CN110144517B - High-strength high-toughness high-aluminum nickel-free easily-welded 40-70 mm-thick wear-resistant steel plate and preparation method thereof - Google Patents
High-strength high-toughness high-aluminum nickel-free easily-welded 40-70 mm-thick wear-resistant steel plate and preparation method thereof Download PDFInfo
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Abstract
The invention provides a high-strength and high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate and a preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by weight: c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.30-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.45-0.60%, V: 0.025-0.040%, B: 0.001-0.0025%, Alt is more than or equal to 0.06%, and the balance is Fe and trace impurities; the preparation method comprises the following steps: slowly cooling the continuous casting billet, heating the continuous casting billet, forming and rolling, slowly cooling the steel plate, quenching and tempering to obtain the finished steel. In the components and the method of the steel plate, a high-aluminum nickel-free component system is adopted, and the content and the proportion relation of four alloy elements of C, Mn, Mo and Cr in the steel are designed to realize the easy welding performance.
Description
Technical Field
The invention relates to the technical field of steel plate preparation, in particular to a high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate and a preparation method thereof.
Background
Wear-resistant steel is a wear-resistant material widely used in various wear conditions. In recent years, along with the continuous progress of smelting, continuous casting, rolling and heat treatment process technologies, the quality of wear-resistant steel products is greatly improved. However, with the continuous expansion of the application field, the service environment of the wear-resistant steel is increasingly harsh, and thus, the requirements on the wear resistance, the hardness uniformity, the high strength and toughness, the low temperature toughness and the like of the wear-resistant steel are continuously improved.
Currently, there have been issued high toughness low alloy wear resistant steels with thicknesses above 40mm, such as: "a wear resistant steel plate having low temperature impact toughness" patent said steel using C: 0.13-0.20%, Si: 0.25 to 0.60%, Mn: 0.4-0.8%, Ni: 0.15-0.35%, Mo: 0.1-0.3%, Cr: 0.25-0.60%, Ti: 0.010-0.035%, P is less than or equal to 0.015%, S is less than or equal to 0.003%, B: 0.0013-0.0030%, Al: 0.010-0.050%, less than or equal to 0.0002% of H and less than or equal to 0.0035% of N, the thickness of the prepared steel plate is 30-60mm, and the Brinell hardness HBW360-HBW460 is more than 50J at minus 40 ℃. The steel contains noble alloy Ni element, the large thickness of the steel plate is 60mm, and the impact energy at minus 40 ℃ is more than 50J; the steel plate of the patent of 'an ultra-thick specification wear-resistant steel plate' adopts C: 0.12-0.20%, Si: 0.40-0.60%, Mn: 0.6-1.10%, Ni: 0.10-0.40%, Mo: 0.2-0.5%, Cr: 0.60-0.90%, Ti: 0.015-0.040%, P: 0.01-0.015%, S: 0.001-0.003%, B: 0.0010-0.0025%, Al: 0.010-0.040%, H is less than or equal to 0.0002%, N is less than or equal to 0.0040%, Mg: 0.007-0.015 percent of the steel plate, the thickness of the prepared steel plate is 60-80mm, the Brinell hardness HBW350-HBW450 is more than or equal to 40J at-20 ℃, and the tensile strength is more than or equal to 1150 MPa; the "a wear-resistant steel plate with thick gauge and narrow hardness range" patent describes that the steel plate adopts a C: 0.16-0.23%, Si: 0.25-0.55%, Mn: 0.60-1.00%, P is less than or equal to 0.013%, S is less than or equal to 0.003%, Ti: 0.010-0.030%, Ni: 0.25-0.50%, Nb: 0-0.030%, Cr: 0.40-0.70%, Mo: 0.20-0.50%, B: 0.0010-0.0035%, Al: 0.010-0.050%; CN106521314A, the steel contains C: 0.11-0.15%, Si: 0.20-0.40%, Mn: 0.90-1.30%, P is less than or equal to 0.010%, S is less than or equal to 0.002%, V: 0.03 to 0.06%, Ti: 0.010-0.030%, Ni: 1.0-2.60%, Nb: 0-0.040%, Cr: 0.40-0.70%, Mo: 0.40-0.70%, Cu: 0.2-0.5%, B: 0.0010-0.0020%, Al: 0.060-0.10%; the impact energy of the steel is more than 60J at the temperature of minus 40 ℃; the steel plate of the patent of '80 mm large-thickness high-toughness low-alloy wear-resistant steel plate' adopts C: 0.18-0.20%, Si: 0.20-0.40%, Mn: 0.90-1.20%, P is less than or equal to 0.012%, S is less than or equal to 0.002%, Cr: 