight percentage: C0.04-0.15%, Si0.05-0.35%, Mn0.5-2.5%, Ti0.005-0.025%, Cr≤1.0%, Mo≤0.5%, Ni≤1.0%, Cu≤0.5%, B≤0.003%, P≤0.02%, S≤0.01%, N≤0.007%, O0.001-0.006%, total content≤0.03% of Al, Zr, Mg, Ca, rare earth element, the Fe of surplus and inevitable impurity element.
C, Si, Mn constituent content in steel plate composition of the present invention is identical with conventional low-carbon and low-alloy high-strength steel, and do not need to carry out special adjustment, therefore content range is respectively C0.04-0.15%, Si0.05-0.35%, Mn0.5-2.5%.Final deoxygenation is carried out owing to adopting Ti, and need the microinclusions being rich in titanium oxide to promote that Intragranular Acicular Ferrite is formed in roller repairing process, so require that there is in steel certain the amount of inclusions, namely require that there is certain titanium and oxygen level, but too much can not damage steel plate toughness, therefore content range is respectively Ti0.005-0.025%, O0.001-0.006%.Can first adopt silicomanganese pre-deoxidation to reduce molten steel oxygen level and to save the usage quantity of Ti before Ti deoxidation.Also Al, Zr, Mg, Ca, rare earth element can be adopted to coordinate with Ti simultaneously and carry out complex deoxidization, form the complex phase inclusion being rich in titanium oxide and other oxide compounds, play the effect promoting Intragranular Acicular Ferrite forming core, but in order to ensure enough titanium oxide contents, require total content≤0.03% of Al, Zr, Mg, Ca, rare earth element.In the present invention, the composition of this simple C-Si-Mn-Ti is adopted just can to realize the object of high temperature rolling and structure refinement.
In order to the grain-size of further refinement steel plate, improve the volume fraction of intragranular acicular ferrite, thus improve the intensity of steel plate further, the alloying element adding and improve steel plate hardening capacity can be adopted, as Cr, Mo, Ni, Cu, B element, but the raising in order to avoid intensity causes the remarkable reduction of toughness or brings the obvious increase of cost of alloy, therefore require that content range is respectively Cr≤1.0%, Mo≤0.5%, Ni≤1.0%, Cu≤0.5%, B≤0.003%.
Nb element is indispensable element in general traditional controlled rolling steel, to reach the object of Unhydrated cement rolling, but steel plate of the present invention adopts the district's rolling of austenite high temperature re-crystallization, do not need the austenite grain size obtaining refinement, even thick austenite crystal is conducive to the object realizing structure refinement in steel of the present invention all the better, does not therefore need in steel of the present invention to add valuable Nb element.
P, S, N element all exist as impurity element in steel of the present invention, require that content range is respectively P≤0.02%, S≤0.01%, N≤0.007%, but under certain condition Intragranular Acicular Ferrite is formed with MnS and TiN that titanium oxide compound is separated out also there is favourable effect.
High temperature rolling in the present invention has obviously different from general high temperature re-crystallization rolling of the prior art, require in general technology that finishing temperature is near austenite recrystallization lower limit temperature, is namely rolled in the cold zone in austenite recrystallization district the austenite grain size obtaining refinement.And in the present invention, do not need the austenite recrystallization crystal grain obtaining refinement, without the need to controlling finishing temperature in lower scope, therefore in order to accelerate rolling rhythm, finishing temperature can be improved as far as possible, after heating steel billet is come out of the stove, directly can enter milling train continuous rolling to finished product thickness without any need for treating warm link.Certainly, also can need according to rhythm of production and carry out rolling front or centre and treat temperature, but finishing temperature need meet and ensures austenite generation perfect recrystallization.
Do not need after light plate of the present invention rolls to suppress austenite to be grown up, so carry out water-cooled immediately after not needing to roll, and allow certain air cooling time of staying temperature, but in order to avoid producing thick grain boundary ferrite, the minimum Wen Wendu for the treatment of is not all 750-850 DEG C according to stabilization of austenite.So the beginning temperature of water-cooled exists between very wide selection area, can from after finish to gauge to water-cooled the random time of 750 DEG C, this is very beneficial for arranging production flexibly according to field condition.But in order to faster production rhythm can roll after carry out water-cooled immediately.
In a particular embodiment, according to composition of the present invention and method of deoxidation, adopt vacuum induction furnace smelting 6 stove steel, be cast into 50kg steel ingot, the chemical composition of each embodiment steel is as shown in table 1.The rolling process for cooling of each embodiment, steel plate thickness and toughness and tenacity are respectively in table 2 and table 3.The typical organization of steel of the present invention is acicular ferrite structure, and Fig. 1 is the metallographic structure photo of embodiment 1.
