CN114058945B - High-strength bainite wear-resistant steel plate and production method thereof - Google Patents
High-strength bainite wear-resistant steel plate and production method thereof Download PDFInfo
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Abstract
The invention belongs to the technical field of wear-resistant steel, and provides a high-strength bainite wear-resistant steel plate and a production method thereof. The wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.20 to 0.35%, mn:1.40 to 2.30%, si:1.20 to 1.60%, cr:0.8 to 1.4%, mo:0.20 to 0.50%, ti:0.12 to 0.32%, V:0.01 to 0.04%, P: not more than 0.02%, S not more than 0.02%, al:0.02 to 0.04%, B:0.0008 to 0.0025 percent, and the balance of Fe and inevitable impurity elements. The microstructure of the wear-resistant steel plate is mainly a carbide-free bainite/martensite complex phase structure which contains multi-scale carbide; the Brinell hardness value meets the NM450 hardness requirement, the tensile strength (Rm) is more than or equal to 1300MPa, the elongation A50 is 10-25%, and the carbon equivalent is 0.55-0.70.
Description
Technical Field
The invention belongs to the technical field of wear-resistant steel, and provides a high-strength bainite wear-resistant steel plate and a production method thereof.
Background
The high-strength wear-resistant steel plate is widely applied to wear-resistant materials under various wear conditions, such as metallurgy, mines, building materials, electric power, railways, military and other fields, key parts comprise excavator bucket teeth, ball mill liners, crusher jaws, crushing walls, rolling mortar walls, tractor track shoes, fan mill impact plates and the like, and the high-strength wear-resistant steel plate is mainly used for vehicles or facilities which are in contact with materials such as ores, coal slurry, silt, cement slurry and the like for long-term work, such as mining electric wheel dumpers, coal mine scraper conveyors, cement mixers, bulldozers, excavators, loaders and the like. In the prior art, the ultrahigh-strength wear-resistant steel has high strength, so that the plasticity and toughness are common, and the wear-resistant steel has the problem of cracking or unstable performance for some parts needing to be used after forming. In addition, in the process of bearing impact load, the problems of peeling and chipping caused by poor obdurability matching exist, and further the problems of shortened service life, poor service stability and the like of the wear-resistant steel are caused.
Patent CN102691017a, "a low-cost wear-resistant steel plate with NM550 hardness and manufacturing method", the composition range of the invented steel of beijing university of science and technology is: c:0.25-0.30%, mn 2.0-2.5%, si:1.6-2.0%, cr:1.0-1.5%, mo:0.20-0.30%, ni:0.5-1.0%, nb:0.01-0.06%, V:0.01-0.06%, B:0.001-0.0015%, S is less than or equal to 0.005%, P is less than or equal to 0.015%, and [ O + N ] is less than or equal to 0.010%; the balance of Fe and inevitable impurity elements; the steel contains high Ni, nb and other noble metal elements, so that the cost is relatively high; the alloy content is high, the carbon equivalent is relatively high, the welding performance is influenced, and the toughness cannot meet the requirement.
The TiC particle reinforced ferrite/bainite based wear-resistant steel plate and the manufacturing method thereof of the Steel research institute comprise the following components: 0-2.0, si:0.30 to 0.60, mo:0 to 1.0, ti:0.4-0.8, S is less than or equal to 0.030, P is less than or equal to 0.030, C is 0.07+ Ti/4; the balance being Fe and unavoidable impurity elements. Wherein the manufacturing method of the steel comprises the following steps: converter or electric furnace smelting, external refining, slab continuous casting, hot continuous rolling, laminar cooling and coiling, the matrix structure of the wear-resistant steel is mainly ferrite/bainite, micron-sized TiC particles with volume fraction of 0.5-3% are uniformly distributed, the yield strength is 500-600MPa, the tensile strength is more than 600-700MPa, and the room-temperature impact power (Akv) of the material can reach 80J/cm 2 Above, the abrasive wear performance is comparable to NM 360. In the invention, the steel grade takes ferrite/bainite matrix structure as the main part, and the space for further improving the strength and the hardness is limited.
