CN109972033A - A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent - Google Patents
A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent Download PDFInfo
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- 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
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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
- 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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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- 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
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Abstract
A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent, the chemical component mass percent of steel are C=0.04 ~ 0.07, Si=0.15 ~ 0.35, Mn=1.58 ~ 1.68, P≤0.015, S≤0.005, Nb=0.02 ~ 0.03, Ti=0.008 ~ 0.02, Al=0.015 ~ 0.05, Ni=0.15 ~ 0.25, Cu=0.10 ~ 0.18, Cr=0.10 ~ 0.18, Ceq≤0.42, remaining is Fe and inevitable impurity；Processing step includes smelting, heating, rolling, relaxation, cooling.The present invention requires -40 DEG C or more of ductility steel plate using continuous casting billet production low-temperature impact, and maximum gauge can reach 150mm；Tradition TMCP technique is broken through to be limited with continuous casting billet milling special heavy plate compression ratio, improve the structure property of thick steel plates by tissue modulation technology, it is not required to additional heat treatment, process is simple, alloy and production cost are reduced, can be widely applied to the manufacture of the multiple fields slab such as shipbuilding, marine worker, wind-powered electricity generation, bridge, building and engineering machinery.
Description
Technical field
The invention belongs to metal material technical field of smelting, in particular to the super-thick steel plate Q460E's of a kind of low-carbon-equivalent
Production method.
Background technique
Super-thick steel plate generally refers to thickness in the steel plate of 60mm or more.In well known technology, TMCP technique generally can only
For rolling the 60mm ductility steel plate below for thering are -40 DEG C of impacts to require.Super-thick steel plate due to compression ratio limitation, according to
The production of TMCP technique, original austenite grain adequately cannot recrystallize and refine during the rolling process, tissue generally compared with
It is coarse, degraded toughness.Especially for the thick structural steel and iron of spy of this rank of Q460E, since intensity and toughness reguirements all compare
Height, country's prior art maximum gauge only accomplishes 120mm at present, and is generally produced using die casting process, to guarantee steel
The elements such as a large amount of Cr, Mo, Ni, V are added while using high C, high Mn content in the intensity of plate in steel, by improving steel
The harden ability of plate and additional quenching-and-tempering process increase be produced into this way to guarantee the obdurability matching of special heavy plate
Sheet and energy consumption, also extend production and delivery cycle, while the carbon equivalent Ceq higher of steel plate, are unfavorable for welding.
Chinese Patent Application No. 201510153521.5 discloses that " a kind of thickness is more than the Q460E steel plate and its system of 120mm
Make method ", summary of the invention is that special thickness Q460E steel plate is produced by DQ+ normalizing process, production process complexity, cost of alloy compared with
Height, Ceq higher are unfavorable for subsequent use.Chinese Patent Application No. 201110176678.1 discloses a kind of " high-strength tenacity structure
Steel Q460E slab and its production method " produces super-thick steel plate Q460E using traditional TMCP technique, passes through rough rolling step austenite
Recrystallization and finish rolling stage crystal grain flatten the mode elongated and refine crystal grain, this method can not get rid of the limitation of compression ratio, i.e.,
The rolling theory for making strict adherence " high temperature, low speed, big pressure ", can only also produce 100mm steel plate below, while Ceq≤
0.48 control is too high.Chinese Patent Application No. 201310329673.7 discloses " the special thickness Q460 grade high-strength degree knot of big substance
Structure steel plate and manufacturing method ", and by traditional rolling mode, the limitation of compression ratio can not be got rid of, utilize the continuous casting of 400mm thickness
Base can only also produce the special thick product of Q460D of maximum gauge 120mm.
Summary of the invention
The object of the present invention is to provide the production method of the super-thick steel plate Q460E of low-carbon-equivalent a kind of, this method overcomes existing
There is the deficiency of TMCP technology, realizes energy-saving, low-carbon environment-friendly.
Technical solution of the present invention:
A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent, the chemical component mass percent of steel be C=0.04 ~
0.07, Si=0.15 ~ 0.35, Mn=1.58 ~ 1.68, P≤0.015, S≤0.005, Nb=0.02 ~ 0.03, Ti=0.008 ~
0.02, Al=0.015 ~ 0.05, Ni=0.15 ~ 0.25, Cu=0.10 ~ 0.18, Cr=0.10 ~ 0.18, Ceq≤0.42, remaining is
Fe and inevitable impurity；Processing step is as follows:
(1) it smelts: by raw materials for metallurgy successively through the pretreatment of KR molten iron, converter smelting, LF refining, RH vacuum refining and continuous casting, system
It produces and meets chemical component requirement, thickness >=300mm continuous casting billet controls class≤0.5 grade center segregation of casting blank C, center porosity
≤ 0.5 grade.
