CN109207858B - Production method of low-alloy ultrahigh-strength steel Q1100E sheet - Google Patents
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Abstract
A production method of a low-alloy ultrahigh-strength steel Q1100E sheet comprises the following components, by weight, 0.15-0.20% of C, 0.10-0.30% of Si, 0.80-1.20% of Mn, 0.015% or less of P, 0.003% or less of S, 0.02-0.05% of Al, 0.010-0.020% of Nb, 0.030-0.060% of V, 0.008-0.020% of Ti, 0.10-0.30% of Cr, 0.50-0.80% of Mo, 0.50% or less of Ni, 0.0015-0.0040% of B, 0.0020% of O, 0.0050% or less of N, 0.00006% of Ti × N, 0.×% of S or less of Mn, 0.0024% of Nb × C or less of 0.0030% of C, 0.52-0.56% of CEV, the balance Fe and inevitable impurities, and key production steps of smelting, primary-secondary-fire, secondary fire, uniform cold-rolled steel sheet, uniform cold-bending and uniform in residual stress.
Description
Technical Field
The invention belongs to the technical field of low alloy steel production, and particularly relates to a production method of a low alloy ultrahigh strength steel Q1100E sheet.
Background
Low-alloy high-strength steel has been widely used in the field of engineering machinery due to its good toughness and weldability. In recent years, with the rapid development of modern equipment manufacturing technologies such as large-tonnage truck cranes, heavy-duty crawler cranes, large concrete pump trucks and the like, low-alloy ultrahigh-strength steels with higher strength levels are valued by various large engineering machinery manufacturers, the demand thereof increases year by year, and the use specifications are mainly thin plates.
However, with the ultra-high strength of steel materials, the ductility and toughness of steel plates are reduced, and the welding performance is deteriorated. In the component and process design of the existing low-alloy ultrahigh-strength steel with the yield strength of more than 1100MPa, the matching of toughness and weldability are mainly considered, for example, U.S. Pat. No. 5,5798004, European patent EP0288054A2, Japanese patent No. 63-79921, Japanese patent No. 4-285119, Chinese patent No. 3, 102505096B, CN104046908B and the like, the improvement on the unevenness of steel plates, especially thin plates, is not related, and meanwhile, the reports on the improvement of the bending capability of the steel plates in the aspect of industrial production technology of the steel plates are few, which are the troublesome problems encountered by many engineering machinery production enterprises when using low-alloy ultrahigh-strength steel plates.
Disclosure of Invention
The invention aims to provide a production method of a low-alloy ultrahigh-strength steel Q1100E sheet, wherein the thickness of a steel plate is 8-12 mm, and the unevenness of the steel plate is controlled to be less than or equal to 3mm/m on the basis of ensuring the strength, toughness and weldability of the steel plate; the cold bending of 180 degrees under the bending core diameter of 2 times of the plate thickness has no crack.
The technical scheme of the invention is as follows:
the production method of the low-alloy ultrahigh-strength steel Q1100E sheet comprises the following chemical components by weight percent, C = 0.15-0.20, Si = 0.10-0.30, Mn = 0.80-1.20, P is less than or equal to 0.015, S is less than or equal to 0.003, Al = 0.02-0.05, Nb = 0.010-0.020, V = 0.030-0.060, Ti = 0.008-0.020, Cr = 0.10-0.30, Mo = 0.50-0.80, Ni is less than or equal to 0.50, B = 0.0015-0.0040, O is less than or equal to 0.0020, N is less than or equal to 0.0050, Ti × N is less than or equal to 0.00006, Mn × S is less than or equal to 0.0024, Nb × C is less than or equal to 0.0030, CEV = 0.52-0.56, the balance is Fe and unavoidable impurities are more than or equal to 0.5 + Cr +/C +/Mn (CEV +/C +/Cu) (15 +):
(1) smelting and casting: the method comprises the steps of cleaning and steelmaking by adopting molten iron pretreatment, converter smelting, LF refining and RH vacuum treatment, then continuously casting the steel into a high-quality casting blank, and controlling the hot pickling of the casting blank to be in accordance with the Mannesmann center segregation level of 1-2.
(2) First longitudinal rolling: heating the casting blank at high temperature and longitudinally rolling the casting blank into a plate blank with the thickness of 60-100 mm, wherein the compression ratio is more than or equal to 3.0; and then finishing the plate blank into a plurality of fire blanks by adopting flame cutting, wherein the length of one fire blank = the width of the finished product + (60-120) mm.
(3) And (3) second-fire cross rolling: performing transverse rolling on a fire blank with the length as wide as the width by adopting a heating mode of rapid heating, short-time heat preservation and low-temperature discharging, wherein the rolling finishing temperature is 800-900 ℃; after rolling, air cooling is carried out to 600-650 ℃, then accelerated cooling is carried out to 350-400 ℃ at a cooling speed of 15-20 ℃/s, and then air cooling is carried out to the room temperature.