Patent CN107217212B, "a bainite steel for high strength and toughness wear-resistant jaw plate and a preparation method thereof", a steel invented by the science and technology development limited company of qingbei, sichuan, includes, C:0.20-0.40%; mn:1.50-2.80%; si:0.10 to 1.80 percent; cr:0.50-1.50%; p: less than or equal to 0.20 percent; s: less than or equal to 0.020%; b:0.0001-0.0020%; the balance of Fe and inevitable impurity elements; the bainite steel for the high-strength and high-toughness wear-resistant jaw plate is obtained by carrying out heat treatment on cast ingots, the structure of the bainite steel is a bainite/martensite structure, and the bainite steel is obtained by integrally selecting austenitizing, cooling to room temperature through different cooling media and tempering.
Patent CN106893942B "a high strength bainite wear resistant steel plate and method for producing the same", the steel invented by the first steel group limited company includes C:0.35-0.40%, si:1.5-1.9%, mn:0.6-1.0%, P is less than or equal to 0.015%, S is less than or equal to 0.010%, cr:0.3-0.9%, nb:0.010-0.03%, al:0.02 to 0.05%, ti:0.010-0.15%, B:0.0010-0.0030% and the balance of Fe and inevitable impurities. The method mainly comprises the steps of molten iron desulfurization, converter top and bottom combined blowing, vacuum treatment, slab casting, slab heating, rolling, water cooling or heat treatment. After heat treatment, good toughness and wear resistance are obtained.
At present, domestic wear-resisting steel uses martensite wear-resisting steel as the main, and under the prerequisite of super high strength level, martensite wear-resisting steel is applied to and has certain shaping requirement and under the shock load operating mode, and the application situation is not good: the problem of cracking or stripping and chipping exists, the stable application of the wear-resistant steel is not facilitated, and in the prior art, the wear-resistant steel plate with the Brinell hardness of more than HB400 is mainly martensitic wear-resistant steel.
Therefore, there is a high strength wear resistant steel having good toughness and a method for producing the same.
Disclosure of Invention
In view of the above problems, the present invention proposes a high strength bainitic wear resistant steel sheet and a method for producing the same to overcome or at least partially solve the above problems.
The technical scheme for realizing the purpose is as follows:
a high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.20 to 0.35%, mn:1.40 to 2.30%, si:1.20 to 1.60%, cr:0.8 to 1.4%, mo:0.20 to 0.50%, ti:0.12 to 0.32%, V:0.01 to 0.04%, P: less than or equal to 0.02 percent, S less than or equal to 0.02 percent, al:0.02 to 0.04%, B:0.0008 to 0.0025 percent, and the balance of Fe and inevitable impurity elements.
Optionally, the wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.19 to 0.24%, mn:1.70-2.10%, si:1.30-1.50%, cr:0.9-1.2%, mo:0.2-0.4%, ti:0.15-0.30%, V:0.01-0.04%, P:0-0.02%, S:0-0.02%, al:0.02-0.04%, B:0.0008 to 0.0025 percent and the balance of Fe and inevitable impurities.
Optionally, the metallographic structure of the wear-resistant steel plate is calculated by volume fraction: 70-80% of bainite, 20-30% of martensite and 5-8% of residual austenite.
A method of producing a high strength bainitic wear resistant steel plate, the method comprising:
sequentially quenching, distributing and tempering the plate blank to obtain the wear-resistant steel plate;
the quenching comprises heating the plate blank cooled to below 60 ℃, keeping the temperature at 850-950 ℃, keeping the temperature for 2-3 min/mm multiplied by the plate thickness, and then quenching at 180-240 ℃;
the temperature of the distribution is 260-320 ℃, the distribution is kept warm, the time of the distribution is 15-40 min, and then the mixture is cooled to room temperature;
the tempering temperature is 200-350 ℃, and the time is 1-3 min/mm multiplied by the plate thickness.
