CN111926236A - Method for producing steel plate with excellent Z-direction performance for welding structure by adopting continuous casting billet under condition of small compression ratio - Google Patents
Method for producing steel plate with excellent Z-direction performance for welding structure by adopting continuous casting billet under condition of small compression ratio Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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- 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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- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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Abstract
The invention discloses a method for producing a steel plate with excellent Z-direction performance for a welding structure by adopting a continuous casting billet under the condition of a small compression ratio, which comprises the following steps: molten iron treatment: controlling the temperature of the desulfurized molten iron and the proportion of low-sulfur steel scraps, and strictly controlling the contents of P, S, As, Sn and the terminal S in the raw molten iron; smelting in a converter: controlling oxygen lance position, oxygen pressure, oxygen flow, oxygen supply time and fluorite adding amount, wherein C is more than or equal to 0.05 percent and less than or equal to 0.07 percent before tapping, and P is less than or equal to 0.003 percent; refining treatment outside the furnace for 45-55 min, wherein S is less than or equal to 0.003% when the steel is out of the furnace, and nitrogen increment is less than or equal to 0.002%; the temperature of the vacuum treatment molten steel is more than or equal to 1580 ℃, the vacuum degree is less than or equal to 0.13kPa, and the treatment time is 15-25 min; adopting full-flow protection pouring, wherein the nitrogen increment is less than or equal to 0.001%, the superheat degree is 15-20 ℃, the pulling speed is 0.75m/min, and the casting blank is fully sealed and slowly cooled for more than 72 h; heating the casting blank to 1260-1280 ℃, keeping the temperature in the furnace for 420-450 min, and soaking for 70-80 min; controlled rolling, cooling and heat treatment; the thickness of the casting blank is 300mm, the compression ratio is not less than 2.30 and not more than 2.75, and the finished steel plate has excellent Z-direction performance and welding performance.
Description
Technical Field
The invention relates to the technical field of low-alloy high-strength steel manufacturing, in particular to a method for producing a steel plate with excellent Z-direction performance for a welding structure by using a continuous casting billet under the condition of a small compression ratio.
Background
The low-alloy high-strength structural steel is one of the most important engineering structural materials in China, and is widely applied to the construction of various engineering fields of national economy, such as building structures, ocean platforms, pressure vessels, boiler manufacturing, water/nuclear power stations, shipbuilding industries, petroleum and natural gas pipelines, bridge structures, heavy machinery manufacturing, traffic and the like. With the continuous large-scale and heavy engineering construction, the requirements on steel materials are higher and higher, and particularly, for super-thick steel plates, besides high strength and ductility, excellent lamellar tearing resistance, welding performance, cold and hot processing performance, performance uniformity and the like are required. The lack of production technology and technical equipment in China for a long time causes that the mechanical property of the high-strength thick steel plate produced in China cannot meet the technical requirements of large-scale construction projects, especially the deficiency of Z-direction performance and welding performance seriously restricts the development of super-thick steel plates in China, and even depends on forging or is directly imported from abroad to meet domestic requirements.
The domestic super-thick steel plate is usually produced by adopting a continuous casting blank with the thickness of 300mm or more, because the temperature difference between the inside and the outside of the casting blank is overlarge, the content of elements such as carbon, phosphorus, sulfur, manganese and the like at the central part of the casting blank is higher than that on the surface of the casting blank, so that serious central segregation is caused, and in the cooling process of a rolled finished product, the core part of the steel plate can generate a hard martensite or bainite structure, so that the lamellar tearing resistance of the steel plate is seriously influenced.
Before the invention, Japanese patent laid-open Nos. 6-198394 and 6-158222 can produce the thick steel plate with excellent Z-directional performance for building structure, and have the disadvantages that alloy elements such as Cu, Ni and Mo are added when the steel plate is produced and designed, the production cost is high, the compression ratio is more than 3.0, and the thickness of the finished steel plate is only 75mm at most.
The Chinese patent No. 2009100481369.2 discloses a super-thick steel plate with excellent Z-direction performance for buildings and a production method thereof, the thickness of a finished product of the steel plate is 60-130 mm, the Z-direction performance of an embodiment of the steel plate is 62-69%, and the steel plate has excellent lamellar tearing resistance, and has the defects that the related steel plate product is not guaranteed in impact toughness, the compression ratio is not less than 3.0, and the industrial production technology is not difficult.
