CN109628854A - A kind of method of ultrafast cold technique production steel plate - Google Patents

A kind of method of ultrafast cold technique production steel plate Download PDF

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CN109628854A
CN109628854A CN201910051142.3A CN201910051142A CN109628854A CN 109628854 A CN109628854 A CN 109628854A CN 201910051142 A CN201910051142 A CN 201910051142A CN 109628854 A CN109628854 A CN 109628854A
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ultrafast
cold technique
ultrafast cold
steel plate
rolling
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CN109628854B (en
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杨海西
张少凯
樊利智
曹晓运
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Hebei Jingye Kuanban Technology Co ltd
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Hebei Jingye Medium Plate Co Ltd
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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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    • C22C33/04—Making ferrous alloys by melting
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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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C21D2211/008—Martensite

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Abstract

A kind of method of ultrafast cold technique production steel plate, it is characterized by: ingredient contains C 0.066~0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb+Ti+V 0.13~0.2%, Al≤0.050% by percentage to the quality, also containing Cr, Mo, Ni, Cu, W, rare earth this 6 class at least 3 classes, surplus is Fe and inevitable impurity element；Ultrafast cold technique is to be cooled to 360-365 DEG C from 845-850 DEG C of finishing temperature with the cooling velocity of 80-90 DEG C/s, and batched in 350-355 DEG C.

Description

A kind of method of ultrafast cold technique production steel plate
Technical field
The invention belongs to technical field of metal material, and in particular to a kind of method of ultrafast cold technique production steel plate, especially It is a kind of method that ultrafast cold technique produces high-intensitive bridge steel plate, seabed tunnel steel plate.
Background technique
Low-alloy structural steel resisting atmosphere corrosion is widely used in the manufacture of the outdoor steel structures such as building, bridge, container, vehicle Field.It is that the Low-Alloy Corrosion Resistants element such as a small amount of Cr, Cu, Ni is added, the Rust Layer Structure of steel is promoted based on low carbon manganese steel It changes, is conducive to slow down atmospheric corrosion speed, significantly improves the atmospheric corrosion resistance of steel.
CN101135029 A describes yield strength 700MPa grade atmospheric corrosion resistant steel and its manufacturing method, intensity compared with It is low, it is unable to satisfy the high-intensitive needs of different occasions.CN103114253 A describes a kind of the very thin of 3~10mm of finished product thickness The production method of specification Ultra-thin ultrahigh-strength steel plates, although yield strength Rp0.2 can be obtained up to 950-1300MPa, Tensile strength Rm:1000-1500MPa, elongation at break A:12-20%, -40 DEG C of impact absorbing energy KV2:80-270J, still Its hot-rolled substrate is by Quenching plus tempering process twice, hence it is evident that affects production efficiency.CN103302255 A is described A kind of thin strap continuous casting 700MPa grades of high-strength air corrosion-resistant steel manufacturing methods, the yield strength of steel band are at least 700MPa, resist Tensile strength is at least 780MPa, elongation percentage is at least 18%, it is also difficult to it is comprehensive to adapt to high intensity, high-elongation, impact resistance etc. The new needs of energy.
In addition autobody sheet and X70, X80 pipe line steel field are concentrated mainly on to the research of ultrafast cold technique at present, for The above high intensity bridge steel plate, seabed tunnel improve high-intensitive, Gao Yanshen using ultrafast cold technique with steel plate field The research of the comprehensive performances such as rate, impact resistance is less.
Summary of the invention
Technical problem solved by the invention is to provide one kind and has the comprehensive performances such as high intensity, high-elongation, impact resistance. To achieve the above object, it is an aspect of the present invention to provide the ingredient of high-intensitive bridge steel plate, seabed tunnel steel plate, another party Face is the production method for proposing high-intensitive bridge steel plate, seabed tunnel steel plate.
Technical solution is as follows:
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient contains C 0.066 by percentage to the quality ~0.069%, Si 0.05~0.1%, Mn1.5~1.55%, P≤0.01%, S≤0.004%, Nb+Ti+V 0.13~ 0.2%, Al≤0.050%, also containing Cr, Mo, Ni, Cu, W, rare earth this 6 class at least 3 classes, surplus is Fe and inevitably Impurity element；Ultrafast cold technique is to be cooled to 360-365 from 845-850 DEG C of finishing temperature with the cooling velocity of 80-90 DEG C/s DEG C, and batched in 350-355 DEG C.