(4) Tempering: the tempering temperature is 200-250 ℃, and the tempering time is 60-90 min.
(5) Cold straightening: and (3) carrying out multi-pass straightening by adopting an 11-roll cold straightening machine according to a mode of straightening the turning plate again after straightening so as to control the unevenness of the steel plate to be less than or equal to 3 mm/m.
In the step (2), preferably, the heating temperature of the casting blank is more than or equal to 1230 ℃, and the soaking time is more than or equal to 45 min; the finishing temperature of the first stage is more than or equal to 1150 ℃, and the finishing temperature of the second stage is less than or equal to 820 ℃; and (3) after rolling, carrying out accelerated cooling at the cooling speed of 3-5 ℃/s and the re-reddening temperature of 650-700 ℃, and then, entering a slow cooling pit for cooling to room temperature. Further preferably, the maximum pass reduction rate of the first-stage rolling is more than or equal to 15 percent; the cumulative reduction rate of the second stage rolling is more than or equal to 50 percent.
In the step (3), preferably, the heating temperature of the first fire blank is 1100-1150 ℃, the heating time is 30-90 min, and the soaking time is 10-20 min; rolling by adopting a high-chromium iron roller, wherein the hardness of the roller body is 75-85 HSD; and (4) carrying out low-speed constant pre-straightening in the air cooling process after rolling, wherein the straightening speed is 0.4-0.6 m/s. Further preferably, the pre-straightening is performed for 1 to 3 times.
The technical principle of the invention is as follows:
the method adopts low carbon equivalent to improve the weldability of the steel plate in terms of component design, adds hardenability elements such as Mo, Cr, Ni and B and microalloying elements such as V, Ti and Nb to improve the toughness of the steel plate, controls the Ti × N product, Mn × S product and Nb × C product to control the precipitation of large-size TiN, MnS and NbC particles so as to improve the bending performance of the steel plate, and controls harmful elements such as P, S, O, N and the like and improves the uniformity of components by the processes of clean steelmaking, control of center segregation of a casting blank, secondary-fire forming and the like.
In the process design, grains are refined and the structure is uniform by secondary firing and controlling the rolling compression amount in the transverse direction and the longitudinal direction; the carbon atoms are promoted to be deviated and gathered on dislocation lines through air cooling after the two-fire rolling, and the air cooling is carried out after the accelerated cooling is carried out to a certain temperature in a martensite transformation region so as to improve the stability of the residual austenite, and finally a certain amount of M-A components which are distributed in a fine and dispersed mode are obtained, so that the bending performance of the steel plate is improved, and the residual structure stress is reduced; through low-temperature tempering and longer tempering time, on one hand, partial residual stress can be eliminated, on the other hand, supersaturated carbon is precipitated from martensite to improve plasticity, and the bending capability of the steel plate is improved; through multi-pass high-temperature pre-straightening and repeated plate-turning cold straightening, the requirements of the plate type and the unevenness of the steel plate are ensured, and meanwhile, the uniformity of the residual stress of the steel plate is improved, so that ideal shape and size precision can be obtained when the whole steel plate is bent.
The invention has the beneficial effects that: according to the method of the invention, the produced low-alloy ultrahigh-strength steel plate not only has good comprehensive mechanical properties: the yield strength is more than or equal to 1100MPa, the tensile strength is more than or equal to 1300MPa, the elongation is more than or equal to 15 percent, the Charpy impact energy at 40 ℃ is far greater than the standard value of 27J, and no crack is generated when the steel is cold-bent for 180 degrees under the bending core diameter of 2 times the plate thickness; the steel plate has good plate shape, the unevenness is less than or equal to 3mm/m, and meanwhile, the steel plate has uniform structure, uniform performance, small and uniform residual stress and excellent whole plate bending capability. The low-alloy ultrahigh-strength steel Q1100E sheet produced by the invention has high added value, can be supplied in batches, and can powerfully promote the development of engineering mechanical equipment in China to a large-scale, light-weight and high-efficiency green manufacturing road.
Drawings
Fig. 1 is a typical metallographic photograph of a low alloy ultra high strength steel Q1100E sheet according to the present invention.
Detailed Description
The invention is further illustrated by the following examples and figures.
The chemical compositions of the steels of the examples of the invention are shown in table 1, with the balance being Fe and unavoidable impurities.
The key production steps of the steel plate in the embodiment of the invention comprise: adopting molten iron pretreatment, converter smelting, LF refining and RH vacuum treatment for cleaning and steelmaking; then continuously casting the casting blank into a high-quality casting blank, and controlling the hot pickling of the casting blank to be in accordance with the Mannesmann center segregation level of 1-2; carrying out first-fire longitudinal rolling on a casting blank, then cooling the casting blank to room temperature in a slow cooling pit, and then carrying out second-fire transverse rolling by adopting a high-chromium iron roller, wherein the hardness of a roller body is 75-85 HSD; through twice controlled rolling and controlled cooling, then low-temperature tempering for a long time, finally, multi-pass straightening is carried out by adopting an 11-roll cold straightening machine according to a mode of straightening a turning plate again after straightening, and finally, the low-alloy ultrahigh-strength steel plate with good comprehensive mechanical property, excellent plate shape and 1100MPa grade yield strength is obtained. Other specific process parameters are shown in table 2.