The Chinese patent with the patent number of 200810141457.9 obtains an ultra-thick steel plate with the thickness of 100-114 mm through quenching and tempering, but the patent has more precious elements of Mo and Cr, so that the process cost is high, and the alloy cost is also high; the Chinese invention patents with patent numbers 200810141500.1 and 201010113835.X also obtain the super-thick steel plate by adding a large amount of precious alloys Mo and Cr and subsequently adopting normalizing plus tempering or secondary quenching plus tempering, but the 2 patents have higher process and alloy cost and are not beneficial to popularization.
The thickness of a Q390E steel plate produced by adopting a 260mm thick continuous casting billet in the patent No. 201010159178.2 is 100mm, the compression ratio is only 2.6, but the related steel plate finished product cannot ensure the lamellar tearing resistance; the Q345EZ35 steel plate produced by the patent with the patent number of 201110302954.4 by adopting a continuous casting billet with the thickness of 300mm has the thickness of 140mm, the compression ratio is only 2.14, and the related steel plate finished product has the laminar tearing resistance which meets the Z35 percent requirement, but the yield strength and the impact energy are both at lower levels.
Disclosure of Invention
The invention aims to provide a method for producing a steel plate with excellent Z-direction performance for a welding structure by adopting a continuous casting billet under the condition of small compression ratio aiming at the defects of the prior art.
The invention relates to a method for producing a steel plate with excellent Z-direction performance for a welding structure by using a continuous casting billet under the condition of small compression ratio, which comprises the following steps:
(1) molten iron treatment: the raw material molten iron is required to have P less than or equal to 0.10 percent, S less than or equal to 0.05 percent, As less than or equal to 0.010 percent, Sn less than or equal to 0.010 percent, KR deep desulfurization molten iron temperature more than or equal to 1250 ℃, desulfurization end point S less than or equal to 0.002 percent and low-sulfur scrap steel less than or equal to 15 percent;
(2) smelting in a converter: charging scrap steel, molten iron and low-sulfur active lime into a furnace, wherein the oxygen lance position is 200mm, the oxygen pressure is 1.0-1.2 MPa, and the oxygen flow is 3.6-4.2 Nm3The oxygen supply time is 13-15 min, and fluorite with the weight not more than 2.5kg/t is added during the blowing period for desulfurization and slag meltingC is more than or equal to 0.05 percent and less than or equal to 0.07 percent before tapping, and P is less than or equal to 0.003 percent;
(3) refining outside the furnace: LF treatment time is 45-55 min, outbound S is less than or equal to 0.003%, and strict nitrogen increment is less than or equal to 0.002%;
(4) and (3) vacuum treatment: the temperature of molten steel is more than or equal to 1580 ℃, the vacuum degree is less than or equal to 0.13kPa, the treatment time is 15-25 min, the adding amount of a CaSi wire is 0.6-0.8 kg/t, and then the soft argon blowing time is controlled to be more than or equal to 5 min;
(5) continuous casting: strictly adopting full-process protective pouring, strictly controlling the nitrogen increment to be less than or equal to 0.001%, controlling the superheat degree to be 15-20 ℃, controlling the pulling speed to be 0.75m/min, and carrying out totally-closed slow cooling for more than 72 hours at a position close to a wind shield after a casting blank is off a line;
(6) heating: heating the casting blank to 1260-1280 ℃, and controlling the total time of the casting blank in the furnace to be 420-450 min, wherein the soaking time of the steel blank is controlled to be 70-80 min;
(7) rolling and cooling: the initial rolling temperature of rough rolling is 1040-1080 ℃, 3 passes are finished, and the single-pass reduction is more than or equal to 45 mm; finishing at the rolling start temperature of 820-840 ℃ for 3-4 times; the laminar cooling speed is 18-22 ℃/s, the final cooling temperature of the surface of the steel plate is 560-570 ℃, and then the steel plate is cooled to 350 ℃ in air and is subjected to totally-enclosed stacking and slow cooling to the room temperature at the position close to the wind shield;
(8) and (3) heat treatment: the quenching temperature is 900-910 ℃, and the in-furnace time (2.1 +/-0.05) min/mm; the tempering temperature is 610-630 ℃, the in-furnace time (2.35 +/-0.05) min/mm, and the steel plate is air-cooled to the room temperature after being taken out of the furnace.
