CN102899556B - Production method for low-alloy medium-thick steel plate - Google Patents
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Abstract
The invention discloses a production method for a low-alloy medium-thick steel plate. The process route comprises the following stages in turn: converter steelmaking, external refining, continuous casting, heating, rolling, and accelerated cooling. Steel comprises the following components by weight percent: 0.15-0.17% of C, 0.20-0.40% of Si, 0.55-0.65% of Mn, less than or equal to 0.020% of P, less than or equal to 0.020% of S, 0.020-0.040% of Al, 0.014-0.016% of Nb, and less than or equal to 0.30% of CEV. The (P+F) micro-structural feature of the traditional Q345D steel plate is maintained by the steel plate; according to the design of the components of the steel plate, the Mn is reduced by 0.9%, no Ni is added and 0.015% of Nb is increased, so that the cost per ton of steel alloy is reduced; the Nb micro-alloying treatment is supplemented with TMCP (Thermo Mechanical Control Process) technology, so that the demand on the performance of the steel plate is met, the percentage elongation is increased by 2%-3% and the impact toughness is increased by about 90J; the CEV of the steel plate is reduced to below 0.30% and the welding property of the steel plate is greatly improved; and the measures, such as, the great reduction of the alloy, the eliminating of ladle furnace process route, the Direct Hot Charging Rolling (DHCR) of hot casting blank, and the like, are taken, so that the production cost of the steel plate is greatly lowered.
Description
Technical field
The invention belongs to steel-smelting technology, is a kind of production method of low-alloy steel plate.
Background technology
Q345D steel plate thickness specification is below 16mm, utilize modernization hot continuous rolling unit substantially can produce in enormous quantities and better economy, but thickness specification is at the plate of moderate thickness of 16～60mm, the economy of its production is poor, after particularly GB GB/T 1591-2008 promulgates, in standard, the Mn content lower limit of Q345D steel grade is cancelled, and steel mill can propose suitable composition and TMCP explained hereafter goes out qualified Q345D steel plate according to the processing unit working condition of self.
Chemical composition and the performance of the 16～60mm specification Q345D steel plate of GB GB/T 1591-2008 to TMCP explained hereafter have concrete requirement; The recommendation that China national Bureau of Technical Supervision promulgates is executed in the GB/T1591-94 low-alloy high-tensile structural steel standard of implementing January 1 nineteen ninety-five, also has concrete requirement.In prior art, 16～60mm specification Q345D steel plate internal control composition of TMCP explained hereafter will be asked for an interview to table 1.
The requirement of table 1 Q345D steel plate internal control composition
In prior art, 16～60mm specification Q345D steel plate technological process of production is generally:
Converter smelting---argon station Argon---LF stove---continuous casting---strand inspection---heating---de-scaling---rolling
---finishing---warehouse-in.
Q345D steel Mn content is higher, and continuously cast bloom center segregation is serious.For guaranteeing continuously cast bloom internal soundness, after molten steel Argon, carry out external refining, dark desulfurization processing, to guarantee the internal soundness of strand.
Because the development trend of high-strength low-alloy steel (HSLA) is to reduce the content of carbon content and alloying element, if adopt thermal mechanical rolling technology by the control to microtexture, can obtain more satisfactory tensile property and toughness.The theory of thermal mechanical rolling is without through cost higher thermal treatment, and obtains the product that performance is significantly improved.Thermal mechanical rolling refers to be rolled in specific temperature range, can obtain the inaccessiable material property of thermal treatment process, and thermal mechanical rolling product has good tensile property, low-temperature flexibility preferably, preferably processability and welding property.
An important feature of alloying element is to be dissolved and formed fine and close carboritride by atom to cause dislocations strengthening to postpone the distortion of austenitic area.Niobium is the active element that expands austenite non-recrystallization district, and austenite recrystallization final temperature can be brought up to 900～950 ° of C from 800～850 ° of C.
At the first rolling sequence (rough rolling step), the austenite of coarse grains constantly refinement after distortion, Recovery and recrystallization after heating.Recrystallize is limited to the effect of grain refining repeatedly, and crystal grain in the middle of only forming, wants austenite perfect recrystallization, roughing temperature must be brought up to 900～950 ° of C.