0.90-1.20%, Mo: 0.20-0.40%, Ni: 0.50-0.80%, Ti: 0.008-0.030%, Nb: 0.01-0.050%, V is less than or equal to 0.030%, B: 0.0008-0.0025%, Alt: 0.02-0.06%, N is less than or equal to 0.0040%, H is less than or equal to 0.0002%, the maximum thickness of the prepared steel plate is 60mm, the yield strength is more than or equal to 1000MPa, the tensile strength is more than or equal to 1050MPa, the elongation is more than or equal to 10%, and the Akv impact power value at minus 40 ℃ is more than or equal to 20J; in summary, in the steel making process, in order to improve the toughness and wear resistance of the finished steel, the steel making is generally carried out by adding precious alloy elements such as Ni, Ti and the like, however, by adopting the above operation, not only the production cost of the steel is increased, but also the welding performance and toughness of the finished steel are affected, for example, TiN particles with sharp corners are easily formed by adding the Ti element, a potential crack source is formed, and the toughness is not improved, so that how to consider the performance of the finished steel and reduce the production cost becomes important.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides a high-strength and high-toughness high-aluminum nickel-free easily-welded 40-70 mm-thick wear-resistant steel plate and a preparation method thereof. The Brinell hardness of the steel plate is 330-370HBW, and the hardness value of the steel plate in the thickness direction is not lower than 90% of the surface hardness; the tensile strength is more than or equal to 850MPa, the elongation after fracture (A5) is more than or equal to 14 percent, and the impact energy at the thickness of 1/4 steel plate at minus 40 ℃ is more than or equal to 70J; the preparation method of the steel plate has the advantages of simple process, small limitation condition on the finished steel plate, obvious finished product advantages, no need of on-line cooling after rolling and the like; the steel plate obtained by the preparation method provided by the invention has large thickness specification, high impact toughness at the low temperature of-40 ℃ and stable mechanical property, and is very suitable for manufacturing large-scale mechanical equipment wear-resistant parts.
The technical scheme of the invention is as follows:
a high-strength high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate comprises the following chemical components in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.30-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.45-0.60%, V: 0.025-0.040%, B: 0.001-0.0025%, Alt is more than or equal to 0.06%, and the balance is Fe and trace impurities.
Furthermore, in the high-strength high-toughness high-aluminum nickel-free easily-welded wear-resistant steel plate with the thickness of 40-70mm, the weight percentages of the four alloy elements of C, Mn, Mo and Cr meet that C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.41%, so that the welding performance of the wear-resistant steel plate is improved.
Furthermore, in the high-strength high-toughness high-aluminum nickel-free wear-resistant steel plate with the thickness of 40-70mm, the percentage content of Alt is 0.060-0.080%, and the toughness of the wear-resistant steel plate is improved by controlling the content of Alt.
Preferably, the high-strength high-toughness high-aluminum nickel-free wear-resistant steel plate with the thickness of 40-70mm is easy to weld and comprises the following chemical components in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.30-1.40%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.45-0.50%, V: 0.025-0.030%, B: 0.001-0.0025%, Alt: 0.060-0.080%, and the balance of Fe and trace impurities; wherein, the weight percentage of the four alloy elements of C, Mn, Mo and Cr satisfies that C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.39 percent.
Preferably, the high-strength high-toughness high-aluminum nickel-free wear-resistant steel plate with the thickness of 40-70mm is easy to weld and comprises the following chemical components in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.40-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.50-0.60%, V: 0.030 to 0.040%, B: 0.001-0.0025%, Alt: 0.060-0.080%, and the balance of Fe and trace impurities; wherein, the weight percentage of the four alloy elements of C, Mn, Mo and Cr satisfies that C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.41 percent.