(2) it heats: continuous casting billet being again heated to 1150 ~ 1180 DEG C, 20 ~ 30min of soaking time.
(3) it rolls: carrying out two-phase control rolling: first stage roughing finishing temperature >=980 DEG C, intermediate base >=1.5 after coming out of the stove
Times plate thickness；700 ~ 760 DEG C of second stage finish rolling start rolling temperature, finishing temperature control is at 690 DEG C ~ 750 DEG C.
(4) relaxation: rear steel plate relaxation is rolled to 10 ~ 20 DEG C of Ar3 or less, the relaxation time controls in ferrite transformation 15% ~ 30%.
(5) cooling: the cooling DQ using Mulpic is quickly cooled down, 5 ~ 10 DEG C/s of cooling rate, red temperature after cooling
350~450℃。
Inventive principle:
Design of Chemical Composition uses the design concept of low-carbon high-manganese, in order to improve intensity and not influence impact flexibility, in C-Mn
On the basis of steel solution strengthening, the alloying elements such as compound addition Nb, Ti, Ni, Cr, Cu give full play to refinement crystal grain, precipitation strength
And the effects of phase transformation strengthening, is to reach high-intensitive, high tenacity and excellent welding performance purpose.
The raising of C content deteriorates the low-temperature flexibility and weldability of steel although can be improved intensity and reduce Ar3 temperature
Can, at the same when the ingredient of low C can inhibit high temperature ferritic transformation pearlite formation, promote the transformation of bainite, for tissue
Regulate and control it is highly beneficial, therefore control C content 0.04 ~ 0.07%.
Mn is weak carbide formation element, it can reduce austenite transformation temperature, fining ferrite grains, to raising steel
Plate intensity and toughness are beneficial, at the same Mn can also solution strengthening ferrite, increase the harden ability of steel plate, promote the formation of bainite.
But when Mn too high levels, segregation is easily formed, and steel plate hardens, ductility degenerates, therefore Mn content of the invention is designed as 1.58
~1.68 %。
Nb can also be improved harden ability, and transition temperature is reduced in mild steel and promotes the formation of bainite structure, and with
Solid solution content of niobium in steel increases, and the trend for forming bainite also increases.The Nb (C, N) that concurrent deformation induction is precipitated is to Ovshinsky
Body crystal boundary has pinning effect, can effectively inhibit the recrystallization of deformed austeaite, but due to compressing in the operation of rolling of the present invention
It is smaller, inhibit the effect of recrystallization that will be weakened, accordingly, it is considered to save the cost, niobium should not be added, should control 0.02% ~
In the range of 0.03%.
Ti is nitrogen killer, and the nitride particles of titanium can prevent the length of steel billet crystal grain in heating, rolling, welding process
Greatly, improve the toughness of base material and welding heat affected zone.It is smaller due to compressing for the present invention, original grain it is oversized
Also it will affect tissue modulation effect when later period phase transformation, therefore the addition of Ti is necessary, but excessive Ti content can cause titanium
Nitride roughening, it is unfavorable to low-temperature flexibility, therefore Ti content in the present invention is set to 0.008 ~ 0.02%.
Ni is particularly critical to the toughness for improving steel plate, can effective disperse C compound aggregation, stablize overcooling austenite, inhibit
Ferrite and bainite crystal grain are grown up.When content is greater than 0.15%, in conjunction with the ultrafast cold technique of DQ of Mulpic, after control is rolled
Cooling rate ultimately forms the compound heterogeneous structure based on pro-eutectoid ferrite and low-carbon bainite in 5 ~ 10 DEG C/S, completes
Cutting to original austenite grains improves low-temperature flexibility.But Ni is expensive, and excessive addition will increase manufacturing cost, therefore
The upper limit is set as 0.25%.
The harden ability for being added to improve steel plate of Cr and Cu, increases precipitating reinforcing effect, belongs to strength enhancing element,
Content is all controlled in 0.10 ~ 0.18% range.
