CN111926256A - Ultra-wide non-anisotropic steel plate with width larger than or equal to 3500mm and production method thereof - Google Patents
Ultra-wide non-anisotropic steel plate with width larger than or equal to 3500mm and production method thereof Download PDFInfo
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
- B21B45/0203—Cooling
- B21B45/0209—Cooling devices, e.g. using gaseous coolants
- B21B45/0215—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes
- B21B45/0218—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes for strips, sheets, or plates
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
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- 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
- 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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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—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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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2201/00—Special rolling modes
- B21B2201/02—Austenitic rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/20—Temperature
Abstract
The invention discloses an ultra-wide non-anisotropic steel plate with the width more than or equal to 3500mm and a production method thereof, wherein the steel plate comprises the following components in percentage by weight: c: 0.10 to 0.16%, Mn: 0.3-0.8%, Si: 0.15-0.50%, P is less than or equal to 0.020%, S is less than or equal to 0.003%, Nb: 0.010-0.025%, Als: 0.010-0.045%, Ti: 0.030-0.050%, Ca: not less than 0.0005%, N: less than or equal to 0.0050 percent, and the balance of Fe and inevitable impurity elements; the super-wide non-anisotropic steel plate with the width of more than or equal to 3500mm, which is prepared by the method, has the yield strength of more than or equal to 420MPa at normal temperature, the tensile strength of more than or equal to 540MPa, the elongation of more than or equal to 20 percent, the transverse and longitudinal strength difference within 15MPa, the transverse and longitudinal impact energy at minus 40 ℃ of more than or equal to 120J, has high strength, high toughness, no anisotropy and no plate thickness effect, and can meet the performance requirements of structural steel such as bridges and the like.
Description
Technical Field
The invention relates to the technical field of steel materials, in particular to an ultra-wide non-anisotropic steel plate with the width of more than or equal to 3500mm and a production method thereof.
Background
Along with the continuous acceleration of the urbanization process in China, the width of bridge floors of large bridges for crossing rivers and rivers in cities is continuously increased, the quantity of overlong and overlong steel plates for processing and building bridge steel box girder structures is continuously increased, higher requirements are provided for the performances of the steel plates in different directions, if the transverse and longitudinal impact energy meets the standard requirements, the difference of the longitudinal and transverse strength is within 15MPa, the production difficulty of medium plate production enterprises is invisibly increased, and the product percent of pass is lower.
Before the present invention, the present invention relates to the production of steel sheets having low anisotropy at home and abroad. For example, patent CN1989266A discloses a "high strength steel plate with small acoustic anisotropy and excellent weldability and manufacturing method thereof", which mainly adopts three-stage controlled rolling mode in the rolling process, and controls the ratio of grain length and width by controlling the temperature and total compression ratio in each rolling stage, but in order to obtain high strength steel plate with tensile strength of more than 570MPa level, noble elements such as Mo, Cr, Cu, etc. need to be added, and the problem of steel plate width is not mentioned, so the manufacturing method thereof may not be suitable for the production of ultra-wide steel plates.
Patent No. CN101305110A discloses "a high strength steel sheet having a yield stress of 450MPa or more and a tensile strength of 570MPa or more, which is small in acoustic anisotropy, excellent in weldability," and a method for manufacturing the same ", which is designed using a composition having a C content of 0.03 to 0.07% and a Mn content up to 2.0%, and rolling also uses a three-stage controlled rolling method, and increases the steel anisotropy by controlling the temperature and the total compression ratio in each rolling stage, but it does not mention how to control MnS inclusions that may be generated at a Mn content of 2.0% to increase the steel anisotropy, and it also does not mention the problem of the steel sheet width, and thus the manufacturing method thereof may not be applied to the production of ultra-wide steel sheets.
Therefore, the invention provides an ultra-wide non-anisotropic steel plate and a manufacturing method thereof aiming at the problems, and the manufacturing of the ultra-wide steel plate with the width being more than or equal to 3500mm is met.
Disclosure of Invention
The invention aims to provide an ultra-wide non-anisotropic steel plate with the width of more than or equal to 3500mm and a production method thereof, wherein the yield strength of the steel plate at normal temperature is more than or equal to 420MPa, the tensile strength is more than or equal to 540MPa, the elongation is more than or equal to 20%, the transverse and longitudinal strength difference is within 15MPa, the transverse and longitudinal impact energy at minus 40 ℃ is more than or equal to 120J, and the steel plate has high strength, high toughness, no anisotropy and no plate thickness effect and can meet the performance requirements of structural steel such as bridges and the like.
