CN100467652C - Easy-weld hardening high-strength steel plate and production method thereof - Google Patents

Easy-weld hardening high-strength steel plate and production method thereof Download PDF

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Publication number
CN100467652C
CN100467652C CNB2006100180118A CN200610018011A CN100467652C CN 100467652 C CN100467652 C CN 100467652C CN B2006100180118 A CNB2006100180118 A CN B2006100180118A CN 200610018011 A CN200610018011 A CN 200610018011A CN 100467652 C CN100467652 C CN 100467652C
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steel plate
steel
easy
strength steel
production
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CN101096735A (en
Inventor
叶建军
林明新
梁永昌
谢良法
陆岳璋
赵全卿
李涛
刘新民
赵文忠
郭桐
林建农
吴永斌
李红文
崔强
王培玉
吴建鹏
王九清
田苗
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Wuyang Iron and Steel Co Ltd
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Wuyang Iron and Steel Co Ltd
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Abstract

The invention relates to an easily welded, hardened and tempered high-intensity steel plate and its producing method, which comprises the following part: C<=0.15%, 0.15%-0.50% Si, 0.80%-1.80% Mn, P<=0.02%, S<=0.01%, Mn<=0.6%, Nb<=0.07%, B<=0.003%, Ni<=1.20%, Cr<=0.80%, Ti<=0.03%, V<=0.08%, the rest Fe and unavoidable impurity. The invention smelts with the electric furnace, which is provided with the low quantity P, S and the pure steel, gets the users' favor, has the low cost and the market competitive ability, solves the problem of big crystal grain and low dynamic ductility, and is fit for producing the high-intensity steel with low draught pressure rolling mill in the other steel factory. The invention also reduces the labor strength, which saves the time of the work, improves the availability ratio of the material, and reduces the leveling expense of making the steel plate.