The present invention is different with traditional handicraft, is not recrystallization and finish rolling stage crystal grain pressure by rough rolling step austenite
The mode of flat elongation refines crystal grain, but by ingredient design, zerolling, relaxation and strong cold technique, to the phase after rolling
Become tissue accuracy controlling, form tiny heterogeneous structure, to refine original austenite grains, reaching improves super-thick steel plate obdurability
Purpose.
By a kind of super-thick steel plate Q460E for low-carbon-equivalent that above method manufactures, organize as pro-eutectoid ferrite+low-carbon
The heterogeneous structure of bainite+degenerate perlite and a small amount of MA constituent element, wherein ferritic volume fraction is 15 ~ 30%, bainite
Volume fraction is 70 ~ 85%, remaining is degenerate perlite and a small amount of MA constituent element；With a thickness of 60 ~ 150mm, yield strength 425 ~
476MPa, 554 ~ 618Mpa of tensile strength, -40 DEG C of center portion impact flexibility of low temperature reach 100J or more.
Solid-state phase changes process of the invention be during the rolling process, by the finish rolling stage Ar3 point (about 700 DEG C or so) with
Upper completion finish to gauge waits for thermophase into relaxation, and proeutectoid ferrite knows from experience the preferential conversion near austenite grain boundary, when the iron of transformation
The volume fraction of ferritic reaches 20% or so, is rapidly cooled into Mulpic, the austenite of the supercooling not changed can rapidly into
Enter bainite transformation section, by control cooling velocity in 5 ~ 10 DEG C/S, overcooling austenite is gradually converted into needle iron, grain shellfish and plate
The low-carbon bainites tissue such as shellfish, while completing together with pro-eutectoid ferrite the cutting to coarse original austenite grains, shape
At tiny crystal grain, improve the toughness of steel plate.The overcooling austenite that residue does not change then further decreases entrance with temperature
Martensite transfor mation section and become the island MA constituent element, and return red to 350 ~ 450 DEG C by control steel plate, so that the part island the MA constituent element is existed
It completes to decompose during self tempering, is changed into degenerate perlite, ultimately forms based on pro-eutectoid ferrite+low-carbon bainite,
Mixing heterogeneous structure supplemented by retained austenite and degenerate perlite.
Outstanding feature and remarkable result of the invention is mainly reflected in:
(1) present invention requires -40 DEG C or more of ductility steel plate using continuous casting billet production low-temperature impact, and maximum gauge can reach
150mm, while guaranteeing product quality, carbon equivalent (Ceq) is controlled within 0.42.
(2) present invention breaks through the rolling special heavy plate compression ratio limitation of tradition TMCP technique, is refined by tissue modulation technology brilliant
Grain improves the core structure performance of special thick steel plates, is not required to additional heat treatment, and process is simple, reduces alloy and production cost,
Lumber recovery is high.
(3) present invention can be realized using steel mill's existing equipment and process conditions, be not required to increase investment and scrap build, be improved
Production efficiency shortens the delivery cycle, energy-saving consumption-reducing.
(4) the method for the present invention production is a kind of economizing type, low-carbon environment-friendly steel new varieties, can be widely applied to shipbuilding,
The manufacture of the multiple fields slab such as marine worker, wind-powered electricity generation, bridge, building and engineering machinery.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of 1 steel plate thickness direction of the embodiment of the present invention, 1/4 position.
Fig. 2 is the metallographic structure figure of 1 steel plate thickness direction of the embodiment of the present invention, 1/2 position.
Fig. 3 is the metallographic structure figure of 2 steel plate thickness direction of the embodiment of the present invention, 1/4 position.
Fig. 4 is the metallographic structure figure of 2 steel plate thickness direction of the embodiment of the present invention, 1/2 position.
Fig. 5 is the metallographic structure figure of 3 steel plate thickness direction of the embodiment of the present invention, 1/4 position.
Fig. 6 is the metallographic structure figure of 3 steel plate thickness direction of the embodiment of the present invention, 1/2 position.
Specific embodiment
The chemical composition ranges of the super-thick steel plate Q460E of a kind of low-carbon-equivalent according to the present invention, be casting continuously to form 300mm ×
The continuous casting billet of 1870mm × L, in Heavy Plate Rolling Line by the manufacturer of the super-thick steel plate Q460E of low-carbon-equivalent of the invention a kind of
Method carries out the preparation of thickness 60mm, 100mm and 150mm steel plate respectively.Chemical component is as shown in table 1, processing parameter such as table 2
Shown, properties of product are as shown in table 3.