The finish rolling of the second rolling sequence occurs in austenite non-recrystallization district, and austenite crystal is elongated, and recrystal grain forms deformation bands, and the refinement ferrite obtaining after phase transformation just has good tensile property and toughness.Finishing temperature and last deflection play a decisive role in thermal mechanical rolling, increase fully refinement essence grain and raising ductility transmition temperature of last deflection.
Under controlled rolling, ferritic transformation starts the thickness that temperature (Ar3) depends on chemical composition, rolling parameter, rate of cooling and the product of steel grade.If the two-phase region of rolling finishing temperature below Ar3 point, the ferrite crystal grain forming so can hardening, although intensity has improved, extension property and toughness extreme difference can form the surface imperfection of cracking and layering in the operation of rolling below.
The thickness of middle temperature control plate blank is generally 2～4 times of finished product thickness, and this also depends on desired acquisition intensity and toughness.
After finish rolling, improve speed of cooling, by the tissue after crystal grain thinning and stable rolling, can improve intensity and toughness.Accelerate coolingly can within the scope of structural transformation, obtain unallowed low temperature in the operation of rolling crystal grain that higher speed of cooling can refinement product and improve surface quality.
Only, when the austenite structure that enters transformation is even refinement, ferritic-pearlitic tissue or bainite structure after product changes just have good intensity and toughness.But the austenite structure of alligatoring can be transformed into the microtexture of sclerosis, make toughness variation.Therefore, only have ACC and controlled rolling are combined, could refine austenite tissue.
The main difference part of processing parameter is being forced cooling speed of cooling and temperature range (start and stop cooling).The advantage of on-line cooling: the content that has reduced alloying element; Because carbon equivalent is low, improve weldability energy; Without increasing alloying element, and intensity and toughness are improved; Thermal mechanical rolling has improved output.
There is data to show, contain the violent steel of niobium 0.039 ﹪ low-alloy carbon: be dissolved in the content of niobium in austenite, increase with the rising of temperature.Below Coarsening Temperature time, can effectively stop grain growth containing niobium second phase particles; In the time of a little higher than Coarsening Temperature, thereby second phase particles loses to a part of grain growth the appearance that inhibition causes mixed crystal.Contriver is studied the C-Mn-Nb steel of niobium=0.020%～0.040% the separating out of Nb, solid solution content at different heating temperature, the results are shown in Table 2.
the amount of separating out of Nb at table 2 different heating temperature, solid solution capacity (%)
Test-results in table shows: Nb (C, N) amount in 900 ℃ of following steel is basic and original, and to roll state content suitable, and when temperature is during higher than 900 ℃, start to dissolve on a small quantity with temperature rising Nb (C, N), exceed the Nb in steel after 990 ℃ (C, N) and start to dissolve in a large number, Nb (C, N) fully solid solution enters in steel.C-Mn-Nb steel is in the time of 1150 ℃, and Nb (C, the N) precipitated phase in steel has dissolved (approximately 95%) substantially, and solid solution enters in steel.
Chinese Patent Application No. 201110041266.7,201110041878.6,201110041280.7,201110041881.8 " a kind of production methods of coils of hot-rolled steel ", disclose the production technology of Q345D, Q345D, Q345D, Q345E Low Alloy Steel Plate respectively.Relating to steel plate thickness scope is the following coils of hot-rolled steel of 16mm, is different from the steel plate of uni-tension rolling.Its Composition Design is as table 3.
Table 3 prior art patent coil of strip Composition Design scope (%)
In sum, the major defect that in prior art, the low-alloy plate of moderate thickness of TMCP explained hereafter exists is: the low-alloy plate of moderate thickness Mn content of TMCP explained hereafter is high, continuously cast bloom center segregation is serious, while rolling rear steel plate, there is local delamination, plate centre line segregation usually forms martensite or bainite structure, impacts defective; For guaranteeing continuous casting billet quality, molten steel must carry out external refining.After entering ladle furnace, carry out desulfurization, adjustment temperature, improved production cost; High Mn content causes steel plate carbon equivalent high, and welding property is poor; Each steel mill has been equipped with modern plate mill, and its ability can not be given full play to, and has wasted the resources of production.