Optionally, the distribution is performed in a heat treatment furnace and/or a salt bath manner; the distribution heat preservation adopts an off-line heat preservation mode.
Optionally, the quenching includes at least one of water cooling, oil cooling and water-air alternation.
Optionally, the method further includes:
the quenching comprises heating, rolling and cooling of a plate blank in sequence before quenching;
the heating temperature of the plate blank is 1150-1240 ℃, and the heating time coefficient is 1-2 min/mm;
the rolling comprises rough rolling and finish rolling, wherein the single-pass reduction rate of the rough rolling is more than 15%, and the rolling is performed for 3-5 times after widening; the initial rolling temperature of the finish rolling is 870-910 ℃, and the final rolling temperature is 840-870 ℃;
the cooling sequentially comprises primary cooling, air cooling and slow cooling, wherein the initial cooling temperature is 800-840 ℃, the final cooling temperature is 300-400 ℃, and the cooling speed is not lower than 15 ℃/s; the air cooling is naturally cooling on a cooling bed after rolling; and the slow cooling comprises the step of carrying out slow cooling heat preservation after the slab is cooled to the final cooling temperature.
Optionally, straightening is performed on the plate blank after the initial cooling, and the straightening adopts a warm straightening and/or cold straightening mode.
Optionally, the initial cooling adopts a laminar cooling mode, and the initial cooling adopts any one of water cooling, fog cooling and air cooling.
Optionally, the air cooling is cold bed air cooling, and the final cooling temperature of the cold bed air cooling is 200-500 ℃.
One or more technical solutions in the embodiments of the present invention have at least the following technical effects or advantages:
according to the invention, an economical alloy component system of Mn-Si-Cr is selected, and multi-scale precipitation strengthening of microalloy elements is combined, so that high-temperature phase transformation is inhibited, and high-strength bainite wear-resistant steel with good comprehensive performance is obtained; the tensile strength (Rm) is more than or equal to 1300MPa, and the elongation A50 is 10-25%; simultaneously, a carbide-free bainite/martensite complex phase structure is obtained through refined structure regulation: the addition of Mn increases the strength of the steel by the solid solution strengthening effect of Mn, and lowers the bainite transformation start temperature. A certain amount of Si element is added to inhibit cementite precipitation, so that the residual austenite is rich in carbon and TiC and VC precipitation is promoted; si is designed to inhibit the precipitation of cementite in the bainite transformation process, so that the consumption of carbon atoms is inhibited, the carbon content in untransformed austenite is improved, and the formation of residual austenite and the formation of carbides except the cementite are promoted; the hardenability of the wear-resistant steel can be improved by adding the Cr element, the solid solution strengthening effect can be achieved, and the strength and the hardness of the steel are improved; a certain amount of Mo is mainly used to improve the hardenability of the steel. By adding appropriate Ti and V, multi-scale precipitates such as TiC, VC and (Ti, V) C can be formed while grain is refined, thereby achieving the precipitation strengthening effect. The precipitate is used as a hard phase to enhance the capability of bainite/martensite complex phase structure for resisting the invasion of furrows, thereby ensuring the service life and the service stability of the wear-resistant steel.
The foregoing description is only an overview of the technical solutions of the present invention, and the embodiments of the present invention are described below in order to make the technical means of the present invention more clearly understood and to make the above and other objects, features, and advantages of the present invention more clearly understandable.