The chemical component of Q460E special heavy plate in 1 embodiment of table
。
The processing parameter of Q460E special heavy plate in 2 embodiment of the present invention of table
。
The product testing performance of Q460E special heavy plate in 3 embodiment of the present invention of table
。
Reach Q460E grades, 425 ~ 476MPa of yield strength using the steel plate that method of the invention produces, tensile strength 554 ~
618Mpa, -40 DEG C of center portion impact flexibility of low temperature reach 100J or more, and thickness directional properties are good, carbon equivalent (Ceq)≤0.42,
Integrate high-intensitive, high tenacity and high welding performance.
Claims (1)
1. the production method of the super-thick steel plate Q460E of low-carbon-equivalent a kind of, it is characterised in that: the chemical component mass percent of steel
For C=0.04 ~ 0.07, Si=0.15 ~ 0.35, Mn=1.58 ~ 1.68, P≤0.015, S≤0.005, Nb=0.02 ~ 0.03, Ti=
0.008 ~ 0.02, Al=0.015 ~ 0.05, Ni=0.15 ~ 0.25, Cu=0.10 ~ 0.18, Cr=0.10 ~ 0.18, Ceq≤0.42,
Remaining is Fe and inevitable impurity；Processing step is as follows:
(1) it smelts: by raw materials for metallurgy successively through the pretreatment of KR molten iron, converter smelting, LF refining, RH vacuum refining and continuous casting, system
It produces and meets chemical component requirement, thickness >=300mm continuous casting billet controls class≤0.5 grade center segregation of casting blank C, center porosity
≤ 0.5 grade；
(2) it heats: continuous casting billet being again heated to 1150 ~ 1180 DEG C, 20 ~ 30min of soaking time；
(3) it rolls: carrying out two-phase control rolling: first stage roughing finishing temperature >=980 DEG C, intermediate base >=1.5 times plate after coming out of the stove
It is thick；700 ~ 760 DEG C of second stage finish rolling start rolling temperature, finishing temperature control is at 690 DEG C ~ 750 DEG C；
(4) relaxation: rear steel plate relaxation is rolled to 10 ~ 20 DEG C of Ar3 or less, the relaxation time controls in ferrite transformation 15% ~ 30%；
(5) cooling: the cooling DQ using Mulpic is quickly cooled down, cooling rate 5 ~ 10 DEG C/s, and red temperature after cooling 350 ~
450℃。
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Cited By (10)
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|---|---|---|---|---|
| CN110616377A (en) * | 2019-11-06 | 2019-12-27 | 湖南华菱湘潭钢铁有限公司 | Production method of low-yield-ratio high-toughness Q460GJ |
| CN111286676A (en) * | 2020-03-31 | 2020-06-16 | 湖南华菱湘潭钢铁有限公司 | Production method of high crack-arresting marine steel plate |
| CN114150130A (en) * | 2021-12-01 | 2022-03-08 | 宁波江丰热等静压技术有限公司 | Heat treatment method and application of plate for hot isostatic pressing lifting tool |
| CN114892090A (en) * | 2022-05-25 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Production method of Q550-grade high-corrosion-resistance high-strength offshore structure steel |
| CN115198193A (en) * | 2022-07-28 | 2022-10-18 | 湖南华菱湘潭钢铁有限公司 | TMCP (thermal mechanical control processing) process extra-thick specification offshore wind power steel EH36 and production method thereof |
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| CN115261726A (en) * | 2022-08-04 | 2022-11-01 | 江苏省沙钢钢铁研究院有限公司 | Super-thick Q370qE bridge steel plate and production method thereof |
| CN115747673A (en) * | 2022-12-12 | 2023-03-07 | 湖南华菱湘潭钢铁有限公司 | 420E-grade super-thick steel plate and production method thereof |
| CN115838902A (en) * | 2022-12-12 | 2023-03-24 | 湖南华菱湘潭钢铁有限公司 | TMCP (thermal mechanical control processing) process super-thick steel plate and production method thereof |
| CN116043128A (en) * | 2022-12-12 | 2023-05-02 | 湖南华菱湘潭钢铁有限公司 | 460E-grade super-thick steel plate and production method thereof |
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Application publication date: 20190705 |