Preferably, the thickness of the casting blank is 300mm, and the compression ratio is more than or equal to 2.30 and less than or equal to 2.75.
Preferably, the method for producing the steel plate for the welded structure with excellent Z-directional performance by using the continuous casting billet under the condition of small compression ratio comprises the following chemical components in percentage by mass: c: 0.10 to 0.17%, Si: 0.15 to 0.50%, Mn: 0.78-1.20%, P is less than or equal to 0.006%, S is less than or equal to 0.003%, Nb: 0.022-0.053%, V: 0.042-0.078%, Ti: 0.008-0.023%, Als: 0.012-0.035%, Ca: 0.0024-0.0069%, Cu is less than or equal to 0.05%, Mo + Cr is less than or equal to 0.10%, Ni is less than or equal to 0.12%, As is less than or equal to 0.010%, Sn is less than or equal to 0.010%, and the balance is Fe and inevitable impurities, and the chemical components also need to satisfy the formula: Ca/S is 2.3-2.4, C + Mn/6+ V/5 is less than or equal to 0.325 percent.
The Z-direction performance of the finished steel plate prepared by the method is more than or equal to 65 percent.
The invention aims to provide a method for producing a steel plate with excellent Z-direction performance for a welding structure by adopting a continuous casting billet under the condition of small compression ratio, the produced finished steel plate has excellent lamellar tearing resistance and welding performance, the production process is simple and feasible, and can be implemented on a large scale in various metallurgical enterprises, the innovation point of the invention is the accurate control of process parameters, and the specific process parameter selection reason is as follows:
(1) in order to ensure the Z-direction performance, welding performance and other performances of the steel plate, raw material impurity elements need to be controlled, so that the KR deep desulfurization requires that the raw material molten iron P is less than or equal to 0.10 percent, S is less than or equal to 0.05 percent, As is less than or equal to 0.010 percent and Sn is less than or equal to 0.010 percent, and low-sulfur steel scrap with the weight percentage less than or equal to 15 percent is added to reduce the content of the impurity elements, purify the steel and improve the comprehensive performance.
(2) The converter smelting requires adding low-sulfur active lime, controlling oxygen blowing process parameters, promoting the effects of removing P and S, adding fluorite with the concentration of less than or equal to 2.5kg/t during the blowing period for desulfurization and slagging, controlling C to be less than or equal to 0.07% and P to be less than or equal to 0.003% before tapping, and preventing the P content of a steel plate finished product from being higher than 0.006% due to nitrogen increase in the subsequent process.
(3) The purpose of the external refining is to supplement alloy and adjust components, remove H and N contents, reduce O and S contents, ensure the molten steel casting temperature and be beneficial to improving the quality of casting blanks; LF outbound requires that S is less than or equal to 0.003 percent and strict nitrogen increment is less than or equal to 0.002 percent; RH is added with calcium-silicon wire to purify the steel, argon is blown to homogenize the components and temperature of the molten steel, and the steel plate finished product with high purity and excellent comprehensive performance is finally obtained through the external refining measures.
(4) In order to improve the internal and surface quality of a casting blank and ensure the content of P in a steel plate finished product, the whole-process protection pouring is strictly adopted during pouring, the superheat degree is reduced by 15-20 ℃, the constant drawing speed is 0.75m/min, and the nitrogen increment is strictly controlled to be less than or equal to 0.001 percent; and after the casting blank is off line, totally-enclosed slow cooling is carried out for more than 72 hours at a position close to the wind shield, so that the casting blank is uniformly and slowly cooled as far as possible, and gas is promoted to continuously and naturally escape, thereby improving the center segregation of the casting blank and improving the purity of steel.
(5) Heating the casting blank to 1260-1280 ℃, controlling the total time of the furnace to be 420-450 min, and keeping the soaking time of the steel blank for 70-80 min so as to ensure that the steel blank is uniformly burnt through, reduce the degree of center segregation and improve the Z-direction performance level.