The preparation method of the high-strength high-toughness high-aluminum nickel-free easily-welded wear-resistant steel plate with the thickness of 40-70mm comprises the following steps:
(1) slow cooling of the continuous casting billet: after the continuous casting billet is taken off line, entering a pit for slow cooling, wherein the slow cooling temperature range is 460-650 ℃, and the slow cooling time is not less than 72 h;
(2) heating a continuous casting blank: the heating temperature of the continuous casting billet is controlled at 1200-1220 ℃;
(3) forming and rolling: the initial rolling temperature of the austenite non-recrystallization region of the steel billet is 910-930 ℃, and the ratio of the initial rolling thickness of the austenite non-recrystallization region to the thickness of the finished steel plate is 2.0-3.0;
(4) slowly cooling the steel plate: stacking and slow cooling steel plates, specifically, quickly stacking and slow cooling the steel plates after the steel plates are formed and rolled, wherein the slow cooling time is not less than 24 hours, and the temperature of the steel plates after slow cooling is not less than 460 ℃;
(5) heating the quenching heat treatment steel plate to 910-920 ℃ for complete austenitizing, and quenching by a quenching machine after the quenching heat preservation time is 20-30 min; then carrying out 550-580 ℃ tempering heat treatment, wherein the tempering heat preservation time is 20-40 min; and obtaining finished steel.
Preferably, in the step (3) of the steel plate preparation method, the initial rolling temperature of the austenite non-recrystallization zone of the steel billet is 920-930 ℃, and the ratio of the initial rolling thickness to the thickness of the finished steel plate is 2.5-3.0; the tempering temperature of the steel plate after quenching in the step (5) is 550-565 ℃, and the heat preservation time is 20-30 min.
Preferably, in the step (3) of the steel plate preparation method, the initial rolling temperature of the austenite non-recrystallization zone of the steel billet is 910-; the tempering temperature of the steel plate after quenching in the step (5) is 565-580 ℃, and the heat preservation time is 30-40 min.
The design principle of the chemical components of the steel plate is as follows:
c: c is the most main alloying element in steel, and an increase in carbon content can significantly improve strength, hardness and hardenability of the steel sheet, but as the carbon content increases, toughness of the steel sheet is adversely affected, and thus, in order to improve hardenability of the steel sheet and ensure good strength and hardness of the steel sheet without decreasing the toughness of the steel sheet, the C content is controlled in the range of 0.16 to 0.18% in the present invention.
Si: si is dissolved in ferrite and austenite in steel, which can remarkably improve the strength and hardness of the steel, however, if Si is too high, temper brittleness is easily generated, and the toughness of the steel is reduced, so that the Si content in the steel is controlled within the range of 0.20-0.30%.
Mn: mn can increase the toughness, strength and hardness of steel, improve the hardenability of the steel and improve the hot workability of the steel, the Mn content of the invention is controlled within the range of 1.30-1.50%, and the Mn content in the steel is properly increased after the steel plate degree is increased.
P and S: is a harmful element in steel and can influence the brittleness of the steel; the sulfur can form plastic inclusion manganese sulfide with manganese in the steel, and has great influence on the transverse plasticity and toughness of the steel plate; meanwhile, phosphorus also seriously affects the plasticity and toughness of the steel plate, in other words, for the invention, the lower the content of phosphorus and sulfur is, the better the content is, but in the actual production process, phosphorus and sulfur are both inevitable, therefore, the content of P is controlled below 0.015 percent, and the content of S is controlled below 0.002 percent.
Nb: nb can effectively refine the microstructure by inhibiting austenite recrystallization in the controlled rolling process and strengthen the matrix by precipitation. In the welding process, Nb segregation and precipitation can prevent austenite grains from coarsening during heating, refine the structure of a heat affected zone and improve the performance of a welded joint, and the Nb content is controlled within the range of 0.01-0.02% in order to improve the toughness and the welding performance of a steel plate.