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with 80-90 DEG C/cooling velocity of s is cooled to 360-365 DEG C, and batched in 350-355 DEG C.
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with 80-90 DEG C/cooling velocity of s is cooled to 360-365 DEG C, and batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite and 1.5-2.5% of 96-97% with the area ratio statistics Lath martensite, hetero-organization is bainite ferrite and/martensitic-austenitic, and the acicular ferrite width of formation is averaged model Enclosing is 0.6-0.75 microns, and lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, surrender is strong Degree >=850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work For 200-250J.
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；
Process route includes: molten iron pretreatment → smelting molten steel → external refining → continuous casting → heating and rolling → ultrafast cold It technique and batches；Core procedure is as follows:
(1) molten iron pretreatment desulfurizing；
(2) converter smelting: use double slag operation, bottom-blowing of converter, carbon content target≤0.055%, phosphorus content≤ 0.015%, tapping temperature is 1600-1650 DEG C；Using floating plug, the double slag-stopping tappings of scum rod；
(3) LF+RH refinery practice or RH or VD vacuum outgas；
(4) continuous casting process: whole process blows protective gas, avoids oxidation and nitrogen pick-up；
(5) it heats and rolls；Steel billet is fitted into heating furnace, and 1180~1220 DEG C of heating temperature, total time inside furnace >= 200min, roughing first stage are the rolling of austenite recrystallization area, and start rolling temperature is 1050~1080 DEG C, single pass reduction ratio > 10%, final reduction rate >=25%, roughing second stage is the rolling of austenite Unhydrated cement, finish rolling start rolling temperature≤890 DEG C, finishing temperature is 840-845 DEG C, adds up reduction ratio >=80%, product thickness 10-18mm after rolling terminates；
(6) it ultrafast cold technique and batches；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with the cold of 80-90 DEG C/s But speed is cooled to 360-365 DEG C, and is batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite and 1.5-2.5% of 96-97% with the area ratio statistics Lath martensite, hetero-organization is bainite ferrite and/martensitic-austenitic, and the acicular ferrite width of formation is averaged model Enclosing is 0.6-0.75 microns, and lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, surrender is strong Degree >=850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work For 200-250J.
The method of ultrafast cold technique production steel plate described above, it is characterised in that ultrafast cold technique and batched in step (6)； Ultrafast cold technique is to be cooled to 365 DEG C from 850 DEG C of finishing temperature with the cooling velocity of 90 DEG C/s, and batched in 355 DEG C.
The method of ultrafast cold technique production steel plate described above, it is characterised in that ultrafast cold technique and batched in step (6)； Ultrafast cold technique is to be cooled to 360 DEG C from 845 DEG C of finishing temperature with the cooling velocity of 80 DEG C/s, and batched in 350 DEG C.
The method of ultrafast cold technique production steel plate described above, it is characterised in that: ingredient is C 0.066%, Si 0.06%, Mn 1.52%, P≤0.01%, S≤0.004%, Nb 0.067%, Ti 0.023%, V 0.033%, Al≤ 0.050%, Cr 0.46%, Mo 0.36%, Ni 0.14%, Cu 0.06%, W 0.015%, rare earth 0.0005%, N 0.003%, surplus is Fe and inevitable impurity element.
The method of the ultrafast cold technique production steel plate described above, it is characterised in that: ingredient is C 0.069%, Si 0.1%, Mn 1.55%, P≤0.01%, S≤0.004%, Nb 0.07%, Ti 0.025%, V 0.035%, Al≤ 0.050%, Cr0.48%, Mo 0.38%, Ni 0.15%, Cu 0.09%, W 0.01%, rare earth 0.001%, N 0.005%, surplus is Fe and inevitable impurity element.
Compared with prior art, the technology of the present invention effect includes:
1, the present invention is help to obtain specifically by being precisely controlled to point and production technology, especially ultrafast cold technique Institutional framework helps have the comprehensive performances such as high intensity, high-elongation, impact resistance.