(6) The purpose of controlling relevant technological parameters during rolling, cooling and heat treatment is to promote the full crushing of crystal grains, refine the structure of a steel plate finished product, reduce the degree of center segregation and facilitate obtaining the mechanical property level required by the invention.
In the embodiment of the invention, the thickness of the casting blank is 300mm, and the compression ratio is more than or equal to 2.30 and less than or equal to 2.75.
According to the embodiment of the invention, the casting blank comprises the following chemical components in percentage by weight: 0.10 to 0.17%, Si: 0.15 to 0.50%, Mn: 0.78-1.20%, P is less than or equal to 0.006%, S is less than or equal to 0.003%, Nb: 0.022-0.053%, V: 0.042-0.078%, Ti: 0.008-0.023%, Als: 0.012-0.035%, Ca: 0.0024-0.0069%, less than or equal to 0.05% of Cu, less than or equal to 0.10% of Mo and Cr, less than or equal to 0.12% of Ni, less than or equal to 0.010% of As, less than or equal to 0.010% of Sn, and the balance of Fe and inevitable impurities, wherein the chemical components also need to satisfy the formula: Ca/S is 2.3-2.4, C + Mn/6+ V/5 is less than or equal to 0.325 percent.
The reasons for the limited amounts of the chemical components in the present invention are detailed below:
the content of C is selected to be 0.10-0.17%, the yield and tensile strength of C are remarkably improved through interstitial solid solution strengthening, and the C can form dispersed micro carbonitride with microalloy elements Nb, V and Ti in steel, so that grain boundary sliding is hindered, crack expansion is delayed, and the strength and toughness are improved; and Mo carbides with different forms can be formed at a certain tempering temperature, so that the strength level of the steel is ensured. When the C content is less than 0.10%, the strength of the steel cannot be secured, and when the C content is more than 0.17%, the plasticity and low-temperature impact toughness of the steel are deteriorated, the weldability of the steel is deteriorated, and the cold brittleness and aging sensitivity of the steel are increased. Therefore, the C content is limited to 0.10-0.17%.
The content of Si is 0.15-0.50%, S exists in ferrite or austenite in the form of solid solution, the strength of the solid solution in steel is improved, Si is a reducing agent and a deoxidizing agent in a steelmaking process, a steel purification effect is achieved, and the lamellar tearing resistance is improved, but the plasticity, the toughness and the ductility of the steel are reduced to a certain extent by the Si, and the welding performance is not facilitated. Therefore, the product performance of the invention is comprehensively considered, and the Si content is limited to 0.15-0.50%.
The content of Mn is selected to be 0.78-1.20%, Mn and iron form a solid solution, the hardness and strength of ferrite and austenite in steel are improved, the steel has the function of refining grains, the steel is one of essential important elements for ensuring the strength and toughness of steel and the low-temperature toughness of a welding heat affected zone, Mn is also a good desulfurizer in the steel-making process, and the lamellar tearing resistance is improved by purifying the steel. However, excessive Mn tends to coarsen steel grains, increases the temper brittleness sensitivity of steel, and is easy to generate white spots due to improper cooling after smelting, casting and forging-rolling, thereby damaging the mechanical properties of the steel, such as lamellar tearing resistance, impact toughness, welding performance and the like. Therefore, the Mn content is limited to 0.78 to 1.20%.
P is less than or equal to 0.006 percent, S is less than or equal to 0.003 percent, and P, S belongs to harmful elements in steel. P increases the cold brittleness of steel, reduces the ductility and toughness and deteriorates the welding performance; and S is easy to form strip MnS inclusions, reduces the toughness and ductility of steel, is easy to cause cracks during forging and rolling, is not beneficial to welding performance, and P, S is easy to form segregation at grain boundaries, and damages the performances of the steel such as lamellar tearing resistance, impact toughness and the like.
The content of Nb is selected to be 0.022-0.053%, part of Nb in the steel is enhanced in strength in a solid solution strengthening mode, the other part of Nb is combined with carbon and nitrogen to form stable carbonitride, and the stable carbonitride has strong fine grain strengthening and precipitation strengthening effects, and the finely divided compounds in dispersion distribution can effectively inhibit austenite grain coarsening at high temperature, and simultaneously enhance the strength and improve the low-temperature toughness. In the tempering process, more and finer Nb composite carbonitrides are precipitated, so that the toughness of the steel is further ensured, and the welding performance is very favorable. When the Nb content is less than 0.022%, the above effect is not significant, and when the Nb content is more than 0.053%, more C is consumed to form carbonitride, so that the effect of C in steel is reduced, and the comprehensive performance of steel is not easily ensured.