In order to achieve the purpose, the invention provides an ultra-wide non-anisotropic steel plate with the width being more than or equal to 3500mm, which comprises the following components in percentage by weight:
c: 0.10 to 0.16%, Mn: 0.3-0.8%, Si: 0.15-0.50%, P is less than or equal to 0.020%, S is less than or equal to 0.003%, Nb: 0.010-0.025%, Als: 0.010-0.045%, Ti: 0.030-0.050%, Ca: not less than 0.0005%, N: less than or equal to 0.0050 percent, and the balance of Fe and inevitable impurity elements.
The transverse and longitudinal yield strength of the steel plate at normal temperature is more than or equal to 420MPa, the tensile strength is more than or equal to 540MPa, the elongation is more than or equal to 20%, and the transverse and longitudinal strength difference is within 15MPa, and the transverse and longitudinal impact energy at minus 40 ℃ is more than or equal to 120J.
The thickness range of the steel plate is 10-100 mm.
The invention relates to a production method of an ultra-wide non-anisotropic steel plate with the width of more than or equal to 3500mm, which comprises LF external refining, RH vacuum circulation treatment, slab continuous casting, casting blank heating, controlled rolling, cooling and stacking slow cooling, and is characterized in that:
(1) LF and RH treatment are adopted in smelting, the S content is guaranteed to be less than or equal to 0.003 percent, steel grades are fed into a calcium wire after RH treatment, and then soft argon blowing time is guaranteed to be more than or equal to 8 min; the casting blanks are stacked or pit-cooled for more than 48 hours;
(2) the selected continuous casting slab ensures that the total compression ratio is more than or equal to 3.0;
(3) heating the continuous casting slab, and controlling the temperature of a soaking section to be 1150-1250 ℃ and the soaking time to be 45-60 minutes;
(4) rolling a steel plate by adopting a controlled rolling process of a rough rolling stage and a finish rolling stage, wherein the rough rolling stage adopts high temperature and high pressure, the steel plate is taken out of a furnace and descaled, and then is rolled, the initial rolling temperature is 1130-1200 ℃, the number of transverse rolling widening passes and longitudinal rolling passes is ensured to be the same in the rough rolling stage, the mean value of the pass pressure is ensured to be more than or equal to 20mm, the total rolling passes in the rough rolling stage are 8-12, the rolling pass interval is 10-15 s, the final rolling temperature is controlled to be more than 1100 ℃, and the rolling stop thickness is not more than 2 times of the thickness of a finished product; the initial rolling temperature of the finish rolling is 880-1000 ℃, and the final rolling temperature of the finish rolling is controlled to be 860-890 ℃;
(5) and immediately performing water cooling after the steel plate is rolled, controlling the temperature before entering water to be more than or equal to 750 ℃, controlling the final cooling temperature of water cooling to be 500-600 ℃, flattening the steel plate, cooling to 400 ℃ in the air, and then taking off the line, stacking and slowly cooling.
The function and control of each component in the invention have the following characteristics:
c: c is an element for expanding an austenite phase region, can obviously improve the strength of the steel, but has adverse effects on the plasticity, toughness and welding performance of the steel. When the C content exceeds 0.23%, the welding performance can slide down greatly, and the C content of the low-alloy structural steel used in welding occasions cannot exceed 0.2%. In order to ensure that the steel plate meets the required strength requirement and does not damage the toughness and weldability of the steel, the content range of C is controlled to be 0.10-0.16%.
Mn: mn is used as a substitutional atom in steel, an austenite phase region is enlarged, the A3 temperature is reduced, pearlite is refined, the strength of the low-carbon and medium-carbon pearlite steel is obviously improved, the ductility and plasticity of a steel plate are not obviously affected while the strength is increased, and the ferrite and the pearlite are strengthened by utilizing manganese in common low-alloy steel, so that the strength of the steel is improved. Mn is added into steel and forms plastic MnS inclusion with S, and the steel plate is extended in the rolling process to cause the increase of the anisotropy of the steel plate. And when the Mn content exceeds 1.0%, the welding performance is reduced, and in order to obtain the best matching effect of the yield strength and the weldability of the steel, the Mn content is controlled to be 0.3-0.8%.