2, have preferable comprehensive mechanical property, in turn avoid increase to process conditions, such as tempering, quenching etc., Production technology has been saved, has not needed to go to obtain performance by production cost, has saved production cost, there is good adaptability.
The content of chemical component of the invention and effect are as follows: (% about ingredient means quality %)
C: be conducive to the intensity index needed for invention steel obtains；Increase the stability of austenite, pass through the partition of carbon The thermal stability and mechanical stability of controllable retained austenite, but excessively high C causes component segregation when being poured, and causes to weld Degradation.Therefore, the additive amount of C is set as C 0.066~0.069%.
Si has the effect of inhibiting to become the precipitation for the carbide for destroying starting point.The thermal stability for increasing austenite, can be with The intensity for improving steel is advantageously implemented the requirement of the intensity and low cost of invention steel.Si element can be improved steel harden ability and Temper resistance, it is advantageous to the comprehensive mechanical property of steel, especially elastic limit, yield strength etc. can also be improved.Therefore it adds 0.05% or more.But when adding more than 0.10%, live weldability is deteriorated.From the viewpoint of site welding, so Si 0.05~0.10%.
Mn is solution strengthening element, can be with stable austenite.Making the phase transition temperature of austenite reduces, and refines the crystal grain of steel, Harden ability and thermostrength are improved, keeps enough intensity and creep resisting ability at high temperature.In addition, making austenite region temperature Degree is expanded in the cooling after the rolling of low temperature side, have be easy to get as microscopic structure of the present invention constitutive requirements it The effect of one continuous cooling transformation tissue.These effects in order to obtain, addition Mn take 1.5% or more.However, even if addition is super 1.6% Mn is crossed, effect is also saturated, so being limited to 1.55% thereon.In addition, the center that Mn encourages continuously casting steel billet is inclined Analysis is formed into the hard phase for destroying starting point, so Mn 1.5~1.55%.
P is impurity, more low the more preferred, if being segregated in the central part of continuously casting steel disc containing having more than 0.02%, drawing Intercrystalline failure is played, significantly reduces low-temperature flexibility, therefore be set as 0.02% or less.In turn, P is due to bringing bad shadow to weldability It rings, it is contemplated that when arriving the above problem, preferably 0.01% or less.
S is impurity, not only causes crackle when hot rolling, but also if excessive, can also low-temperature flexibility be made to be deteriorated.Therefore, It is set as 0.004% or less.In turn, S is segregated in the immediate vicinity of continuously casting steel disc, and the MnS of stretching is formed after rolling, not only at For the starting point of hydrogen induced cracking, it is also possible to generating plate crackle.Sulphur is usually present in steel in the form of FeS.FeS plasticity is poor, Fusing point is low.FeS is distributed in around crystal boundary when molten steel crystal.Therefore, S≤0.004%.
Nb, Ti are one of elements important in the present invention.Nb has the effect that it passes through the towing under solid solution condition Effect and/or as carbon nitridation precipitate pinning effect, inhibit rolling in or rolling after austenite recovery and recrystallization and Effective crystal particle diameter grain refined improves low-temperature flexibility by reducing the crevasse crack propagation of brittle break by grain growth.In turn, exist Fine carbide is generated in the coiling process of feature as hot rolled steel plate manufacturing process, is conducive to mention because of its precipitation strength It is high-intensitive.Also, Nb, which has the effect that, makes γ/α phase change delay, by reducing phase transition temperature, in slow cooling speed Also the microscopic structure after making phase transformation under degree steadily becomes continuous cooling transformation tissue.But these effects in order to obtain, it is necessary to At least 0.065% or more addition.On the other hand, when addition is more than 0.075%, not only its effect is saturated, but also is difficult in hot rolling Make its solid solution in preceding heating process, to form coarse carbonitride and become the starting point destroyed, it is possible to keep low temperature tough Property, acid resistance be deteriorated.In view of production cost and strengthening effect are best, Nb 0.065~0.07% is chosen.