The content of V is selected to be 0.042-0.078%, and as Nb, part of V in the steel improves the strength in a solid solution strengthening mode, and the other part of V is combined with carbon and nitrogen to form stable carbonitride, so that the steel has the effects of refining structure grains, strengthening precipitation, improving the strength and improving the low-temperature toughness. During the tempering process, V can increase the tempering stability and produce a secondary hardening effect. When the V content is less than 0.042%, the above effect is not significant, and when the V content is more than 0.078%, more solid solution V is adversely affected in impact toughness and weldability.
The Ti is selected to be 0.008-0.023%, TiC particles formed by the Ti at high temperature can block grain boundary sliding and delay crack formation and expansion, and the strength and the toughness of the steel are obviously improved. The carbonitride of Ti can also effectively inhibit the growth of austenite grains in the heating and welding processes and improve the toughness and HAZ low-temperature toughness, but when the content of Ti is less than 0.008 percent, the effect is not obvious, and when the content of Ti is more than 0.023 percent, more TiC precipitated at the grain boundary during heating and welding increases the brittleness of the grain boundary, which is not beneficial to the plasticity and the toughness and the welding performance.
The content of Als is selected to be 0.012-0.035%, Als and nitrogen have strong binding force, and formed AlN has the effect of grain refinement, improves the impact toughness of the steel at low temperature, and simultaneously has the effect of inhibiting the strain aging of the steel. In addition, Als in the steel has the functions of deoxidizing and purifying the steel, and is very favorable for improving the lamellar tearing resistance. However, if the content of Als is too high, large oxide inclusions are formed, and the overall properties of the steel are adversely affected.
The content of Ca is selected to be 0.0024-0.0069%, Ca in the steel has a deoxidizing effect, the effect of adding Ca in combination with Als is better, the content of oxygen in the steel can be reduced to be below 20ppm, not only can the generation of casting blank air holes be prevented, but also the fluidity of molten steel can be improved due to the reduction of the content of oxygen and inclusions in the steel, and the surface quality of a casting blank is improved; simultaneously forming CaO and Al in the steel2O3The calcium aluminate which is easy to float upwards is formed by the action, and the removal speed and the effect of the nonmetallic inclusion are obviously improved. In addition, Ca can also modify and spheroidize manganese sulfide inclusions, purify steel quality and improve the lamellar tearing resistance of the steel. When the content of Ca is less than 0.0024% of the Ca content is not obvious, when the Ca content is more than 0.0078%, the Ca is easy to be deviated in crystal boundary, and large-scale composite inclusions are easy to form, which is not favorable for strength and toughness and lamellar tearing resistance. Therefore, Ca is limited to 0.0024 to 0.0069%.
The Cu content is less than or equal to 0.05 percent, the Mo + Cr content is less than or equal to 0.10 percent, and the Cu, the Mo and the Cr are elements with strong solid solution strengthening, which are very beneficial to improving the strength but not beneficial to the impact toughness.
The Ni content of the invention is selected to be less than or equal to 0.12 percent, and the Ni in the steel can refine the ferrite matrix structure, improve the strength and improve the low-temperature impact toughness; meanwhile, the carbon content can be properly reduced by adding a proper amount of Ni, so that the plastic toughness and the welding performance of the steel are further improved.
As is less than or equal to 0.010 percent and Sn is less than or equal to 0.010 percent, As and Sn in the steel are used As harmful residual elements and mainly exist in a solid solution state and a compound state, and even a lower content can have great influence on the performance. As and Sn are easy to generate segregation at grain boundaries to destroy the continuity of metal, thereby causing the phenomenon of temper brittleness, hot brittle cracks and other defects are easy to generate on the surface during hot processing, simultaneously the cold brittleness of steel is increased, the elongation and the impact toughness of the steel are reduced, the welding performance and the lamellar tearing resistance of the steel are deteriorated, and therefore, the content of As and Sn in the steel is strictly limited.