Drawings
Various additional advantages and benefits will become apparent to those of ordinary skill in the art upon reading the following detailed description of the preferred embodiments. The drawings are only for purposes of illustrating the preferred embodiments and are not to be construed as limiting the invention. Moreover, in the drawings, like reference numerals are used to refer to like elements throughout. In the drawings:
FIG. 1 is a scanning electron microscope photograph of bainite abrasion resistant steel in comparative example 1 and examples 6 to 8 of the present invention;
FIG. 2 is a TEM photograph of bainite abrasion resistant steels in comparative example 1 and examples 6 to 8 according to the present invention;
FIG. 3 is a graph showing the ratio of precipitates in the tissue according to example 8 of the present invention;
FIG. 4 is a microphotograph of Ti (C, N) carbide precipitated in the structure of example 8 of the present invention.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly apparent therefrom. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
It should also be noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
In order to solve the technical problems, the technical scheme in the embodiment of the invention has the following general idea:
a high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.20 to 0.35%, mn:1.40 to 2.30%, si:1.20 to 1.60%, cr:0.8 to 1.4%, mo:0.20 to 0.50%, ti:0.12 to 0.32%, V:0.01 to 0.04%, P: not more than 0.02%, S not more than 0.02%, al:0.02 to 0.04%, B:0.0008 to 0.0025 percent, and the balance of Fe and inevitable impurity elements.
The chemical components of the wear-resistant steel plate are less in precious alloy. The wear-resistant steel plate is mainly designed by a Mn-Si-Cr component system, so that the content of noble alloy is low, the carbon equivalent of the steel plate is low, the hardenability of the steel plate can be ensured under the conditions of low alloy component and low carbon equivalent, and the alloy cost is low.
The method selects an economical alloy component system of Mn-Si-Cr, combines multi-scale precipitation strengthening of microalloy elements, inhibits the occurrence of high-temperature phase change, and improves the strength of steel by the solid solution strengthening effect of Mn and simultaneously reduces the initial transformation temperature of bainite by adding Mn. A certain amount of Si element is added to inhibit cementite precipitation, so that the residual austenite is rich in carbon and TiC and VC precipitation is promoted; si is designed to inhibit the precipitation of cementite in the bainite transformation process, so that the consumption of carbon atoms is inhibited, the carbon content in untransformed austenite is improved, and the formation of residual austenite and the formation of carbides except the cementite are promoted; the hardenability of the wear-resistant steel can be improved by adding the Cr element, the solid solution strengthening effect can be achieved, and the strength and the hardness of the steel are improved; a certain amount of Mo element is mainly used to improve the hardenability of steel. By adding appropriate Ti and V, multi-scale precipitates such as TiC, VC and (Ti, V) C can be formed while grain is refined, thereby achieving the precipitation strengthening effect.
As an optional embodiment, the wear-resistant steel plate comprises the following chemical components in percentage by mass:
the wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.19 to 0.24%, mn:1.70-2.10%, si:1.30-1.50%, cr:0.9-1.2%, mo:0.2-0.4%, ti:0.15-0.30%, V:0.01-0.04%, P:0-0.02%, S:0-0.02%, al:0.02-0.04%, B:0.0008 to 0.0025 percent, and the balance of Fe and inevitable impurities.
As an alternative embodiment, the metallographic structure of the wear-resistant steel plate is, in terms of volume fraction: 70-80% of bainite, 20-30% of martensite and 5-8% of residual austenite.
The carbide-free bainite/martensite complex phase structure finally ensures that the bainite wear-resistant steel plate obtains good comprehensive performance, and the residual stress of the steel plate is effectively reduced, and the precipitate is used as a hard phase to enhance the capability of the bainite/martensite complex phase structure for resisting the invasion of furrows, thereby ensuring the service life and the service stability of the wear-resistant steel.
70-80% of bainite, 20-30% of martensite guarantee excellent mechanical properties of the wear-resistant steel plate, 70-80% of bainite function to be carbide-free bainite in a bainite structure and residual austenite beneficial to toughness and plasticity of the wear-resistant steel, the adverse effect of too large volume fraction is that the strength and hardness of the wear-resistant steel cannot meet requirements, and the adverse effect of too small volume fraction is that the expected effect of optimizing the toughness and plasticity cannot be achieved.