Ti starts to analyse at a high temperature of after the slab cast by continuously casting or steel ingot just solidifies as nitride Out.Precipitate containing the Ti nitride is stable at high temperature, and also not exclusively solid solution, plays pinning in subsequent slab reheating Effect inhibits the coarsening of the austenite grain in slab reheating, microscopic structure is miniaturize, improves low-temperature flexibility.In addition, Inhibit to generate ferritic core in γ/α phase transformation, there is the effect for promoting to generate the continuous cooling transformation tissue as important document of the present invention Fruit.Said effect in order to obtain, it is necessary to the Ti of addition at least 0.02% or more.On the other hand, even if addition is more than 0.012%, The effect is also saturated.Product strength is improved generally for making full use of N and Ti to form TiN, TiC of small and dispersed distribution.By In imperceptibly crystallizing or be precipitated using these precipitates of fine oxide as core and containing Ti nitride, therefore make containing Ti nitrogen Compound, carbide the average equivalent circular diameter of precipitate become smaller, not only inhibit because of the effect intensively dispersed in rolling or roll The recovery and recrystallization of austenite after system also inhibits the ferritic grain growth after batching.Therefore Ti 0.02~0.025%.
V is also common alloy element, and V strengthens steel matrix by precipitation strength and crystal grain refinement, and 0.1% V can To increase by the intensity of 60~100MPa, while V is also ferrite stabilizer, inhibits bainite and perlitic transformation, makes residual Remaining Ovshinsky scale of construction increases.But the selection of V has certain particularity in the present invention, is mainly reflected in VC or V (C, N) 900 DEG C or more can be completely dissolved in austenite, therefore it mainly austenite-ferrite phase transition process alternate precipitation and Precipitation strength in ferrite.The selection of final rolling temperature has fully taken into account the Precipitation Behavior of VC or V (C, N) and true in the application Fixed, neither transition is added and wastes V, it is also considered that influence of the V to strengthening, refining the performances such as crystal grain, therefore V 0.03~ 0.035%.
Al is to make most fine oxides disperse necessary element in deoxygenation of liquid steel.When being excessively added, Effect disappears, so its upper limit is set as 0.05%.
N is formed as described above inhibits the austenite grain in slab reheating containing Ti, V, Nb nitride, carbonitride Coarsening, by subsequent control roll in effective crystal particle diameter have relevant austenite partial size grain refined, by making microscopic structure As continuous cooling transformation tissue, so as to improve low-temperature flexibility.But content less than 0.001% when, cannot get the effect. When on the other hand, containing having more than 0.005%, ductility reduction due to timeliness, formability when tubing is reduced.
Cr is the element for facilitating the intensity of steel by precipitation strength and improving, and preferably adds 0.45% or more.Another party Face sometimes rises hardenability, and bainite tissue when Cr is more than 0.5% and adds, and damages toughness, it is therefore preferable that The upper limit is set as 0.48%.Therefore Cr 0.45~0.48%.
Mo has the effect of improving hardenability, increase intensity.In addition, Mo coexists with Nb, it is strong to inhibit to roll in control The recrystallization of austenite, austenite structure is miniaturize when processed, has the effect of improving low-temperature flexibility.But even if addition is super 0.35% is crossed, effect is also saturated, therefore is set as 0.4% or less.In addition, ductility reduction, having can when 0.4% or more addition Formability when tubing can be made to reduce.Therefore Mo 0.35~0.38%.
Ni is formed tough for low temperature compared with Mn or Cr, Mo in rolling structure (the especially central segregation band of slab) Property, acid resistance harmful sclerotic tissue the case where it is less, therefore, having does not make low-temperature flexibility or site welding be deteriorated and improve The effect of intensity.In addition Ni can also promote the rust of surface of steel plate to densify, and promote the formation for stablizing rusty scale.But even if addition More than 0.15%, effect is also saturated, therefore is set as Ni 0.12~0.15%.
Cu has the effect of improving corrosion resistance, resistance to hydrogen induced cracking characteristic.It should at least add 0.05% or more, but It is that, even if addition is more than 0.09%, effect is also saturated.Therefore Cu 0.05~0.09%.