Description

Easy-weld hardening high-strength steel plate and production method thereof
Technical field
The present invention relates to a kind of easy-weld hardening high strength WH80Q steel plate, simultaneously, also relate to a kind of production method of this easy-weld hardening high-strength steel plate, belong to the low-alloy high-strength Welded Structural Steel and make the field.
Background technology
Tradition quenched and tempered steel has shortcomings such as high-carbon quantity, cost that high alloy content and carbon equivalent high brought is higher, welding property is not satisfactory.The DILLMAX690 steel plate that domestic construction machinery industry is produced from import such as Japanese WELTEN80C, SUMITEN80, Sweden SUMTIN780, U.S. A514Gr.B and German DILLINGER Iron And Steel Company mostly with 80kg level high-strength steel, higher, the Cr (1.50%) of C (0.18%) content in the DILLMAX690 steel plate that Germany DILLINGER Iron And Steel Company produces, Ni (1.80%) alloy content are higher, and the steel plate cost value rises.Above-mentioned several import steel price is generally very high.
Along with presenting consumption in the construction machinery industry at home, high-strength steel increases gradually, domestic some other steel plate of this level of iron and steel manufacturer production, but, all below 60mm, can't satisfy the growing slab market requirement because specification limit is narrower.
Summary of the invention
At the problems referred to above, the object of the present invention is to provide a kind of lower carbon equivalent and the easy-weld hardening high-strength steel plate of alloy content, to reduce its production cost greatly.
Simultaneously, the present invention also aims to provide a kind of production method of this easy-weld hardening high-strength steel plate.
To achieve these goals, technical program of the present invention lies in having adopted a kind of easy-weld hardening high-strength steel plate, form: C≤0.15% by the chemical ingredients of following weight percentage, Si 0.15-0.50%, Mn 0.80-1.80%, P≤0.02%, S≤0.01%, Mo≤0.6%, Nb≤0.07%, B≤0.003%, Ni≤1.20%, Cr≤0.80%, Ti≤0.03%, V≤0.08%, surplus are Fe and unavoidable impurities.
Described carbon content is 0.05-0.15%.
Described steel thickness is 10-120mm.
Simultaneously, technical program of the present invention also lies in adopting a kind of production method of easy-weld hardening high-strength steel plate, may further comprise the steps: (1) is earlier through smelting step: adopt ultra-high power electric arc furnace to smelt, choose the high-quality steel grade, melting period is adopted big quantity of slag stream slag operation, vacuum decarburization; Send into then and carry out refining in the LF refining furnace, deoxidation fast, according to taking off the S situation, fine setting Mn, Mo, Nb, Ni, Cr, V content are transferred Ti, B before the bull ladle; (2) heating rolling step: steel ingot is at soaking pit, 1180-1260 ℃ of Heating temperatures, and rate of heating: below 1000 ℃≤100 ℃/h, steel billet heats at continuous oven, 1180-1260 ℃ of Heating temperatures, rate of heating〉10min/cm; Adopt the two-stage controlled rolling, the fs is the Ovshinsky recrystallize stage, and in this stage, austenite deformation and recrystallize carry out simultaneously; Subordinate phase is (950 ℃ ~ A of non-recrystallize stages of austenite R3), in this stage, austenite crystal is elongated, and forms high-density mechanical twin and deformed belt in the austenite of non-recrystallization in elongation, and microalloy carbon, nitride are separated out because of deformation induced simultaneously, carry out water-cooled after rolling, and the water-cooled temperature is lower than 750 ℃; (3) modified step: quenching temperature is 930-950 ℃, passes through tempering after the quenching again, and tempering temperature is 580-670 ℃, and soaking time is 2.5-3.5min/mm, and inspection by sampling gets qualified finished product.
Percentage pass reduction 〉=10% of fs in the step (2), accumulative total draft 〉=60%.
Accumulative total draft 〉=50% of fs in the step (2).
The heat-eliminating medium that quenches in the step (3) is a water.
It is the microalloy element complex intensifying that quenching and tempering, high WH80Q of the present invention adopts Cr-Ni-Mo-B, through rational heat treatment technology, obtains good obdurability coupling, does not reduce the welding property of slab simultaneously again.Carbon content is at 0.05-0.15% among the present invention, the development of high-strength steel is the process that progressively reduces carbon content, the reduction of carbon content, help improving the toughness of steel on the one hand, can improve the welding property of steel on the other hand significantly, the large-scale steel structure members of the stressed complexity of suitable more high tenacity of the present invention and welding property; Si content is between 0.15-0.5%, and Si mainly improves the intensity of steel with the solution strengthening form, but can not too high levels, in order to avoid reduce the toughness of steel; Mn content is chosen in 0.80-1.80%, and Mn mainly plays solution strengthening and reduces transformation temperature and improve armor plate strength, and Mn can significantly improve the hardening capacity of steel, and with the increase of Mn content, the plasticity and the low-temperature impact toughness of steel plate slightly descend, and intensity significantly improves; Cr content≤0.8%, Ni content≤1.2%, Cr, Ni can increase austenite and cross cold energy power, reduce the transition temperature of martensite and bainite, promote martensitic formation; Mo content≤0.8%, B content≤0.003%, an amount of Mo and B can significantly increase the hardening capacity of steel, postpone supercooled austenite to perlitic transformation, by the compound interpolation of Mo and B, after rolling, cools off fast through ACC again steel plate, can eliminate ferrite and pearlitic generation in the steel substantially; Cr, Ni content are lower than external similar steel grade, have both satisfied steel plate obdurability demand, play the saving alloy again, the effect that reduces cost; Nb content≤0.07%, Nb is fairly obvious to the grain refining effect, separates out by Nb in the operation of rolling (C, N) strain inducing to hinder the answer of deformation austenite, recrystallize, make the rolling deformation austenite structure in non-recrystallization zone of finish rolling stage be transformed into tiny phase-change product again during phase transformation through controlled rolling and controlled cooling; V content≤0.08%, V have higher precipitation strength effect, are used for improving the intensity of steel; Titanium is the solid N element of intensive, and tiny Ti, N particle can hinder the austenite crystal of steel when heating effectively and grow up, and can improve the welding property of steel significantly; P content≤0.020%, S content≤0.010% are in order to guarantee that steel is pure, in the quenching and tempering, high, and the higher impelling strength that influences steel plate of P content.
Adopt method of the present invention to produce and realized the lower carbon equivalent and the chemical composition design of alloy content, the heating of strict control strand, rolling and cooling parameter, steel plate is after modifier treatment, not only obtain every mechanical performance index of technical qualification requirements but also reduced production cost, obtained more tiny weave construction and the welding property of Geng Jia simultaneously; Specification limit is wide, and thickness 10-120mm is used for the import substitution product, fills up the domestic market blank, satisfies the demand that the home and abroad construction machinery industry constantly increases consumption.The mechanical property of steel plate of the present invention reaches following requirement: Rp0.2 〉=665MPa after testing, Rm 〉=760MPa, A 〉=14% ,-20 ℃ of AKV 〉=34J.Carbon equivalent Ceq≤0.60% has good welding property.