Si: si improves the strength of steel in a solid solution strengthening mode and is a good deoxidizer in a smelting process, but when the content of silicon in the steel is too high, the yield ratio is increased, the plasticity and the toughness of the steel are reduced, and in order to obtain a steel plate with low yield ratio, high toughness and high plasticity, the content range of Si is controlled to be 0.15-0.50%.
P: p is a harmful element in steel, the content of P is strictly controlled, the content of P can increase the cold brittleness tendency of steel, reduce the low-temperature toughness of steel and deteriorate the welding performance, so the content of P is controlled to be less than or equal to 0.020%.
S: s is easy to form sulfides with alloy elements in steel, is unfavorable for low-temperature toughness, is unfavorable for toughness, elongation and reduction of area of steel due to sulfide inclusion, causes fatigue cracks due to stress concentration of container hard gas, reduces S content, reduces the level of non-metallic inclusions in steel, is favorable for ensuring impact toughness, improves Z-direction performance, reduces anisotropy of steel plates and reduces poor transverse and longitudinal performance, so that the content range of S is controlled to be less than or equal to 0.003 percent.
Nb: nb can obviously improve the austenite recrystallization temperature of the steel, enlarge the range of a non-recrystallization region and facilitate the realization of high-temperature rolling. The niobium can also inhibit the growth of austenite grains, has remarkable fine grain strengthening and precipitation strengthening effects, can remarkably improve the yield strength and the impact toughness and reduce the ductile-brittle transition temperature of the steel by adding the niobium into the steel, but is influenced by the limit value of the content of C and the heating temperature, the excessively high Nb cannot be dissolved in the solution and deteriorates the welding performance, so the control range of the Nb addition content is 0.010-0.025 percent.
Al: al is a main deoxidizing element in steel, and can fix N element, refine crystal grains and improve the toughness of the steel, and in order to ensure that the deoxidizing and the nitrogen fixing are more sufficient, the content range of Al is controlled to be more than or equal to 0.015 percent.
Ti: the strong carbonitride element of Ti, which readily bonds with O, C, N, forms very stable Ti (C, N), which slowly melts into solid solution only above 1000 ℃ and effectively blocks the growth of austenite grains when the billet is heated. But when the titanium is added in a large amount, the titanium nitride is coarsened, the low-temperature toughness is reduced, and trace titanium is very effective in improving the toughness of a welding heat affected zone.
N: the steel has a solid solution strengthening effect, but when the steel is tempered after quick cooling or stays at room temperature for a long time, micro-nitrides are precipitated, so that the low-carbon steel has an aging phenomenon, the toughness is reduced while the strength and the hardness are improved, and the fracture sensitivity is increased, so that the macro-structure looseness or pores can be caused by the overhigh content of residual nitrogen in the steel and the control is needed, and therefore, the content range of N is controlled to be less than or equal to 0.005 percent.
Ca: the trace calcium can be used as a purifying agent for deoxidation and desulphurization in steel, improves the form of non-metallic inclusions, and is used for treating clean steel by calcium.
According to the production method provided by the invention, the refining process is optimized, the S content is controlled, large-particle MnS inclusions are reduced, the plastic inclusions such as MnS are subjected to denaturation treatment by calcium wire feeding, and then the plastic inclusions are fully floated by soft blowing, so that the anisotropy of the steel plate is prevented from being increased due to the fact that the plastic inclusions such as MnS extend along the longitudinal direction in the rolling process.
The heating process is set below 1250 ℃, so as to prevent austenite grains from coarsening to seriously affect the toughness, ensure enough soaking time and fully and uniformly diffuse the element segregation and the like of the steel grade.
The rolling process and the cooling process adopt high temperature and high pressure in the rough rolling stage, the initial rolling temperature is controlled to be less than or equal to 1200 ℃, the final rolling temperature is more than 1100 ℃, in the rough rolling stage, the dynamic recrystallization degree of transverse austenite and longitudinal austenite is ensured to be the same by controlling the same number of widening passes and longitudinal passes of transverse rolling, the interval of rolling passes is 10-15 s, the full recovery after the recrystallization of austenite is ensured, and the uniformity of grains is ensured. The total rolling reduction in the finish rolling stage is not more than 50%, and by controlling the reduction, the aspect ratio of the deformed austenite grains can be controlled within a low range, and the aspect ratio of the deformed austenite grains can be further reduced by controlling the finish rolling temperature of the finish rolling to 860 ℃ or higher, and the anisotropy of the steel can be further reduced. After the steel plates are cooled, the steel plates are stacked and slowly cooled, so that the uniform release of stress in the steel is ensured, and the isotropy of the steel plates is ensured. Thereby obtaining the ultra-wide non-anisotropic steel plate with the thickness of more than or equal to 3500 mm.