The 20-30% martensite has the function of ensuring the strength and hardness level of the wear-resistant steel, and the adverse effect of the excessive volume fraction is that the strength and hardness of the wear-resistant steel are too high and the toughness and plasticity are poor, and the adverse effect of the too low volume fraction is that the expected strength and hardness level is not reached.
A method of producing a high strength bainitic wear resistant steel plate, the method comprising:
sequentially quenching, distributing and tempering the plate blank to obtain the bainite wear-resistant steel plate;
the quenching comprises heating the plate blank cooled to below 60 ℃, keeping the temperature at 850-950 ℃, keeping the temperature for 2-3 min/mm multiplied by the plate thickness, and then quenching at 180-240 ℃;
the temperature of the distribution is 260-320 ℃, the distribution is kept warm, the time of the distribution is 15-40 min, and then the mixture is cooled to room temperature;
the tempering temperature is 200-350 ℃, and the time is 1-3 min/mm multiplied by the plate thickness.
The invention creatively selects quenching, partitioning and tempering processes, generates a part of bainite or martensite to partition crystal grains through the quenching process, refines the effective crystal grain size, fully diffuses carbon atoms through the subsequent partitioning process, further enriches carbon in the residual austenite and stabilizes the residual austenite, and finally obtains a carbide-free bainite/martensite complex phase structure with good obdurability matching. The purpose of tempering is to reduce or eliminate internal stress in the steel, reduce quench brittleness, and ensure that carbides are precipitated in the structure to ensure the wear resistance of the steel plate. The preparation process is finely controlled, the residual stress of the steel plate is effectively reduced while the expected complex phase structure is obtained, and finally the bainite/martensite complex phase structure steel plate with high strength and high toughness can be obtained, wherein the microstructure of the steel plate is mainly a carbide-free bainite/martensite complex phase structure, and the steel plate has a finer and uniform lath structure and better toughness and plasticity; wherein multi-scale carbides are included; the multi-scale carbide is beneficial to improving the wear resistance of the steel plate, and based on the high-Ti component design, the multi-scale carbide obtained by the tempering process improves the micro-cutting resistance of a carbide-free bainite/martensite complex phase structure, thereby improving the wear resistance of the steel plate.
As an optional embodiment, the distribution is performed by using a heat treatment furnace and/or a salt bath; the distribution heat preservation adopts an off-line heat preservation mode. The off-line heat preservation is to cool the rolled steel to room temperature and then heat the steel again to the complete austenitizing temperature for heat preservation.
The carbon is distributed by a conventional heat treatment furnace and/or salt bath method, so that the carbon can be effectively distributed; meanwhile, the quenching and partitioning process is a novel heat treatment process, phase transformation is induced, carbon partitioning is completed through isothermal treatment, a carbide-free bainite/martensite complex phase structure is obtained in the phase transformation process, and membrane-shaped residual austenite is formed when the structure is cooled to room temperature. Carbide-free bainite means that carbon atoms in bainite and ferrite diffuse into nearby residual austenite during bainite transformation, and carbide precipitation is avoided, and the bainite is distinguished by the distribution of the carbon atoms. Carbide-free bainite is a special form of bainite.
As an alternative embodiment, the quenching includes at least one of water cooling, oil cooling and water-air alternation.
Any mode can be selected for quenching, as long as the quenching effect is achieved, water cooling, oil cooling and water air cooling can be performed alternately, quenching can be performed rapidly and effectively, cooling is performed at a speed higher than the critical cooling speed, and therefore the expected complex phase structure is obtained, if the expected complex phase structure is heated to a proper temperature and then cooled in air (air cooling), the purpose of quenching cannot be achieved, and the steel structure complex obtained by the method cannot be obtained.
The water-air alternation means that water-cooling and air-cooling alternate cooling equipment is adopted, and the reason for the water-air alternation is that the cooling path of the bainite wear-resistant steel can be effectively regulated and controlled, so that the obdurability matching of the wear-resistant steel is realized.