Because steel of the present invention adopts electrosmelting, P, S content are low, and steel is pure, receives praises from customers; Steel of the present invention is few because of the bullion content that adds, and cost is low, has market competitiveness; Steel of the present invention adopts II type controlled rolling process, has solved the mill milling insufficient pressure and the thick inequality of crystal grain, the impelling strength that cause lower phenomenon, is fit to the low rolling pressure milling train of other steel mill and produces high-strength steel.Because steel cold-bending property of the present invention is good, material does not ftracture when making, and rebound resilience is good, has reduced labour intensity, has saved man-hour and the utilization ratio that has improved material.The steel plate template that adopts method of the present invention to produce is good, and roughness reaches≤5mm/m, can reduce 50 yuan/ton of the making mangling expenses of making side.Because steel of the present invention has excellent comprehensive performances, be used for engineering machinery at present, impelling strength has sizable rich amount, can be widely used in power station, bridge, engineering rack and have great application prospect.Its rolling technology is simple, and the hardening and tempering process scope is wide, and easy handling is suitable for having the Steel Plant of quenching press to produce.Adopt steel of the present invention to substitute the import steel, import steel valency is by 15000 yuan per ton, and as pressing 8500 yuan/ton of average production costs, steel of the present invention is than 6500 yuan/ton of import saving per ton.Manufactory such as manufacturing engineering machinery employing quenching and tempering, high and employing low alloy steel are compared, and can alleviate deadweight 10-50%, and can improve equipment performance and work-ing life, have saved the energy simultaneously, bring bigger benefit therefore can for manufacturing and use department.
Processing step of the present invention is as follows:
Electrosmelting → VD/VOD stove vacuum decarburization → LF stove refining → continuous casting (die casting) → steel billet (ingot) clears up → heats → roll plate → roll back water-cooled → modified → steel plate inspection, reconditioning → tempering → inspection by sampling → warehouse-in
(1) smelting technology: the present invention adopts the 90T ultra-high power electric arc furnace to smelt, and selects the high-quality furnace charge for use, and melting period is adopted big quantity of slag stream slag operation, and P Gao Shixian goes to take off C behind the P, the characteristics that performance low temperature easily takes off P.Slag free tapping does not add any C of containing reductor in the tapping process.
Steel grade of the present invention is in the quick deoxidation of LF stove refining furnace, and according to taking off the S situation, fine setting Mn, Nb, V, Cr, Ni, Mo elements such as (not containing the C alloy) are transferred Ti and B before the bull ladle.
(2) heating rolling technology:
Heating process:
Suitably control rate of heating and Heating temperature can guarantee homogeneous heating and prevent that crystal grain is thick, can guarantee fully solid solution of alloying element competent heat-up time.
Heating cycle is pressed II group steel heating process and is carried out, and soaking time is by increasing by 2 hours with ingot shape II group steel.
Cooling controlling and rolling controlling process:
WH80Q has adopted the two-stage controlled rolling process.Fs is the austenite recrystallization stage, and in this stage (more than 1000 ℃), austenite deformation and recrystallize carry out simultaneously, and the tiny austenite grain because of recrystallize obtains will cause the refinement of ferrite crystal grain.This stage percentage pass reduction 〉=10%, accumulative total draft 〉=60%.Subordinate phase is (950 ℃ ~ A of non-recrystallize stages of austenite R3), in this stage, austenite crystal is elongated, form high-density mechanical twin and deformed belt in the austenite of non-recrystallization in elongation, simultaneously microalloy carbon, nitride are separated out because of deformation induced, thereby have increased ferritic nucleation site, refinement ferrite crystal grain.This stage draft should be tried one's best greatly, accumulative total draft 〉=50%.
The essence of controlled chilling is cooled off fast to the non-recrystallization austenite exactly, forming core on austenite grain boundary and deformation bands even in the deformed austenite, impel and organize further refinement, impel deformed austenite to be transformed into martensite or bainite structure, keep simultaneously dislocation and the distortion that forms in the operation of rolling as much as possible, improve the obdurability of steel plate.The actual production light plate go into water temp more than the Ar3 temperature, adopt suitable speed of cooling, guarantee that leaving water temperature(LWT) below 750 ℃, had both guaranteed template, guaranteed the hot rolling microstructure preparation again.
Adopt the controlled rolling and controlled cooling production technique, WH80Q has obtained favorable tissue, passes through modifier treatment (quenching+high tempering) again, can obtain good comprehensive performances.
(3) hardening and tempering process
Selecting the quenching temperature of WH80Q is 930 ℃-950 ℃, considers from the economy of quenching, and selects water as heat-eliminating medium, and the speed of cooling that can make WH80Q is greater than critical cooling velocity, thus the acquisition martensitic stucture.
Pass through tempering after the quenching again, be transformed into comparatively stable tempered structure, simultaneously, can also eliminate internal stress.Select different tempering temperatures, obtain tissue accordingly, satisfy the mechanical property requirements that the user proposes, to realize elasticity production.Tempering temperature is selected 580 ℃-670 ℃, and soaking time is selected 2.5-3.5min/mm, is organized as tempered sorbite after the tempering, has good obdurability coupling.
Embodiment
Embodiment 1
The hardening high-strength steel of present embodiment each composition of percentage composition by weight consists of: C 0.10%, Si0.20%, Mn 0.94%, P 0.015%, S 0.004%, Mo 0.38%, Ni 0.86%, Cr 0.47%, Nb 0.055%, V 0.053%, B 0.002%, Ti 0.022%, surplus is Fe and inevitably is mingled with.Ceq is 0.48%, rolls into the 48mm steel plate.
Its mechanical property: yield strength: 795MPa, tensile strength: 830MPa, A are 17.5% ,-20 ℃ of ballistic work AKV (vertically) 190,168,150J, cold bending test D=3a, and 180 ° are intact.
Embodiment 2
The hardening high-strength steel of present embodiment each composition of percentage composition by weight consists of: heat (batch) number C 0.12%, Si 0.30%, Mn 0.95%, P 0.008%, S 0.003%, Mo 0.37%, Ni 1.14%, Cr 0.61%, Nb 0.057%, V 0.056%, B 0.0020%, Ti 0.020%, surplus is Fe and inevitably is mingled with.Ceq is 0.56%, rolls into the 80mm steel plate.
Its mechanical property: yield strength: 830MPa, tensile strength: 910MPa, A are 16% ,-20 ℃ of ballistic work AKV (vertically) 150,97,174J, cold bending test D=3a, and 180 ° are intact.
It should be noted last that: above embodiment is the unrestricted technical scheme of the present invention in order to explanation only, although the present invention is had been described in detail with reference to the foregoing description, those of ordinary skill in the art is to be understood that: still can make amendment or be equal to replacement the present invention, and not breaking away from any modification or partial replacement of the spirit and scope of the present invention, it all should be encompassed in the middle of the claim scope of the present invention.