The super-wide non-anisotropic steel plate with the width of more than or equal to 3500mm, which is prepared by the method, has the yield strength of more than or equal to 420MPa at normal temperature, the tensile strength of more than or equal to 540MPa, the elongation of more than or equal to 20 percent, the transverse and longitudinal strength difference within 15MPa, the transverse and longitudinal impact energy at minus 40 ℃ of more than or equal to 120J, has high strength, high toughness, no anisotropy and no plate thickness effect, and can meet the performance requirements of structural steel such as bridges and the like.
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 chemical components contained in the steel plate according to each example of the present invention in percentage by mass;
table 2 below is a table showing the results of mechanical property tests of the steel sheets according to the examples of the present invention.
TABLE 1 tabulated list of chemical components and weight percent contents (wt%) in the examples of the invention
Example 1
The present example illustrates the production of a super wide non-anisotropic steel sheet having a width of 3650mm, and the components and weight percentages of the steel sheet of the present example are shown in table 1.
The production method of the ultra-wide non-anisotropic steel plate with the width of 3650mm comprises the following steps:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 10 min; stacking the casting blanks for 49 h;
(2) the size of the selected continuous casting plate blank is 200 × 2000mm × L;
(3) the temperature of the soaking section of the continuous casting slab is 1195 ℃, and the soaking time is 52 minutes;
(4) rolling a steel plate by adopting a rough rolling and finish rolling two-stage rolling process, wherein the rough rolling stage adopts high temperature and high pressure, the initial rolling temperature is controlled to be 1180 ℃, the transverse rolling widening pass number and the longitudinal rolling pass number are both 4, the rolling pass interval is 15s, the final rolling temperature is controlled to be 1120 ℃, and the rolling stop thickness is 40 mm; the initial rolling temperature of finish rolling is less than or equal to 990 ℃, and the final rolling temperature is controlled to 872 ℃;
(5) the temperature of the rolled steel plate before entering water is 755 ℃, the final cooling temperature of water cooling is 582 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing steps has the specification of 10mm 3650mm L, and the mechanical properties of the steel plate are shown in Table 2.
Example 2
This example illustrates the production of a 3720mm wide ultra-wide non-anisotropic steel sheet, the components and weight percentages of which are shown in table 1.
The production method of the ultra-wide anisotropic-free steel plate with the width of 3720mm comprises the following steps:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 12 min; stacking the casting blanks for 52 h;
(3) the size of the selected continuous casting plate blank is 250mm x 2200mm x L;
(3) the temperature of the soaking section of the continuous casting slab is 1182 ℃, and the soaking time is 49 minutes;
(4) rolling a steel plate by adopting a two-stage rolling process of rough rolling and finish rolling, wherein the rough rolling stage adopts high temperature and high pressure, the starting rolling temperature is controlled to be 1162 ℃, the transverse rolling widening pass number and the longitudinal rolling pass number are ensured to be 5, the rolling pass interval is 12s, the final rolling temperature is 1121 ℃, and the rolling stopping thickness is 50 mm; the initial rolling temperature of finish rolling is not more than 900 ℃, and the final rolling temperature is controlled to 865 ℃;
(5) the temperature of the rolled steel plate before water feeding is 772 ℃, the final cooling temperature of water cooling is 532 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing steps has the thickness specification of 20mm 3720mm L, and the mechanical properties of the steel plate are shown in Table 2.
Example 3
In this example, the invention is explained by taking the production of a super wide non-anisotropic steel plate with a width of 3580mm as an example, and the components and the weight percentage contents of the steel plate of this example are shown in table 1.