W is the element for improving intensity, hardness, improving corrosion resistance, and the rust for being created on surface of steel plate can be made if containing W Miniaturization promotes stablizing for surface of steel plate rusty scale to be formed, to play the role of improving corrosion resistance.This effect contains with it The increase of amount and tend towards stability.Therefore W 0.01-0.015%.
It is the element modified to non-metallic inclusion that RE, which is common, while can also refine crystal grain, improves the pinning of oxide Effect or resistance to lamellar tearing improve intensity and toughness.But it even if adds less than 0.0001%, also without the effect；Addition When more than 0.001%, cost be will increase.
Specific embodiment
It elaborates below with reference to specific embodiment to technical solution of the present invention.
Embodiment 1
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient is C by percentage to the quality 0.066%, Si 0.06%, Mn 1.52%, P≤0.01%, S≤0.004%, Nb 0.067%, Ti 0.023%, V 0.033%, Al≤0.050%, Cr 0.46%, Mo 0.36%, Ni 0.14%, Cu 0.06%, W 0.015%, rare earth 0.0005%, N 0.003%, surplus are Fe and inevitable impurity element；
Process route includes: molten iron pretreatment → smelting molten steel → external refining → continuous casting → heating and rolling → ultrafast cold It technique and batches；Core procedure is as follows:
(1) molten iron pretreatment desulfurizing；
(2) converter smelting: use double slag operation, bottom-blowing of converter, carbon content target≤0.055%, phosphorus content≤ 0.015%, tapping temperature is 1600-1650 DEG C；Using floating plug, the double slag-stopping tappings of scum rod；
(3) LF+RH refinery practice or RH or VD vacuum outgas；
(4) continuous casting process: whole process blows protective gas, avoids oxidation and nitrogen pick-up；
(5) it heats and rolls；Steel billet is fitted into heating furnace, and 1180~1220 DEG C of heating temperature, total time inside furnace >= 200min, roughing first stage are the rolling of austenite recrystallization area, and start rolling temperature is 1050~1080 DEG C, single pass reduction ratio > 10%, final reduction rate >=25%, roughing second stage is the rolling of austenite Unhydrated cement, finish rolling start rolling temperature≤890 DEG C, finishing temperature is 840-845 DEG C, adds up reduction ratio >=80%, product thickness 10-18mm after rolling terminates；
(6) it ultrafast cold technique and batches；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with the cold of 80-90 DEG C/s But speed is cooled to 360-365 DEG C, and is batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite and 1.5-2.5% of 96-97% with the area ratio statistics Lath martensite, hetero-organization is bainite ferrite and/martensitic-austenitic, and the acicular ferrite width of formation is averaged model Enclosing is 0.6-0.75 microns, and lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, surrender is strong Degree >=850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work For 200-250J.
Embodiment 2
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient is C by percentage to the quality 0.068%, Si 0.08%, Mn 1.52%, P≤0.01%, S≤0.004%, Nb 0.067%, Ti 0.023%, V 0.032%, Al≤0.050%, Cr0.47%, Mo 0.37%, Ni 0.13%, Cu 0.06%, W 0.011%, rare earth 0.0007%, N 0.005%, surplus are Fe and inevitable impurity element；
Process route includes: molten iron pretreatment → smelting molten steel → external refining → continuous casting → heating and rolling → ultrafast cold It technique and batches；Core procedure is as follows:
(1) molten iron pretreatment desulfurizing；
(2) converter smelting: use double slag operation, bottom-blowing of converter, carbon content target≤0.055%, phosphorus content≤ 0.015%, tapping temperature is 1600-1650 DEG C；Using floating plug, the double slag-stopping tappings of scum rod；
(3) LF+RH refinery practice or RH or VD vacuum outgas；
(4) continuous casting process: whole process blows protective gas, avoids oxidation and nitrogen pick-up；
(5) it heats and rolls；Steel billet is fitted into heating furnace, and 1180~1220 DEG C of heating temperature, total time inside furnace >= 200min, roughing first stage are the rolling of austenite recrystallization area, and start rolling temperature is 1050~1080 DEG C, single pass reduction ratio > 10%, final reduction rate >=25%, roughing second stage is the rolling of austenite Unhydrated cement, finish rolling start rolling temperature≤890 DEG C, finishing temperature is 840-845 DEG C, adds up reduction ratio >=80%, product thickness 10-18mm after rolling terminates；
(6) it ultrafast cold technique and batches；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with the cold of 80-90 DEG C/s But speed is cooled to 360-365 DEG C, and is batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite and 1.5-2.5% of 96-97% with the area ratio statistics Lath martensite, hetero-organization is bainite ferrite and/martensitic-austenitic, and the acicular ferrite width of formation is averaged model Enclosing is 0.6-0.75 microns, and lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, surrender is strong Degree >=850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work For 200-250J.