Claims (6)

1, a kind of easy-weld hardening high-strength steel plate is characterized in that: the chemical ingredients by following weight percentage is formed: C 0.05-0.15%, Si 0.15-0.50%, Mn 0.80-1.80%, P 0.008-0.02%, S 0.003-0.01%, Mo 0.37-0.6%, Nb 0.055-0.07%, B 0.002-0.003%, Ni 0.86-1.20%, Cr 0.47-0.80%, Ti 0.02-0.03%, V 0.053-0.08%, surplus is Fe and unavoidable impurities.
2, easy-weld hardening high-strength steel plate according to claim 1 is characterized in that: described steel thickness is 10-120mm.
3, a kind of production method of easy-weld hardening high-strength steel plate as claimed in claim 1 or 2, it is characterized in that: (1) is earlier through smelting step: adopt ultra-high power electric arc furnace to smelt, choose the high-quality steel grade, melting period is adopted big quantity of slag stream slag operation, vacuum decarburization: send into then and carry out refining in the LF refining furnace, deoxidation fast is according to taking off the S situation, fine setting Mn, Mo, Nb, Ni, Cr, V content are transferred Ti, B before the bull ladle; (2) heating rolling step: steel ingot is at soaking pit, 1180-1260 ℃ of Heating temperatures, and rate of heating: below 1000 ℃≤100 ℃/h, steel billet heats at continuous oven, 1180-1260 ℃ of Heating temperatures, rate of heating〉10min/cm; Adopt the two-stage controlled rolling, the fs is the Ovshinsky recrystallize stage, and in this stage, austenite deformation and recrystallize carry out simultaneously; Subordinate phase is that the non-recrystallize phase temperature of austenite is 950 ℃-Ar3, in this stage, austenite crystal is elongated, form high-density mechanical twin and deformed belt in the austenite of non-recrystallization in elongation, microalloy carbon, nitride are separated out because of deformation induced simultaneously, carry out water-cooled after rolling, the water-cooled temperature is lower than 750 ℃; (3) modified step: quenching temperature is 930-950 ℃, passes through tempering after the quenching again, and tempering temperature is 580-670 ℃, and soaking time is 2.5-3.5min/nm, and inspection by sampling gets qualified finished product.
4, the production method of easy-weld hardening high-strength steel plate according to claim 3 is characterized in that: percentage pass reduction 〉=10% of fs in the step (2), accumulative total draft 〉=60%.
5, the production method of easy-weld hardening high-strength steel plate according to claim 3 is characterized in that: accumulative total draft 〉=50% of fs in the step (2).
6, the production method of easy-weld hardening high-strength steel plate according to claim 3 is characterized in that: the heat-eliminating medium that quenches in the step (3) is a water.
CNB2006100180118A 2006-06-26 2006-06-26 Easy-weld hardening high-strength steel plate and production method thereof Expired - Fee Related CN100467652C (en)

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