The chemical composition (weight percent) of table 1 various embodiments of the present invention steel plate
| Embodiment | 1 | 2 | 3 | 4 | 5 | 6 |
| C | 0.04 | 0.08 | 0.07 | 0.15 | 0.05 | 0.15 |
| Si | 0.05 | 0.09 | 0.16 | 0.2 | 0.35 | 0.09 |
| Mn | 2.5 | 1.6 | 0.64 | 0.5 | 1.16 | 1.0 |
| Ti | 0.016 | 0.013 | 0.025 | 0.005 | 0.02 | 0.015 |
| Cr | 0.02 | 0.1 | 1.0 | 0.27 | 0.43 | 0.02 |
| Mo | 0.01 | 0.02 | 0.01 | 0.017 | 0.1 | 0.5 4 --> |
| Ni | 0.03 | 0.05 | 0.02 | 1.0 | 0.5 | 0.1 |
| Cu | 0.06 | 0.1 | 0.02 | 0.5 | 0.01 | 0.04 |
| B | 0.0005 | 0.003 | 0.0001 | 0.0003 | 0.0002 | 0.001 |
| Al | 0.01 | 0.006 | 0.006 | 0.004 | 0.009 | 0.005 |
| Zr | 0.0005 | 0.008 | 0.001 | 0.0005 | 0.0003 | 0.004 |
| Mg | 0.0003 | 0.0004 | 0.0034 | 0.0003 | 0.0004 | 0.002 |
| Ca | 0.0004 | 0.0005 | 0.0004 | 0.0042 | 0.0003 | 0.0005 |
| RE | 0.0002 | 0.0001 | 0.0002 | 0.0001 | 0.01 | 0.001 |
| P | 0.01 | 0.012 | 0.01 | 0.011 | 0.02 | 0.008 |
| S | 0.005 | 0.01 | 0.005 | 0.008 | 0.005 | 0.006 |
| N | 0.005 | 0.004 | 0.007 | 0.0035 | 0.005 | 0.002 |
| O | 0.004 | 0.003 | 0.005 | 0.001 | 0.006 | 0.004 |
The rolling process for cooling of table 2 various embodiments of the present invention steel plate
The mechanical property of table 3 various embodiments of the present invention steel plate
Claims (6)
1. a high-strong toughness high-temperature hot rolled steel plate, is characterized in that, described steel plate chemical composition comprises by weight percentage: C0.04-0.15%, Si0.05-0.35%, Mn0.5-2.5%, Ti0.005-0.025%, Cr≤1.0%, Mo≤0.5%, Ni≤1.0%, Cu≤0.5%, B≤0.003%, P≤0.02%, S≤0.01%, N≤0.007%, O0.001-0.006%, total content≤0.03% of Al, Zr, Mg, Ca, rare earth element, surplus is Fe and inevitable impurity element.
2. a preparation method for high-strong toughness high-temperature hot rolled steel plate as claimed in claim 1, is characterized in that, said method comprising the steps of:
(1) in smelting casting operation, by each constituent content in mentioned component requirement adjustment molten steel, and be cast into continuously cast bloom or ingot casting, wherein in steel liquid deoxidation link, adopt Ti to carry out deoxidation;
(2) before rolling in heating process, by the steel billet smelted by mentioned component requirement or Heating Steel Ingots to 1150-1260 DEG C, insulation 30-240 minute;
(3) in hot-rolled process, one-phase high temperature continuous rolling is carried out to finished product thickness in the Austenite Dynamic Recrystallization district of steel or complete Static Recrystallization district;
(4) in roller repairing operation, speed of cooling requirement >=5 DEG C/s of accelerating cooling, the water-cooled of watering to steel plate, final cooling temperature is 550-650 DEG C, and steel plate air cooling is to room temperature subsequently.
3. preparation method according to claim 2, is characterized in that, in described step (1), steel liquid deoxidation link also adopted silicomanganese to carry out pre-deoxidation before employing Ti carries out deoxidation.
4. preparation method according to claim 2, is characterized in that, also adopts one or more elements in Al, Zr, Mg, Ca, rare earth to coordinate with Ti and carry out complex deoxidization in described step (1).
5. preparation method according to claim 2, it is characterized in that, in described step (3), hot rolling start rolling temperature is up to the Heating temperature of blank, the minimum need of start rolling temperature are satisfied ensures that finishing temperature is in austenite perfect recrystallization district, hot rolling finishing temperature >=1000 DEG C under this condition.
6. preparation method according to claim 2, is characterized in that, in described step (4), starts water-cooled immediately or first carry out treating that Wen Houzai carries out water-cooled after steel plate finish to gauge, treats that the minimum temperature of temperature is 750-850 DEG C.
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| CN113186469A (en) * | 2021-04-30 | 2021-07-30 | 攀钢集团攀枝花钢铁研究院有限公司 | 780 MPa-grade hot rolled steel plate for hydraulic bulging and preparation method thereof |
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| CN112981237A (en) * | 2021-01-28 | 2021-06-18 | 江阴兴澄特种钢铁有限公司 | Steel for ball cage type universal joint retainer and production method thereof |
| CN113025903A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Fine-grain hot-rolled plate strip steel and preparation method thereof |
| CN113186469A (en) * | 2021-04-30 | 2021-07-30 | 攀钢集团攀枝花钢铁研究院有限公司 | 780 MPa-grade hot rolled steel plate for hydraulic bulging and preparation method thereof |
| CN113186469B (en) * | 2021-04-30 | 2022-03-22 | 攀钢集团攀枝花钢铁研究院有限公司 | 780 MPa-grade hot rolled steel plate for hydraulic bulging and preparation method thereof |
| CN113930674A (en) * | 2021-09-13 | 2022-01-14 | 广西柳州钢铁集团有限公司 | Welded bottle steel hot-rolled plate strip HP295 and manufacturing method thereof |
| CN115161548A (en) * | 2022-05-25 | 2022-10-11 | 昆明理工大学 | Ti-Zr composite microalloyed 700 MPa-grade high-strength and high-toughness steel plate and preparation method thereof |
| CN115161548B (en) * | 2022-05-25 | 2023-03-24 | 昆明理工大学 | Ti-Zr composite microalloyed 700 MPa-grade high-strength and high-toughness steel plate and preparation method thereof |
| CN115323275A (en) * | 2022-09-05 | 2022-11-11 | 东北大学 | High-strength high-toughness rare earth warm-rolled low-carbon low-manganese TRIP steel and preparation method thereof |
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