The production method of the ultra-wide anisotropic-free steel plate with the width of 3580mm comprises the following steps of:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 8 min; stacking the casting blanks for 62 h;
(2) the size of the selected continuous casting slab is 300mm 2250mm L;
(3) the temperature of the soaking section of the continuous casting slab is 1246 ℃, and the soaking time is 60 minutes;
(4) rolling a steel plate by adopting a two-stage rolling process of rough rolling and finish rolling, wherein the rough rolling stage adopts high temperature and high pressure, the initial rolling temperature is 1199 ℃, the transverse rolling widening pass number and the longitudinal rolling pass number are both ensured to be 5, the rolling pass interval is 15s, the final rolling temperature is 1125 ℃, and the rolling stop thickness is 75 mm; the initial rolling temperature of finish rolling is less than or equal to 912 ℃, and the final rolling temperature is controlled to be 884 ℃;
(5) the temperature of the steel plate before water feeding is 785 ℃ after rolling is finished, the final cooling temperature of water cooling is 508 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing technology steps has the thickness specification of 40 mm-3580 mm-L, and the mechanical properties of the steel plate are shown in Table 2.
Example 4
This example illustrates the invention by taking the production of a super wide non-anisotropic steel sheet with a width of 3610mm as an example, and the components and weight percentage contents of the steel sheet of this example are shown in table 1.
The production method of the ultra-wide non-anisotropic steel plate with the width of 3610mm comprises the following steps:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 8 min; stacking the casting blanks for 62 h;
(2) the size of the selected continuous casting plate blank is 300mm x 2300mm x L;
(3) the temperature of the soaking section of the continuous casting slab is 1225 ℃, and the soaking time is 40 minutes;
(4) rolling a steel plate by adopting a rough rolling and finish rolling two-stage rolling process, wherein the rough rolling stage adopts high temperature and high pressure, the starting rolling temperature is controlled to 1176, the transverse rolling widening pass number and the longitudinal rolling pass number are both 5, the rolling pass interval is 14s, the final rolling temperature is 1102 ℃, and the rolling stop thickness is 90 mm; the initial rolling temperature of finish rolling is less than or equal to 875 ℃, and the final rolling temperature is controlled to 864 ℃;
(5) the temperature of the steel plate before water feeding is 801 ℃ after rolling is finished, the final cooling temperature of water cooling is 512 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing steps has the thickness specification of 60mm 3610mm L, and the mechanical properties of the steel plate are shown in Table 2.
Example 5
This example illustrates the production of a 3575mm wide ultra-wide non-anisotropic steel sheet, the components and weight percentages of which are shown in table 1.
The production method of the ultra-wide anisotropic-free steel plate with the width of 3575mm comprises the following steps of:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 9 min; stacking the casting blanks for 45 hours;
(2) the size of the selected continuous casting plate blank is 350mm 2300mm L;
(3) the temperature of the soaking section of the continuous casting slab is 1156 ℃, and the soaking time is 59 minutes;
(4) rolling a steel plate by adopting a rough rolling and finish rolling two-stage rolling process, wherein the rough rolling stage adopts high temperature and high pressure, the initial rolling temperature is controlled at 1138, the transverse rolling widening pass number and the longitudinal rolling pass number are both ensured to be 6, the rolling pass interval is 15s, the final rolling temperature is 1105 ℃, and the rolling stop thickness is 100 mm; the initial rolling temperature of finish rolling is not more than 883 ℃, and the final rolling temperature is controlled to be 875 ℃;
(5) the temperature of the steel plate before water feeding is 811 ℃ after rolling is finished, the final cooling temperature of water cooling is 546 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing steps has the thickness specification of 80mm x 3575mm x L, and the mechanical properties of the steel plate are shown in Table 2.
Example 6
This example illustrates the invention by taking the production of a super wide non-anisotropic steel sheet with a width of 3610mm as an example, and the components and weight percentage contents of the steel sheet of this example are shown in table 1.
The production method of the ultra-wide non-anisotropic steel plate with the width of 3610mm comprises the following steps:
(1) LF and RH treatment are adopted in smelting, calcium wires are fed into steel after RH treatment, and then soft argon blowing time is 9 min; stacking the casting blanks for 45 hours;
(2) the size of the selected continuous casting plate blank is 350mm 2350mm L;
(3) the temperature of the soaking section of the continuous casting slab is below 1201 ℃, and the soaking time is 51 minutes;
(4) rolling a steel plate by adopting a two-stage rolling process of rough rolling and finish rolling, wherein the rough rolling stage adopts high temperature and high pressure, the rolling start temperature is 1165, the transverse rolling widening pass number and the longitudinal rolling pass number are both 5, the rolling pass interval is 10s, the finish rolling temperature is 1127 ℃, and the rolling stop thickness is 120 mm; the initial rolling temperature of finish rolling is less than or equal to 895 ℃, and the final rolling temperature is controlled to be 885 ℃;
(5) the temperature of the rolled steel plate before water feeding is 821 ℃, the final cooling temperature of water cooling is 566 ℃, and the steel plate is cooled to 400 ℃ in the air after being leveled and is subjected to line stacking and slow cooling. The steel plate manufactured by adopting the element component content and the processing technology steps has the thickness specification of 100mm 3502mm L, and the mechanical properties of the steel plate are shown in Table 2.