Summary of the invention
The present invention aims to provide a kind of production method of low-alloy steel plate, particularly producing thickness is 16～60mm low-alloy Q345D steel plate production technique cheaply, overcome the deficiency that prior art exists, meet the demand of manufacturing, realize theory energy-saving and cost-reducing, green iron and steel.Its feature, for reducing alloy content, reduces center segregation, improves performance uniformity; Reduce carbon equivalent, improve welding property; Use microalloying to carry out TMCP explained hereafter, plate property meets the requirement of GB/T1591-2008, and more traditional production plate property increases substantially; Steel plate is organized as stable (P+F); Exempt part operation and reduce alloy content, continuously cast bloom direct hot charging, reduces production costs.
Technical scheme of the present invention: a kind of production method of low-alloy steel plate, operational path is: converter steelmaking → external refining → continuous casting → heating → rolling → accelerate cooling.
The moiety mass percent of steel is: C=0.15～0.17, Si=0.20～0.40, Mn=0.55～0.65, P≤0.020, S≤0.020, Al=0.020～0.040, Nb=0.014～0.016, CEV≤0.30.
rest part is Fe and uncontrollable impurity element.
Processing step is:
A, converter steelmaking: molten steel sulfur content S≤0.020%, temperature >=1250 ℃, molten iron must be taken off slag totally before entering converter; Converter terminal control C-T coordinates tapping, P≤0.020%, and S≤0.020%, pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; After tapping, squeeze into the deoxidation of Al line and be no less than 150～200m.
B, external refining: argon blowing time >=17min is processed at Argon station, reinforced adjusting component and temperature; Ladle soft blow Ar time >=10min; Argon station is processed molten steel and is finished to control by Als >=0.025%.
C, continuous casting: 1526 ℃ of liquidus lines, 5～15 ℃ of middle bag superheating temperature controls; During pulling speed of continuous casting adopts, plate strand is produced typical pulling rate execution, and stable state casting, produces thickness of strand 300mm, the omnidistance protective casting of carrying out of continuous casting.
D, heating: slab adopts high temperature direct heating, 1260 ± 20 ℃ of heating zones, 1240 ± 20 ℃ of soaking zones, 1240 ℃ ± 10 ℃ of the heart portion temperature of coming out of the stove, rate of heating 6～8min/cm, total time inside furnace is greater than 3h.
E, rolling: roughing adopts high temperature, depresses greatly, rolling technique at a slow speed, and reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches more than 18%, 1150～1170 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures; Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%, 830～900 ℃ of start rolling temperatures, 800～840 ℃ of finishing temperatures.
F, accelerate cooling: roll the strong cold technique of the cooling selection of rear ACC, open 800～820 ℃ of cold temperature, be cooled to 630～650 ℃ of air coolings.
The plate property actual achievement of producing by technique scheme is as table 4, table 5.
table 4 steel plate stretching performance actual achievement
table 5 steel plate-20 ℃ longitudinal impact property actual achievement
From table 4 and table 5, the Q345D steel plate that this patent invention is produced meets the requirement of GB/T1591-2008 completely, and the CEV of steel plate is below 0.30%, and steel plate has good welding property.Yield strength, tensile strength have that larger surplus capacity, particularly unit elongation have improved 2%～3%, impelling strength has improved 90J left and right.
By carrying out submerged arc welding test to falling manganese Q345D plate, result shows to fall under manganese Q345D plate is input as 50kJ/cm condition in heat welds, and tensile property, bending property and the impact property of welding joint are good, can meet standard-required.
The technology of the present invention principle: the present invention possesses the microstructure feature of traditional Q 345D steel plate, is organized as F+P.Its know-why is that the mutagenesis of using Nb microalloy treatment to be aided with the operation of rolling is separated out and to roll rear acceleration cooling, increases substantially intensity and the toughness of steel plate, meets and significantly reduces the requirement of steel plate to intensity after alloy content; Alloy content significantly reduces, and significantly reduces the center segregation of strand, provides possibility for exempting ladle furnace refining; Alloy content significantly reduces, and has also reduced the susceptibility of strand crackle simultaneously, has reduced the generation of crackle, provides possibility for continuously cast bloom directly fills; Alloy content significantly reduces, and the CEV of steel plate is dropped to below 0.30%, has greatly improved the welding property of steel plate; Hot-cast base directly fills (DHCR) has reduced the fuel consumption of heating of plate blank; Significantly the reducing of alloy, the measure such as removal, the direct shove charge of hot-cast base of ladle furnace operational path, greatly reduced the production cost of steel plate.