Meanwhile, the chemical components also need to satisfy the formula: Ca/S is 2.3-2.4, C + Mn/6+ V/5 is less than or equal to 0.325 percent. The Ca has the deoxidation effect, has better effect when being matched with the Als, can reduce the oxygen content in steel to be less than 20ppm, not only can prevent casting blank air holes from being generated, but also can improve the fluidity of molten steel and the surface quality of casting blanks due to the reduction of the oxygen and inclusion content in the steel, and simultaneously forms CaO and Al in the steel2O3Calcium aluminate which is easy to float upwards is formed under the action of the calcium aluminate, so that the removal speed and effect of nonmetallic inclusions are obviously improved; in addition, Ca can also deteriorate and spheroidize manganese sulfide inclusions, purify steel quality and improve the lamellar tearing resistance of steel, when Ca/S is less than 2.3, Ca cannot play the due role, and when Ca/S is more than 2.4, redundant Ca is easy to segregate in a grain boundary, is easy to form large-scale composite inclusions, and is not beneficial to toughness and lamellar tearing resistance. When C + Mn/6+ V/5 > 0.325%, the sum of carbon equivalent will be increasedThe sensitivity coefficient of welding cracks, and the welding performance and HAZ impact toughness are reduced.
The steel of the present invention contains the above chemical components, and the balance of Fe and inevitable impurities.
In the embodiment of the invention, the Z-direction performance of the finished steel plate is more than or equal to 65 percent.
It should be noted that, through the verification of the trial and error of the present inventors, the steel plate product with the chemical composition of the present invention, which is manufactured strictly by the technological parameters of the present invention, such as smelting, rolling, cooling, heat treatment, etc., can meet the requirements of the present invention. Compared with the prior art, the steel of the invention does not need to add a large amount of noble metals such as Mo, Cr and the like, has low alloy cost and simple and easy production process, and can be implemented on a large scale in various metallurgical enterprises; the steel plate produced by the method has the characteristics of high strength, high plasticity, low yield ratio, excellent low-temperature toughness, good performance uniformity and the like, and particularly the finished steel plate has excellent Z-direction performance and welding performance.
Detailed Description
In order to better explain the technical solution of the present invention, the technical solution of the present invention is further described below with reference to specific examples, which are only exemplary to illustrate the technical solution of the present invention and do not limit the present invention in any way.
The following table 1 is a list of values of chemical components in percentage by weight in each example and comparative example of the present invention;
table 2 below is a list of values of the main process parameters of the examples and comparative examples of the present invention;
the following table 3 shows the mechanical property test results of the examples and comparative examples of the present invention.
The thicknesses of the steel plates of the examples 1 to 8 and the comparative examples 1 to 3 are both 110 to 130 mm.
The method for producing the steel plate for the welding structure with excellent Z-direction performance by using the continuous casting billet under the condition of small compression ratio comprises the following steps:
(1) molten iron treatment: the raw material molten iron is required to have P less than or equal to 0.10 percent, S less than or equal to 0.05 percent, As less than or equal to 0.010 percent, Sn less than or equal to 0.010 percent, KR deep desulfurization molten iron temperature more than or equal to 1250 ℃, desulfurization end point S less than or equal to 0.002 percent and low-sulfur scrap steel less than or equal to 15 percent;
(2) smelting in a converter: charging scrap steel, molten iron and low-sulfur active lime into a furnace, wherein the oxygen lance position is 200mm, the oxygen pressure is 1.0-1.2 MPa, and the oxygen flow is 3.6-4.2 Nm3The oxygen supply time is 13-15 min, fluorite with the weight of less than or equal to 2.5kg/t is added during the converting period for desulfurization and slag melting, C is more than or equal to 0.05% and less than or equal to 0.07% before tapping, and P is less than or equal to 0.003%;
(3) refining outside the furnace: LF treatment time is 45-55 min, outbound S is less than or equal to 0.003%, and strict nitrogen increment is less than or equal to 0.002%;