As an optional implementation, the method further comprises:
the quenching comprises heating, rolling and cooling of a plate blank in sequence before quenching;
the heating temperature of the plate blank is 1150-1240 ℃, and the heating time coefficient is 1-2 min/mm;
the rolling comprises rough rolling and finish rolling, wherein the single-pass reduction rate of the rough rolling is more than 15%, and the rolling is performed for 3-5 times after widening; the start rolling temperature of the finish rolling is 870-910 ℃, and the finish rolling temperature is 840-870 ℃;
the cooling sequentially comprises initial cooling, air cooling and slow cooling, wherein the initial cooling temperature is 800-840 ℃, the final cooling temperature is 300-400 ℃, and the cooling speed is not lower than 15 ℃/s; and the slow cooling comprises the step of carrying out slow cooling heat preservation after the plate blank is cooled to the final cooling temperature.
The rough rolling stage adopts low-speed high pressure, the single-pass reduction rate is more than 15%, the pass reduction rate is required to be gradually increased for 3-5 times after widening, and the pass reduction rate is gradually increased at the rate of increasing more than 4% in each pass; the crystal grains at the center of the steel plate can be refined, which is beneficial to the uniformity of the structure in the thickness direction of the steel plate; in the finish rolling stage, ti carbide is promoted to be precipitated through induced deformation.
In the slow cooling stage, after the wear-resistant steel plate is cooled to the final cooling temperature, arranging the wear-resistant steel plate in a slow cooling pit for slow cooling and heat preservation; the initial cooling temperature of the initial cooling stage is 800-840 ℃, mn element segregation is inhibited, and the generation of a coarse high-temperature bainite structure is prevented from being unfavorable for subsequent structure regulation; in the slow cooling stage, the problems of cracking and the like caused by stress concentration of the steel plate are prevented in order to release the stress of the steel plate and promote hydrogen discharge.
As an alternative, the slab is straightened after the initial cooling, and the straightening can be performed by warm straightening and/or cold straightening.
The shape of the steel plate is ensured, and the defects of bending and the like can be eliminated under the action of external force through various straightening processes, so that the product reaches a qualified state. The temperature straightening is generally carried out at 650-1000 ℃, and is only used for medium plates; cold straightening is widely used for straightening various types of section steel and steel pipes and also for the complementary straightening of medium and thick plates.
As an optional implementation manner, the initial cooling may adopt a laminar cooling manner, and the initial cooling may adopt any one of water cooling, fog cooling and air cooling.
The whole cooling zone of laminar cooling is divided into a plurality of cooling sections, the cooling speed and the final cooling temperature of the plate band steel are controlled by controlling the flow of water, starting the number of the cooling sections and changing the speed of a roller way, the laminar cooling is accelerated to control the cooling speed and the final cooling temperature more quickly and accurately, and any one of water cooling, fog cooling and air cooling can be selected according to the shape of a steel part and the difference of processing equipment.
In an alternative embodiment, the air cooling is cold bed air cooling, and the final cooling temperature of the cold bed air cooling is 200-500 ℃.
Namely, the primary cooling, the cold bed air cooling and the slow cooling are sequentially performed in a triple cooling mode, and the primary cooling stage, the cold bed air cooling and the slow cooling stage, namely, the three stages of water cooling (on-line water cooling), cold bed cooling and slow cooling pit cooling, are sequentially performed through the design of the triple cooling grading cooling. Water cooling (or mist cooling or air cooling instead), wherein the proper water cooling is used for shortening the time of an Mn segregation temperature zone to inhibit Mn segregation, and meanwhile, the poor tissue inheritance of the formation of a coarse high-temperature bainite tissue on a subsequent tissue is prevented; cooling in the cooling bed, and effectively dividing crystal grains by partial bainite transformation in an air cooling environment; through slow cooling in the slow cooling pit, the phase change is promoted, the stress release is facilitated, the cracking problem is prevented, and meanwhile, the hydrogen discharge is facilitated to inhibit the hydrogen embrittlement.