Therefore, the present invention's a kind of low-cost and high-performance that used TMCP explained hereafter, there is the Q345D steel plate of good welds performance.Compared with prior art, the present invention has the following advantages: steel plate has still retained (P+F) microstructure characteristic of traditional Q 345D steel plate; In steel plate Composition Design, Mn reduces by 0.9%, does not add Ni, has increased 0.015%Nb, has reduced ton Steel Alloy cost; Nb microalloy treatment is aided with TMCP technique, has met the requirement of plate property, and unit elongation has improved 2%～3%, impelling strength has improved 90J left and right; The CEV of steel plate drops to below 0.30%, has greatly improved the welding property of steel plate; Significantly the reducing of alloy, the measure such as removal, the direct shove charge (DHCR) of hot-cast base of ladle furnace operational path, greatly reduced the production cost of steel plate.
Accompanying drawing explanation
Accompanying drawing is the organization chart that patent of the present invention is produced continuously cast bloom low power and steel plate.
Embodiment
The production method of embodiment 1:Q345D steel plate.The composition mass percent of steel designs in table 6.
table 6 Q345D slab composition (%)
Production technique:
Molten steel sulfur content S≤0.020%, temperature >=1250 ℃, molten iron must be taken off slag totally before entering converter, and converter adds molten iron and steel scrap, and molten iron is that 85%～95% to 5%～15%, C-T coordinates tapping, P≤0.020%, S≤0.020% with steel scrap proportioning; Strict pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; After tapping, squeeze into the de-190m oxygen of Al line, and suitably adjust depending on the variation of Intake Quantity, terminal C, molten steel oxidation.
Argon (whole process) time 20min is processed at Argon station, reinforced adjusting component and temperature; Bright circle≤the 200mm of ladle soft blow Ar(after adjusting component and temperature) time 15min; Argon station is processed molten steel and is finished to control by Als >=0.025%;
1526 ℃ of this molten steel phase lines, 10 ℃ of middle bag superheating temperature controls; During pulling speed of continuous casting adopts, plate strand is produced typical pulling rate execution, the casting of strict implement stable state; Produce thickness of strand 300mm(casting machine and produce maximum ga(u)ge); The strict protective casting of the omnidistance implementation of continuous casting, prevents molten steel secondary oxidation and nitrogen pick-up.
Slab adopts high temperature direct heating (DHCR), 800 ℃ of charging temperatures, 1270～1250 ℃ of heating zones; 1230～1250 ℃ of soaking zones; Rate of heating 7min/cm(adjusts according to slab charging temperature), total time inside furnace is greater than 3h.
Roughing: adopt " high temperature, depress greatly, at a slow speed " rolling technique, reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches 20%; 1150～1170 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures.
Finish rolling: accumulative total draft is greater than 60%, and last three percentage pass reductions 15%, are rolled into 60mm Plate Steel; 830～850 ℃ of start rolling temperatures, 800～810 ℃ of finishing temperatures
Roll the strong cold technique of the cooling selection of rear ACC, open 810 ℃ of cold temperature, be cooled to 630 ℃ of air coolings.
Roll into 60mm plate property check: yield strength 346MPa, tensile strength 527MPa, unit elongation 30%, clod wash is qualified ,-20 ℃ of average ballistic work 278J.
The production method of embodiment 2:Q345D steel plate.The composition mass percent of steel designs in table 7.
table 7 Q345D slab composition (%)
Molten steel sulfur content S≤0.020%, temperature >=1250 ℃, molten iron must be taken off slag totally before entering converter, and converter adds molten iron and steel scrap, and molten iron is that 85%～95% to 5%～15%, C-T coordinates tapping, P≤0.020%, S≤0.020% with steel scrap proportioning; Strict pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; After tapping, squeeze into the de-170m oxygen of Al line, and suitably adjust depending on the variation of Intake Quantity, terminal C, molten steel oxidation.
Argon (whole process) time 18min is processed at Argon station, reinforced adjusting component and temperature; Bright circle≤the 200mm of ladle soft blow Ar(after adjusting component and temperature) time 13min; Argon station is processed molten steel and is finished to control by Als >=0.025%;
1526 ℃ of this molten steel phase lines, 12 ℃ of middle bag superheating temperature controls; During pulling speed of continuous casting adopts, plate strand is produced typical pulling rate execution, the casting of strict implement stable state; Produce thickness of strand 300mm(casting machine and produce maximum ga(u)ge); The strict protective casting of the omnidistance implementation of continuous casting, prevents molten steel secondary oxidation and nitrogen pick-up.