Embodiment 3
A kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient is C by percentage to the quality 0.069%, Si 0.1%, Mn 1.55%, P≤0.01%, S≤0.004%, Nb 0.07%, Ti 0.025%, V 0.035%, Al≤0.050%, Cr0.48%, Mo 0.38%, Ni 0.15%, Cu 0.09%, W 0.01%, rare earth 0.001%, N 0.005%, surplus are Fe and inevitable impurity element；
Process route includes: molten iron pretreatment → smelting molten steel → external refining → continuous casting → heating and rolling → ultrafast cold It technique and batches；Core procedure is as follows:
(1) molten iron pretreatment desulfurizing；
(2) converter smelting: use double slag operation, bottom-blowing of converter, carbon content target≤0.055%, phosphorus content≤ 0.015%, tapping temperature is 1600-1650 DEG C；Using floating plug, the double slag-stopping tappings of scum rod；
(3) LF+RH refinery practice or RH or VD vacuum outgas；
(4) continuous casting process: whole process blows protective gas, avoids oxidation and nitrogen pick-up；
(5) it heats and rolls；Steel billet is fitted into heating furnace, and 1180~1220 DEG C of heating temperature, total time inside furnace >= 200min, roughing first stage are the rolling of austenite recrystallization area, and start rolling temperature is 1050~1080 DEG C, single pass reduction ratio > 10%, final reduction rate >=25%, roughing second stage is the rolling of austenite Unhydrated cement, finish rolling start rolling temperature≤890 DEG C, finishing temperature is 840-845 DEG C, adds up reduction ratio >=80%, product thickness 10-18mm after rolling terminates；
(6) it ultrafast cold technique and batches；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with the cold of 80-90 DEG C/s But speed is cooled to 360-365 DEG C, and is batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite and 1.5-2.5% of 96-97% with the area ratio statistics Lath martensite, hetero-organization is bainite ferrite and/martensitic-austenitic, and the acicular ferrite width of formation is averaged model Enclosing is 0.6-0.75 microns, and lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, surrender is strong Degree >=850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work For 200-250J.
Comparative example 1
Product composition and production craft step (1)-(5) with embodiment 1, difference be step (6) cooling technique be from 845 DEG C of finishing temperature is cooled to 355 DEG C with the cooling velocity of 5-15 DEG C/s, and is batched in 350 DEG C.
By metallographic structure analysis, final tissue is the acicular ferrite and 11-13% of 72-82% with the area ratio statistics Bainite ferrite, hetero-organization are martensitic-austenitic, and the acicular ferrite width average range of formation is 1.5-1.8 micro- Rice；By mechanics property analysis, yield strength >=620MPa, tensile strength >=760MPa, elongation after fracture >=18%, -40 DEG C Ballistic work be 220-250J.
Comparative example 2
Product composition and production craft step (1)-(5) with embodiment 2, difference be the ultrafast cold technique of step (6) and It batches；Ultrafast cold technique be cooled to 370-375 DEG C from 840-845 DEG C of finishing temperature with the cooling velocity of 80-90 DEG C/s, and It is batched in 345-350 DEG C.
By metallographic structure analysis, final tissue is the acicular ferrite and 3.5-5% of 91-92% with the area ratio statistics Lath martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, the acicular ferrite width average range of formation It is 0.65-0.8 microns, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >=750MPa, tensile strength >=950MPa, elongation after fracture >=20%, -40 DEG C of ballistic work are 220-260J.