(4) and (3) vacuum treatment: the temperature of molten steel is more than or equal to 1580 ℃, the vacuum degree is less than or equal to 0.13kPa, the treatment time is 15-25 min, the adding amount of a CaSi wire is 0.6-0.8 kg/t, and then the soft argon blowing time is controlled to be more than or equal to 5 min;
(5) continuous casting: strictly adopting full-process protective pouring, strictly controlling the nitrogen increment to be less than or equal to 0.001%, controlling the superheat degree to be 15-20 ℃, controlling the pulling speed to be 0.75m/min, and carrying out totally-closed slow cooling for more than 72 hours at a position close to a wind shield after a casting blank is off a line;
(6) heating: heating the casting blank to 1260-1280 ℃, and controlling the total time of the casting blank in the furnace to be 420-450 min, wherein the soaking time of the steel blank is controlled to be 70-80 min;
(7) rolling and cooling: the initial rolling temperature of rough rolling is 1040-1080 ℃, 3 passes are finished, and the single-pass reduction is more than or equal to 45 mm; finishing at the rolling start temperature of 820-840 ℃ for 3-4 times; the laminar cooling speed is 18-22 ℃/s, the final cooling temperature of the surface of the steel plate is 560-570 ℃, and then the steel plate is cooled to 350 ℃ in air and is subjected to totally-enclosed stacking and slow cooling to the room temperature at the position close to the wind shield;
(8) and (3) heat treatment: the quenching temperature is 900-910 ℃, and the in-furnace time (2.1 +/-0.05) min/mm; the tempering temperature is 610-630 ℃, the in-furnace time (2.35 +/-0.05) min/mm, and the steel plate is air-cooled to the room temperature after being taken out of the furnace.
The thickness of the casting blank is 300mm, and the compression ratio is not less than 2.75 and not more than 2.30.
In the method for producing a steel plate for welded structures excellent in Z-directional performance from a continuous casting slab under a low reduction ratio condition according to the embodiments of the present invention, the continuous casting slab contains the following chemical components in parts by mass: c: 0.10 to 0.17%, Si: 0.15 to 0.50%, Mn: 0.78-1.20%, P is less than or equal to 0.006%, S is less than or equal to 0.003%, Nb: 0.022-0.053%, V: 0.042-0.078%, Ti: 0.008-0.023%, Als: 0.012-0.035%, Ca: 0.0024-0.0069%, Cu is less than or equal to 0.05%, Mo + Cr is less than or equal to 0.10%, Ni is less than or equal to 0.12%, As is less than or equal to 0.010%, Sn is less than or equal to 0.010%, and the balance is Fe and inevitable impurities, and the chemical components also need to satisfy the formula: Ca/S is 2.3-2.4, C + Mn/6+ V/5 is less than or equal to 0.325 percent.
TABLE 1 inventive and comparative examples of the invention chemical composition (wt%)
TABLE 2 tabulation of values of the main process parameters for each example of the invention and comparative example
TABLE 3 results of mechanical property measurements of examples of the present invention and comparative examples
The steel plate 1/4 and 1/2 of the steel plate of the invention and the steel plate of the invention are respectively sampled to carry out normal temperature tensile property, longitudinal impact energy at 40 ℃ and full thickness Z-direction property tests, and the low temperature impact test of a submerged arc welding heat affected zone is carried out. The comparative performance results show that: the product of the invention has better comprehensive performance and low-temperature impact toughness of a welding heat affected zone, and the steel plate produced by the method of the invention has the characteristics of high strength, high plasticity, low yield ratio, excellent low-temperature toughness, good performance uniformity and the like, and especially the finished steel plate has excellent Z-direction performance and welding performance. Compared with the prior art, the steel of the invention does not need to add a large amount of precious metals such as Mo, Cr and the like, has low alloy cost and simple and easy production process, can be implemented in various metallurgical enterprises in large scale, and can be widely applied to various steel structure projects such as buildings, ocean platforms, pipelines, bridges, factories and mines, stadiums and the like.
The embodiments described above are merely specific examples of the present invention exemplified for explaining the present invention, and do not limit the present invention in any way, and any insubstantial changes from the contents and forms described above, which do not depart from the scope of the claims of the present invention, should be construed as falling within the scope of the claims of the present invention.