V: because the steel adopts the low-carbon component design, the reduction of the C content has larger influence on the strength loss of the steel, and the addition of niobium and titanium microalloy elements mainly plays the roles of fine grain strengthening and precipitation strengthening, delays austenite recrystallization and prevents austenite grains from growing. When Nb and V are both welding reheat crack sensitive elements, too high addition is not suitable, therefore, V in the steel of the invention is controlled within the range of 0.025-0.040%.
Mo: mo can improve the tempering stability and hardenability of the steel and prevent the tempering brittleness. In the invention, the tempering temperature adopted after the steel plate is quenched is higher, and in order to reduce the softening of the steel plate caused by high-temperature tempering and reduce the tempering brittleness, the content of Mo is controlled within the range of 0.45-0.60 percent.
Cr: the addition of Cr can increase the hardenability of steel and ensure a martensite structure in the inside of a thick gauge steel sheet to ensure a sufficiently high hardness of the steel sheet, but when the content of Cr in steel is excessively high, the weldability of the steel sheet is greatly reduced, and for this reason, the present invention controls the Cr content in steel within the range of 0.25-0.35%.
And (3) Alt: alt is one of the strongest deoxidizers, can effectively remove oxygen in steel and improve the purity of molten steel, and is also an important grain refining element, thereby having a positive effect on improving the impact toughness of a steel plate. In view of the large gauge and high toughness requirements of the steel sheet to which the present invention relates, the Alt content is controlled to be in the range of 0.060-0.080%.
Compared with the prior art, the invention has the beneficial effects that:
(1) the 40-70mm high-toughness wear-resistant steel disclosed by the invention is not added with a noble alloy nickel element, so that the preparation cost is greatly reduced.
(2) In the design process, the high-toughness wear-resistant steel with easy welding performance is designed and prepared by matching the components of C, Mn, Mo and Cr in the designed steel, and the preparation cost is greatly reduced.
(3) In order to improve the toughness of the steel, the high-aluminum composition design is adopted, and Ti element is not added, so that the formation probability of TiN particles with sharp corners is avoided, and the toughness of the steel plate is improved.
(4) The thickness of the steel plate obtained by the preparation method reaches 40-70mm, the impact toughness reaches more than 70J at the low temperature of-40 ℃, the hardness values of the steel plate in the thickness direction are uniform, and the core hardness is not lower than 90% of the surface hardness.
Detailed Description
In order to make those skilled in the art better understand the technical solutions in the present invention, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
A high-strength high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate comprises the following chemical components in percentage by weight:
c: 0.16%, Si: 0.21%, Mn: 1.32%, P: 0.011%, S: 0.001%, Nb: 0.01%, Cr: 0.26%, Mo: 0.47%, V: 0.027%, B: 0.0015%, Alt: 0.065 percent, and the balance of Fe and trace impurities, wherein C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.352 percent.
The thickness of the high-strength high-toughness high-aluminum nickel-free easy-welding wear-resistant steel plate is 40mm, the width of the steel plate is 2500mm, and the specific preparation method comprises the following steps:
(1) smelting: performing KR pretreatment, smelting by a 120-ton top-bottom combined blown converter, refining by a 120-ton LF ladle furnace, refining by a 120-ton RH vacuum degassing refining, a slab caster and other technological processes on molten iron to obtain a continuous casting billet with the section size of 250mm multiplied by 1800 mm; the thickness of the continuous casting billet is 250 mm;
(2) the effective metallurgical compression ratio is 4.50;
(3) slow cooling of the continuous casting billet: after the continuous casting billet is taken off line, entering a pit for slow cooling, and after 72 hours, stacking for slow cooling at 468 ℃;
(4) heating a continuous casting blank: controlling the heating temperature of the continuous casting billet to be 1210 ℃;
(5) forming and rolling: the initial rolling temperature of an austenite non-recrystallization region of the steel billet is 930 ℃, the initial rolling thickness of the austenite non-recrystallization region is 112mm, and the ratio of the initial rolling temperature of the austenite non-recrystallization region to the thickness of a finished steel plate is 2.8;
(6) slowly cooling the steel plate: stacking the rolled steel plates for slow cooling, wherein the temperature of the stacked slow-cooled steel plates is not lower than 460 ℃ after 24 hours;
(7) quenching heat treatment: heating the steel plate to 910 ℃, and quenching and preserving heat for 23 min; after heat preservation, putting the steel plate into a quenching machine to quench and cool the steel plate to room temperature;
(8) tempering heat treatment: then carrying out tempering heat treatment at 550 ℃, wherein the tempering heat preservation time is 20 min;
the tensile strength of the wear-resistant steel plate with the thickness of 40mm obtained by the process is 933MPa, the elongation after fracture (A5) is 16.5 percent, the average value of the surface Brinell hardness is 335HBW, the average value of the Brinell hardness in the thickness direction of the steel plate is 311HBW, and the low-temperature impact energy at minus 40 ℃ is 74J.