Slab adopts high temperature direct heating (DHCR), 750 ℃ of charging temperatures, 1250～1240 ℃ of heating zones; 1220～1230 ℃ of soaking zones; Rate of heating 7min/cm(adjusts according to slab charging temperature), total time inside furnace is greater than 3h.
Roughing: adopt " high temperature, depress greatly, at a slow speed " rolling technique, reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches 20%; 1150～1170 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures.
Finish rolling: accumulative total draft is greater than 60%, and last three percentage pass reductions 22%, are rolled into 20mm Plate Steel; 850～860 ℃ of start rolling temperatures, 820～830 ℃ of finishing temperatures
Roll the strong cold technique of the cooling selection of rear ACC, open 830 ℃ of cold temperature, be cooled to 650 ℃ of air coolings.
Roll into 20mm plate property check: yield strength 387Mpa, tensile strength 530MPa, unit elongation 29%, clod wash is qualified ,-20 ℃ of average ballistic work 292J.
Claims (1)
1. a production method for low-alloy steel plate, operational path is: converter steelmaking → external refining → continuous casting → heating → rolling → accelerate is cooling, it is characterized in that:
The composition quality per-cent of steel is: C=0.15～0.17, and Si=0.20～0.40, Mn=0.55～0.65, P≤0.020, S≤0.020, Al=0.020～0.040, Nb=0.014～0.016, CEV≤0.30, rest part is Fe and uncontrollable impurity element;
Processing step is:
A, converter steelmaking: molten steel sulfur content S≤0.020%, temperature >=1250 ℃, molten iron must be taken off slag totally before entering converter; Converter terminal control C-T coordinates tapping, P≤0.020%, and S≤0.020%, pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; After tapping, squeeze into the deoxidation of Al line and be no less than 150～200m;
B, external refining: argon blowing time >=17min is processed at Argon station, reinforced adjusting component and temperature; Ladle soft blow Ar time >=10min; Argon station is processed molten steel and is finished to control by Als >=0.025%;
C, continuous casting: 1526 ℃ of liquidus lines, 5～15 ℃ of middle bag superheating temperature controls; During pulling speed of continuous casting adopts, plate strand is produced typical pulling rate execution, and stable state casting, produces thickness of strand 300mm, the omnidistance protective casting of carrying out of continuous casting;
D, heating: slab adopts high temperature direct heating, 1260 ± 20 ℃ of heating zones, 1240 ± 20 ℃ of soaking zones, 1240 ℃ ± 10 ℃ of the heart portion temperature of coming out of the stove, rate of heating 6～8min/cm, total time inside furnace is greater than 3h;
E, rolling: roughing adopts high temperature, depresses greatly, rolling technique at a slow speed, and reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches more than 18%, 1150～1170 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures; Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%, 830～900 ℃ of start rolling temperatures, 800～840 ℃ of finishing temperatures;
F, accelerate cooling: roll the strong cold technique of the cooling selection of rear ACC, open 800～820 ℃ of cold temperature, be cooled to 630～650 ℃ of air coolings.
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| CN103215499B (en) * | 2013-05-13 | 2015-08-19 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of easy-formation high-strength medium plate |
| CN103215502B (en) * | 2013-05-13 | 2015-02-18 | 湖南华菱湘潭钢铁有限公司 | Production method of easily formable high-strength medium-thick steel plate |
| CN103233178B (en) * | 2013-05-13 | 2015-03-18 | 湖南华菱湘潭钢铁有限公司 | Production method of formable high-strength medium-thickness steel plate |
| CN103225042B (en) * | 2013-05-13 | 2015-08-05 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of easy-formation high-strength medium plate |
| EP2860276B1 (en) * | 2013-08-13 | 2018-05-02 | Nippon Steel & Sumitomo Metal Corporation | Steel plate |
| CN111621716B (en) * | 2020-05-14 | 2021-10-01 | 河北普阳钢铁有限公司 | Nb-containing low alloy steel rolling process |
| CN112267072A (en) * | 2020-09-30 | 2021-01-26 | 江苏沙钢集团有限公司 | Economical thin Q355B steel plate and preparation method thereof |
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