Comparative example 3
Product composition and production craft step (1)-(5) with embodiment 3, difference be the ultrafast cold technique of step (6) and It batches；Ultrafast cold technique is to be cooled to 350-355 DEG C from 840-845 DEG C of finishing temperature with the cooling velocity of 95-100 DEG C/s, And it is batched in 345-350 DEG C.
By metallographic structure analysis, final tissue is the acicular ferrite and 3- of 95.5-96.5% with the area ratio statistics 3.5% lath martensite, hetero-organization are granular bainite, and the acicular ferrite width average range of formation is 0.6-0.75 Micron, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >=830MPa resists Tensile strength >=950MPa, elongation after fracture >=23%, -40 DEG C of ballistic work are 210-230J.
Comparative example 4
Production technology in the same manner as in Example 1, but ingredient be C 0.05%, Si 0.05%, Mn 1.3%, P≤ 0.01%, S≤0.004%, Nb 0.06%, Ti 0.01%, V 0.02%, Al≤0.050%, Cr 0.45%, Mo 0.35%, Ni 0.12%, Cu 0.05%, W 0.01%, rare earth 0.0001%, N 0.0015%, surplus are Fe and can not keep away The impurity element exempted from；
By metallographic structure analysis, final tissue is the acicular ferrite and 5-8.5% of 85-89% with the area ratio statistics Lath martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, the acicular ferrite width average range of formation It is 0.7-0.75 microns, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >=690MPa, tensile strength >=840MPa, elongation after fracture >=19.5%, -40 DEG C of ballistic work are 250-270J.
Comparative example 5
Product composition in the same manner as in Example 1, but ingredient be C 0.065%, Si 0.05%, Mn 1.5%, P≤ 0.01%, S≤0.004%, Nb 0.065%, Ti 0.02%, V 0.03%, Al≤0.050%, Cr 0.2%, Mo 0.15%, Ni 0.1%, rare earth 0.0001%, N 0.0015%, surplus are Fe and inevitable impurity element；
By metallographic structure analysis, final tissue is the acicular ferrite of 88-91% and the plate of 5-7% with the area ratio statistics Martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, and the acicular ferrite width average range of formation is 0.6-0.85 microns, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >= 720MPa, tensile strength >=920MPa, elongation after fracture >=18%, -40 DEG C of ballistic work are 240-260J.
Comparative example 6
Product composition in the same manner as in Example 1, but ingredient be C 0.065%, Si 0.05%, Mn 1.5%, P≤ 0.01%, S≤0.004%, Nb 0.065%, Ti 0.05%, Al≤0.050%, Cr 0.45%, Mo 0.35%, Ni 0.12%, Cu 0.05%, rare earth 0.0001%, N 0.0013%, surplus are Fe and inevitable impurity element；
By metallographic structure analysis, final tissue is the acicular ferrite and 4.5- of 93-95.5% with the area ratio statistics 6.5% lath martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, the acicular ferrite width of formation Average range is 0.7-0.85 microns, and lath martensite width average range is 0.48-0.55 microns；By mechanical property point Analysis, yield strength >=750MPa, tensile strength >=950MPa, elongation after fracture >=24%, -40 DEG C of ballistic work are 250- 270J。
Term used herein is explanation and term exemplary, and not restrictive.Since the present invention can be with a variety of Form be embodied without departing from invention spirit or essence, it should therefore be appreciated that above-described embodiment be not limited to it is any above-mentioned Details, and should widely explaining within the spirit and scope of the appended claims, thus fall into claim or its etc. Whole change and modification in effect range all should be appended claims and be covered.

Claims (7)

1. a kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with 80-90 DEG C/cooling velocity of s is cooled to 360-365 DEG C, and batched in 350-355 DEG C.