Example 2
A high-strength high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate comprises the following chemical components in percentage by weight:
the chemical components and the weight percentage content are as follows: c: 0.17%, Si: 0.26%, Mn: 1.38%, P: 0.010%, S: 0.002%, Nb: 0.015%, Cr: 0.31%, Mo: 0.48%, V: 0.028%, B: 0.0018%, Alt: 0.069 percent, and the balance of Fe and trace impurities, wherein C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.372 percent.
The preparation method of the wear-resistant steel plate provided by the embodiment has the following differences from the embodiment 1:
(1) the thickness of the finished steel plate is 50mm, the width is 2600mm, and the effective metallurgical compression ratio is 3.46;
(2) slow cooling of the continuous casting billet: the thickness of the continuous casting billet is 280 mm; after the continuous casting billet is taken off line, entering a pit for slow cooling, and after 72 hours, stacking for slow cooling at 521 ℃;
(4) heating a continuous casting blank: controlling the heating temperature of the continuous casting slab to 1215 ℃;
(5) forming and rolling: the initial rolling temperature of the austenite non-recrystallization zone of the steel billet is 922 ℃. The initial rolling thickness of the austenite non-recrystallization region is 125mm, and the ratio of the initial rolling temperature of the austenite non-recrystallization region to the thickness of a finished steel plate is 2.5;
(6) slowly cooling the steel plate: stacking the rolled steel plates for slow cooling, wherein the temperature of the stacked slow-cooled steel plates is not lower than 460 ℃ after 36 hours;
(7) quenching heat treatment: heating the steel plate to 915 ℃, and quenching and preserving heat for 23 min; after heat preservation, putting the steel plate into a quenching machine to quench and cool the steel plate to room temperature;
(8) tempering heat treatment: then carrying out the tempering heat treatment at 563 ℃, wherein the tempering heat preservation time is 30 min;
the 50 mm-thick wear-resistant steel plate obtained by the process has the tensile strength of 978MPa, the elongation after fracture (A5) of 15.0 percent, the average value of the surface Brinell hardness of 356HBW, the average value of the Brinell hardness in the thickness direction of the steel plate of 324HBW, and the low-temperature impact energy at minus 40 ℃ at the thickness position of 1/4 steel plate of 79J.
Example 3
A high-strength high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate comprises the following chemical components in percentage by weight:
c: 0.17%, Si: 0.25%, Mn: 1.45%, P: 0.012%, S: 0.001%, Nb: 0.018%, Cr: 0.33%, Mo: 0.55%, V: 0.035%, B: 0.0022%, Alt: 0.071% of the balance of Fe and trace impurities, wherein C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.387%.
The preparation method of the wear-resistant steel plate provided by the embodiment has the following differences from the embodiment 1:
(1) the thickness of the finished steel plate is 60mm, the width of the finished steel plate is 2400mm, and the effective metallurgical compression ratio is 3.13;
(2) slow cooling of the continuous casting billet: the thickness of the continuous casting billet is 300 mm; after the continuous casting billet is off-line, entering a pit for slow cooling, and after 72 hours, stacking for slow cooling at the temperature of 603 ℃;
(4) heating a continuous casting blank: controlling the heating temperature of the continuous casting billet at 1220 ℃;
(5) forming and rolling: the initial rolling temperature of an austenite non-recrystallization region of the steel billet is 916 ℃, the initial rolling thickness of the austenite non-recrystallization region is 145mm, and the ratio of the initial rolling temperature of the austenite non-recrystallization region to the thickness of a finished steel plate is 2.42;
(6) slowly cooling the steel plate: stacking the rolled steel plates for slow cooling, wherein the temperature of the stacked slow-cooled steel plates is not lower than 460 ℃ after 48 hours;
(7) quenching heat treatment: heating the steel plate to 918 ℃, and quenching and preserving heat for 28 min; after heat preservation, putting the steel plate into a quenching machine to quench and cool the steel plate to room temperature;
(8) tempering heat treatment: then carrying out tempering heat treatment at 570 ℃, wherein the tempering heat preservation time is 37 min.