TABLE 2 mechanical Properties of the steel sheets produced according to the examples of the present invention
As can be seen from Table 2, the steel sheets produced by the composition and production method of the present invention were subjected to a room temperature tensile test and a-40 ℃ longitudinal impact test, and the results were as follows: the yield strength of the steel plate at normal temperature is more than or equal to 420MPa, the tensile strength is more than or equal to 540MPa, the elongation is more than or equal to 20%, the transverse and longitudinal strength difference is within 15MPa, the transverse and longitudinal impact energy at-40 ℃ is more than or equal to 120J, the steel plate has high strength, high toughness, no anisotropy and no plate thickness effect, and can meet the performance requirements of structural steel such as bridges and the like.
Claims (4)
1. An ultra-wide non-anisotropic steel plate with the width more than or equal to 3500mm is characterized by comprising the following components in percentage by weight:
c: 0.10 to 0.16%, Mn: 0.3-0.8%, Si: 0.15-0.50%, P is less than or equal to 0.020%, S is less than or equal to 0.003%, Nb: 0.010-0.025%, Als: 0.010-0.045%, Ti: 0.030-0.050%, Ca: not less than 0.0005%, N: less than or equal to 0.0050 percent, and the balance of Fe and inevitable impurity elements.
2. The ultra-wide non-anisotropic steel plate with the width being more than or equal to 3500mm as claimed in claim 1, is characterized in that: the transverse and longitudinal yield strength of the steel plate at normal temperature is more than or equal to 420MPa, the tensile strength is more than or equal to 540MPa, the elongation is more than or equal to 20%, and the transverse and longitudinal strength difference is within 15MPa, and the transverse and longitudinal impact energy at minus 40 ℃ is more than or equal to 120J.
3. The ultra-wide non-anisotropic steel plate with the width being more than or equal to 3500mm as claimed in claim 1, is characterized in that: the thickness range of the steel plate is 10-100 mm.
4. The method for producing the ultra-wide non-anisotropic steel plate with the width being more than or equal to 3500mm according to claim 1, which comprises LF external refining, RH vacuum circulation treatment, slab continuous casting, casting blank heating, controlled rolling, cooling and stacking slow cooling, and is characterized in that:
(1) LF and RH treatment are adopted in smelting, the S content is guaranteed to be less than or equal to 0.003 percent, steel grades are fed into a calcium wire after RH treatment, and then soft argon blowing time is guaranteed to be more than or equal to 8 min; the casting blanks are stacked or pit-cooled for more than 48 hours;
(2) the selected continuous casting slab ensures that the total compression ratio is more than or equal to 3.0;
(3) heating the continuous casting slab, and controlling the temperature of a soaking section to be 1150-1250 ℃ and the soaking time to be 45-60 minutes;
(4) rolling a steel plate by adopting a controlled rolling process of a rough rolling stage and a finish rolling stage, wherein the rough rolling stage adopts high temperature and high pressure, the steel plate is taken out of a furnace and descaled, and then is rolled, the initial rolling temperature is 1130-1200 ℃, the number of transverse rolling widening passes and longitudinal rolling passes is ensured to be the same in the rough rolling stage, the mean value of the pass pressure is ensured to be more than or equal to 20mm, the total rolling passes in the rough rolling stage are 8-12, the rolling pass interval is 10-15 s, the final rolling temperature is controlled to be more than 1100 ℃, and the rolling stop thickness is not more than 2 times of the thickness of a finished product; the initial rolling temperature of the finish rolling is 880-1000 ℃, and the final rolling temperature of the finish rolling is controlled to be 860-890 ℃;
(5) and immediately performing water cooling after the steel plate is rolled, controlling the temperature before entering water to be more than or equal to 750 ℃, controlling the final cooling temperature of water cooling to be 500-600 ℃, flattening the steel plate, cooling to 400 ℃ in the air, and then taking off the line, stacking and slowly cooling.
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