2. a kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with 80-90 DEG C/cooling velocity of s is cooled to 360-365 DEG C, and batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite of 96-97% and the plate of 1.5-2.5% with the area ratio statistics Martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, and the acicular ferrite width average range of formation is 0.6-0.75 microns, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >= 850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work are 200-250J。
3. a kind of method of ultrafast cold technique production steel plate, it is characterised in that: ingredient be by percentage to the quality C 0.066~ 0.069%, Si 0.05~0.1%, Mn 1.5~1.55%, P≤0.01%, S≤0.004%, Nb 0.065~0.07%, Ti 0.02~0.025%, V 0.03~0.035%, Al≤0.050%, Cr 0.45~0.48%, Mo 0.35~0.38%, Ni 0.12~0.15%, Cu 0.05~0.09%, W 0.01-0.015%, rare earth 0.0001-0.001%, N 0.001- 0.005%, surplus is Fe and inevitable impurity element；
Process route includes: molten iron pretreatment → smelting molten steel → external refining → continuous casting → heating and rolling → ultrafast cold technique With batch；Core procedure is as follows:
(1) molten iron pretreatment desulfurizing；
(2) converter smelting: use double slag operation, bottom-blowing of converter, carbon content target≤0.055%, phosphorus content≤0.015%, out Steel temperature is 1600-1650 DEG C；Using floating plug, the double slag-stopping tappings of scum rod；
(3) LF+RH refinery practice or RH or VD vacuum outgas；
(4) continuous casting process: whole process blows protective gas, avoids oxidation and nitrogen pick-up；
(5) it heats and rolls；Steel billet is fitted into heating furnace, and 1180~1220 DEG C of heating temperature, total time inside furnace >=200min, slightly The first stage is rolled for the rolling of austenite recrystallization area, and start rolling temperature is 1050~1080 DEG C, single pass reduction ratio > 10%, extreme trace Secondary reduction ratio >=25%, roughing second stage are the rolling of austenite Unhydrated cement, finish rolling start rolling temperature≤890 DEG C, finish to gauge temperature Degree is 840-845 DEG C, adds up reduction ratio >=80%, product thickness 10-18mm after rolling terminates；
(6) it ultrafast cold technique and batches；Ultrafast cold technique is the finishing temperature from 845-850 DEG C with the cooling speed of 80-90 DEG C/s Degree is cooled to 360-365 DEG C, and is batched in 350-355 DEG C；
By metallographic structure analysis, final tissue is the acicular ferrite of 96-97% and the plate of 1.5-2.5% with the area ratio statistics Martensite, hetero-organization are bainite ferrite and/martensitic-austenitic, and the acicular ferrite width average range of formation is 0.6-0.75 microns, lath martensite width average range is 0.4-0.5 microns；By mechanics property analysis, yield strength >= 850MPa, tensile strength >=1050MPa, elongation after fracture >=25%, yield tensile ratio 0.79-0.82, -40 DEG C of ballistic work are 200-250J。
4. a kind of method of cold technique production steel plate ultrafast as described in claim 1-3, it is characterised in that ultrafast cold in step (6) It technique and batches；Ultrafast cold technique is to be cooled to 365 DEG C from 850 DEG C of finishing temperature with the cooling velocity of 90 DEG C/s, and in 355 It DEG C is batched.
5. a kind of method of cold technique production steel plate ultrafast as described in claim 1-3, it is characterised in that ultrafast cold in step (6) It technique and batches；Ultrafast cold technique is to be cooled to 360 DEG C from 845 DEG C of finishing temperature with the cooling velocity of 80 DEG C/s, and in 350 It DEG C is batched.
6. a kind of method of cold technique production steel plate ultrafast as described in claim 1-3, it is characterised in that: ingredient is with quality percentage It is C 0.066%, Si 0.06%, Mn 1.52%, P≤0.01%, S≤0.004%, Nb 0.067%, Ti than meter 0.023%, V 0.033%, Al≤0.050%, Cr 0.46%, Mo 0.36%, Ni 0.14%, Cu 0.06%, W 0.015%, rare earth 0.0005%, N 0.003%, surplus are Fe and inevitable impurity element.
7. a kind of method of cold technique production steel plate ultrafast as described in claim 1-3, it is characterised in that: ingredient is with quality percentage Than meter be C 0.069%, Si 0.1%, Mn 1.55%, P≤0.01%, S≤0.004%, Nb 0.07%, Ti 0.025%, V 0.035%, Al≤0.050%, Cr 0.48%, Mo 0.38%, Ni 0.15%, Cu 0.09%, W 0.01%, rare earth 0.001%, N 0.005%, surplus are Fe and inevitable impurity element.
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