Fig. 1 is a typical metallographic photograph of a low-alloy ultrahigh-strength steel Q1100E sheet according to the present invention, and it can be seen from the photograph that the structure of the steel sheet is composed of tempered martensite and M-a components in fine and dispersed distribution, and the structure is fine and uniform, such that the steel sheet according to the present invention has high toughness, high plasticity, and good cold-bending property, as shown in table 3.
Table 4 shows the results of the unevenness test of the steel sheets according to the examples of the present invention, and it can be seen that the low alloy ultrahigh strength steel Q1100E sheet of the present invention has a very good plate shape and the unevenness is not more than 3 mm/m.
TABLE 1 chemical composition of the steels of the examples (weight%,%)
TABLE 2 concrete Process parameters of the Steel sheets of the examples
TABLE 3 mechanical Properties of the steel sheets of the examples
TABLE 4 results of unevenness test of the steel sheets of examples
Claims (2)
1. The production method of the low-alloy ultrahigh-strength steel Q1100E is characterized in that the steel plate is 8-12 mm thick, and the steel comprises the following chemical components by weight percent of C = 0.15-0.20, Si = 0.10-0.30, Mn = 0.80-1.20, P is less than or equal to 0.015, S is less than or equal to 0.003, Al = 0.02-0.05, Nb = 0.010-0.020, V = 0.030-0.060, Ti = 0.008-0.020, Cr = 0.10-0.30, Mo = 0.50-0.80, Ni is less than or equal to 0.50, B = 0.0015-0.0040, O is less than or equal to 0.0020, N is less than or equal to 0.0050, Ti × N is less than or equal to 0.00006, Mn × S is less than or equal to 0.0024, Nb × C is less than or equal to 0.0030, CEV =0.52, the balance is Fe and unavoidable impurities are Fe and Cr + 5 +/C (the key production:
(1) smelting and casting: adopting molten iron pretreatment, converter smelting, LF refining and RH vacuum treatment for cleaning and steelmaking; then continuously casting the casting blank into a high-quality casting blank, and controlling the hot pickling of the casting blank to be in accordance with the Mannesmann center segregation level of 1-2;
(2) first longitudinal rolling: heating the casting blank at a high temperature and longitudinally rolling the casting blank into a plate blank with the thickness of 60-100 mm, wherein the heating temperature of the casting blank is more than or equal to 1230 ℃, and the soaking time is more than or equal to 45 min; the finishing temperature of the first stage is more than or equal to 1150 ℃, and the finishing temperature of the second stage is less than or equal to 820 ℃; the maximum pass reduction rate of the first stage rolling is more than or equal to 15 percent, and the accumulated reduction rate of the second stage rolling is more than or equal to 50 percent; the compression ratio is more than or equal to 3.0; after rolling, carrying out accelerated cooling at the cooling speed of 3-5 ℃/s and the re-reddening temperature of 650-700 ℃, and then cooling to room temperature in a slow cooling pit; then, finishing the plate blank into a plurality of first fire blanks by adopting flame cutting, wherein the length of the first fire blank = the width of a finished product + (60-120) mm;
(3) and (3) second-fire cross rolling: a heating mode of rapid heating, short-time heat preservation and low-temperature discharging is adopted, wherein the heating temperature of a first fire blank is 1100-1150 ℃, the heating time is 30-90 min, and the soaking time is 10-20 min; performing transverse rolling on the first fire blank with the length as wide, wherein the rolling finishing temperature is 800-900 ℃; rolling by adopting a high-chromium iron roller, wherein the hardness of the roller body is 75-85 HSD; carrying out low-speed constant pre-straightening in the air cooling process after rolling, wherein the straightening speed is 0.4-0.6 m/s; after rolling, firstly air-cooling to 600-650 ℃, then accelerating cooling to 350-400 ℃ at a cooling speed of 15-20 ℃/s, and then air-cooling to room temperature;
(4) tempering: the tempering temperature is 200-250 ℃, and the tempering time is 60-90 min;
(5) cold straightening: and (3) carrying out multi-pass straightening by adopting an 11-roll cold straightening machine according to a mode of straightening the turning plate again after straightening, and controlling the unevenness of the steel plate to be less than or equal to 3 mm/m.
2. The production method of the low-alloy ultrahigh-strength steel Q1100E sheet according to claim 1, wherein the production method comprises the following steps: and (4) in the step (3), pre-straightening is carried out for 1-3 times.
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