The tensile strength of the wear-resistant steel plate with the thickness of 60mm obtained by the process is 965MPa, the elongation after fracture (A5) is 16.0%, the average value of the surface Brinell hardness is 360HBW, the average value of the Brinell hardness in the thickness direction of the steel plate is 330HBW, and the low-temperature impact energy at-40 ℃ in the thickness position of 1/4 steel plate is 88J.
Example 4
A high-strength high-toughness high-aluminum nickel-free easy-welding 40-70 mm-thick wear-resistant steel plate comprises the following chemical components in percentage by weight:
c: 0.18%, Si: 0.29%, Mn: 1.48%, P: 0.009%, S: 0.001%, Nb: 0.018%, Cr: 0.34%, Mo: 0.57%, V: 0.038%, B: 0.0021%, Alt: 0.077 percent, and the balance of Fe and trace impurities, wherein C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.402 percent.
The preparation method of the wear-resistant steel plate provided by the embodiment has the following differences from the embodiment 1:
(1) the thickness of the finished steel plate is 70mm, the width of the finished steel plate is 2100mm, and the effective metallurgical compression ratio is 3.06;
(2) slow cooling of the continuous casting billet: after the continuous casting billet is taken off line, entering a pit for slow cooling, and after 72 hours, stacking for slow cooling at the temperature of 646 ℃;
(4) heating a continuous casting blank: controlling the heating temperature of the continuous casting billet to be 1218 ℃;
(5) forming and rolling: the initial rolling temperature of an austenite non-recrystallization region of the steel billet is 911 ℃, the initial rolling thickness of the austenite non-recrystallization region is 141mm, and the ratio of the initial rolling temperature of the austenite non-recrystallization region to the thickness of a finished steel plate is 2.01;
(6) slowly cooling the steel plate: stacking the rolled steel plates for slow cooling, wherein the temperature of the stacked slow-cooled steel plates is not lower than 460 ℃ after 72 hours;
(7) quenching heat treatment: heating the steel plate to 918 ℃, quenching and preserving heat for 25min, and putting the steel plate into a quenching machine after preserving heat to quench and cool the steel plate to room temperature;
(8) tempering heat treatment: then, the tempering heat treatment at 577 ℃ is carried out, and the tempering heat preservation time is 36 min.
The tensile strength of the wear-resistant steel plate with the thickness of 70mm obtained by the process is 991MPa, the elongation after fracture (A5) is 16.0 percent, the average value of the surface Brinell hardness is 347HBW, the average value of the Brinell hardness in the thickness direction of the steel plate is 321HBW, and the low-temperature impact energy at minus 40 ℃ at the thickness part of the 1/4 steel plate is 90J.
Modifications and alterations of this invention by those skilled in the art are intended to be covered by the scope of this invention without departing from the spirit and scope of this invention.
Claims (7)
1. A high-strength high-toughness high-aluminum nickel-free wear-resistant steel plate with a thickness of 40-70mm and easy welding is characterized by comprising the following chemical components in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.30-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.45-0.60%, V: 0.025-0.040%, B: 0.001-0.0025%, Alt is more than or equal to 0.06%, and the balance is Fe and trace impurities;
the preparation method of the wear-resistant steel plate comprises the following steps:
(1) slow cooling of the continuous casting billet: after the continuous casting billet is taken off line, entering a pit for slow cooling, wherein the slow cooling temperature range is 460-650 ℃, and the slow cooling time is not less than 72 h;
(2) heating a continuous casting blank: the heating temperature of the continuous casting billet is controlled at 1200-1220 ℃;
(3) forming and rolling: the initial rolling temperature of the austenite non-recrystallization region of the steel billet is 910-930 ℃, and the ratio of the initial rolling thickness of the austenite non-recrystallization region to the thickness of the finished steel plate is 2.0-3.0;
(4) slowly cooling the steel plate: stacking and slow cooling steel plates, specifically, quickly stacking and slow cooling the steel plates after the steel plates are formed and rolled, wherein the slow cooling time is not less than 24 hours, and the temperature of the steel plates after slow cooling is not less than 460 ℃;
(5) heating the quenching heat treatment steel plate to 910-920 ℃ for complete austenitizing, and quenching by a quenching machine after the quenching heat preservation time is 20-30 min; then carrying out 550-580 ℃ tempering heat treatment, wherein the tempering heat preservation time is 20-40 min; and obtaining finished steel.