Claims (4)
1. A method for producing a steel plate for welded structures excellent in Z-direction performance from a continuous casting slab under a small compression ratio condition is characterized by comprising the following steps:
(1) molten iron treatment: the raw material molten iron is required to have P less than or equal to 0.10 percent, S less than or equal to 0.05 percent, As less than or equal to 0.010 percent, Sn less than or equal to 0.010 percent, KR deep desulfurization molten iron temperature more than or equal to 1250 ℃, desulfurization end point S less than or equal to 0.002 percent and low-sulfur scrap steel less than or equal to 15 percent;
(2) smelting in a converter: charging scrap steel, molten iron and low-sulfur active lime into a furnace, wherein the oxygen lance position is 200mm, the oxygen pressure is 1.0-1.2 MPa, and the oxygen flow is 3.6-4.2 Nm3The oxygen supply time is 13-15 min, fluorite with the weight of less than or equal to 2.5kg/t is added during the converting period for desulfurization and slag melting, C is more than or equal to 0.05% and less than or equal to 0.07% before tapping, and P is less than or equal to 0.003%;
(3) refining outside the furnace: LF treatment time is 45-55 min, outbound S is less than or equal to 0.003%, and strict nitrogen increment is less than or equal to 0.002%;
(4) and (3) vacuum treatment: the temperature of molten steel is more than or equal to 1580 ℃, the vacuum degree is less than or equal to 0.13kPa, the treatment time is 15-25 min, the adding amount of a CaSi wire is 0.6-0.8 kg/t, and then the soft argon blowing time is controlled to be more than or equal to 5 min;
(5) continuous casting: strictly adopting full-process protective pouring, strictly controlling the nitrogen increment to be less than or equal to 0.001%, controlling the superheat degree to be 15-20 ℃, controlling the pulling speed to be 0.75m/min, and carrying out totally-closed slow cooling for more than 72 hours at a position close to a wind shield after a casting blank is off a line;
(6) heating: heating the casting blank to 1260-1280 ℃, and controlling the total time of the casting blank in the furnace to be 420-450 min, wherein the soaking time of the steel blank is controlled to be 70-80 min;
(7) rolling and cooling: the initial rolling temperature of rough rolling is 1040-1080 ℃, 3 passes are finished, and the single-pass reduction is more than or equal to 45 mm; finishing at the rolling start temperature of 820-840 ℃ for 3-4 times; the laminar cooling speed is 18-22 ℃/s, the final cooling temperature of the surface of the steel plate is 560-570 ℃, and then the steel plate is cooled to 350 ℃ in air and is subjected to totally-enclosed stacking and slow cooling to the room temperature at the position close to the wind shield;
(8) and (3) heat treatment: the quenching temperature is 900-910 ℃, and the in-furnace time (2.1 +/-0.05) min/mm; the tempering temperature is 610-630 ℃, the in-furnace time (2.35 +/-0.05) min/mm, and the steel plate is air-cooled to the room temperature after being taken out of the furnace.
2. The method for producing a steel plate for welded structures excellent in Z-directional properties from a continuous cast slab under a small compression ratio condition according to claim 1, characterized in that: the thickness of the casting blank is 300mm, and the compression ratio is not less than 2.75 and not more than 2.30.
3. The method for producing a steel plate for welded structures excellent in Z-directional properties from a continuous cast slab under a small compression ratio condition according to claim 1, characterized in that: the casting blank comprises the following chemical components in percentage by mass: c: 0.10 to 0.17%, Si: 0.15 to 0.50%, Mn: 0.78-1.20%, P is less than or equal to 0.006%, S is less than or equal to 0.003%, Nb: 0.022-0.053%, V: 0.042-0.078%, Ti: 0.008-0.023%, Als: 0.012-0.035%, Ca: 0.0024-0.0069%, Cu is less than or equal to 0.05%, Mo + Cr is less than or equal to 0.10%, Ni is less than or equal to 0.12%, As is less than or equal to 0.010%, Sn is less than or equal to 0.010%, and the balance is Fe and inevitable impurities, and the chemical components also need to satisfy the formula: Ca/S = 2.3-2.4, and C + Mn/6+ V/5 is less than or equal to 0.325%.
4. The method for producing a steel plate for welded structures excellent in Z-directional properties from a continuous cast slab under a small compression ratio condition according to claim 1, characterized in that: the Z-direction performance of the finished steel plate is more than or equal to 65 percent.
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