2. The wear-resistant steel plate as claimed in claim 1, wherein the four alloying elements C, Mn, Mo, Cr are in a weight percentage of C +0.1Mn +0.1Mo +0.05Cr ≦ 0.41%.
3. The wear resistant steel sheet of claim 2, wherein the percentage of Alt is 0.060 to 0.080%.
4. The wear-resistant steel plate as claimed in any one of claims 1 to 3, wherein the steel plate has the following chemical composition in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.30-1.40%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.45-0.50%, V: 0.025-0.030%, B: 0.001-0.0025%, Alt: 0.060-0.080%, and the balance of Fe and trace impurities; wherein, the weight percentage of the four alloy elements of C, Mn, Mo and Cr satisfies that C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.39 percent.
5. The wear-resistant steel plate as claimed in any one of claims 1 to 3, wherein the steel plate has the following chemical composition in percentage by weight:
c: 0.16-0.18%, Si: 0.20-0.30%, Mn: 1.40-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.002%, Nb: 0.01-0.020%, Cr: 0.25-0.35%, Mo: 0.50-0.60%, V: 0.030 to 0.040%, B: 0.001-0.0025%, Alt: 0.060-0.080%, and the balance of Fe and trace impurities; wherein, the weight percentage of the four alloy elements of C, Mn, Mo and Cr satisfies that C +0.1Mn +0.1Mo +0.05Cr is less than or equal to 0.41 percent.
6. The wear-resistant steel sheet as claimed in claim 1, wherein in the step (3) of the steel sheet preparation method, the initial rolling temperature of the austenite non-recrystallization zone of the steel sheet is 920-; the tempering temperature of the steel plate after quenching in the step (5) is 550-565 ℃, and the heat preservation time is 20-30 min.
7. The wear-resistant steel sheet as claimed in claim 1, wherein in the step (3) of the steel sheet preparation method, the initial rolling temperature of the austenite non-recrystallization zone of the steel sheet is 910-; the tempering temperature of the steel plate after quenching in the step (5) is 565-580 ℃, and the heat preservation time is 30-40 min.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS49115042A (en) * | 1973-03-09 | 1974-11-02 | ||
| CN101451220A (en) * | 2007-12-03 | 2009-06-10 | 舞阳钢铁有限责任公司 | High-strength abrasion-proof steel plate and method for producing the same |
| CN101451219A (en) * | 2007-12-03 | 2009-06-10 | 舞阳钢铁有限责任公司 | High intensity wear-resistant steel plate and preparation method thereof |
| CN103589964A (en) * | 2013-11-27 | 2014-02-19 | 内蒙古包钢钢联股份有限公司 | Steel plate used for 750MPa-grade hot rolling concrete agitator tank |
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2019
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS49115042A (en) * | 1973-03-09 | 1974-11-02 | ||
| CN101451220A (en) * | 2007-12-03 | 2009-06-10 | 舞阳钢铁有限责任公司 | High-strength abrasion-proof steel plate and method for producing the same |
| CN101451219A (en) * | 2007-12-03 | 2009-06-10 | 舞阳钢铁有限责任公司 | High intensity wear-resistant steel plate and preparation method thereof |
| CN103589964A (en) * | 2013-11-27 | 2014-02-19 | 内蒙古包钢钢联股份有限公司 | Steel plate used for 750MPa-grade hot rolling concrete agitator tank |
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