The method for producing a high-strength bainite wear-resistant steel plate and the bainite wear-resistant steel plate provided by the embodiments of the present invention will be described in detail below with reference to the examples and experimental data.
Example 1
A high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.20%, mn:1.40%, si:1.20%, cr:0.8%, mo:0.2%, ti:0.12%, V:0.01%, P: not more than 0.02%, S not more than 0.02%, al:0.02%, B:0.0008 percent of Fe and inevitable impurity elements as the rest. The thickness of the plate is 10mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating, rolling, primary cooling, straightening, slow cooling, quenching, distributing and tempering of a plate blank, and sequentially quenching, distributing and tempering the plate blank to obtain the bainite wear-resistant steel plate; the quenching comprises heating the plate blank cooled to below 60 ℃, keeping the temperature at 850-950 ℃, keeping the temperature for 2-3 min/mm multiplied by the plate thickness, and then quenching at 180-240 ℃; the temperature of the distribution is 260-320 ℃, the distribution and heat preservation are carried out, the time of the distribution and heat preservation is 15-40 min, and then the temperature is cooled to the room temperature; the tempering temperature is 200-350 ℃, and the time is 1-3 min/mm multiplied by the plate thickness. The distribution is carried out by a heat treatment furnace and/or a salt bath method; the distribution heat preservation adopts an off-line heat preservation mode. Optionally, the quenching includes at least one of water cooling, oil cooling and water-air alternation. The heating temperature of the plate blank is 1150-1240 ℃, and the heating time coefficient is 1-2 min/mm; the rolling comprises rough rolling and finish rolling, wherein the single-pass reduction rate of the rough rolling is more than 15%, and the pass reduction rate is gradually increased after 3-5 passes of widening; the start rolling temperature of the finish rolling is 870-910 ℃, and the finish rolling temperature is 840-870 ℃; the cooling comprises initial cooling and slow cooling, wherein the initial cooling temperature is 800-840 ℃, the final cooling temperature is 300-400 ℃, and the cooling speed is not lower than 15 ℃/s; and the slow cooling comprises the step of carrying out slow cooling heat preservation after the slab is cooled to the final cooling temperature. And straightening the plate blank after the initial cooling and the subsequent cooling, wherein the straightening adopts a warm straightening and/or cold straightening mode. The primary cooling is performed in a laminar cooling mode, and the primary cooling is performed by any one of water cooling, fog cooling and air cooling. The cooling is carried out by triple cooling, namely the primary cooling, the cold bed air cooling and the slow cooling in sequence, wherein the final cooling temperature of the cold bed air cooling is 200-500 ℃. The specific technical parameters of the process control are shown in the table 1.
The production method adopted by the embodiment sequentially comprises slab heating, rolling, primary cooling, straightening, slow cooling, quenching, partitioning and tempering, and the specific technical parameters of process control are shown in table 1.
Example 2
A high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.35%, mn:2.30%, si:1.60%, cr:1.4%, mo:0.50%, ti:0.32%, V:0.04%, P: less than or equal to 0.018%, S less than or equal to 0.01%, al:0.04%, B:0.0025 percent, and the balance of Fe and inevitable impurity elements.
The metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 70% bainite, 30% martensite. The thickness of the plate is 10mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, quenching, distribution and tempering, specific technical parameters of process control are shown in a table 1, and the rest is the same as that of the embodiment 1.
Example 3
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:2.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:0.92%, mo:0.30%, V:0.03%, al:0.029%, ti:0.2%, B:0.0023 percent, and the balance of Fe and inevitable impurity elements.
The metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 80% bainite, 20% martensite. The thickness of the plate is 8mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating, rolling, primary cooling, straightening, slow cooling, quenching, distributing and tempering of a plate blank, wherein specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Example 4
A high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.30%, mn:2.10%, si:1.40%, cr:1.2%, mo:0.45%, ti:0.28%, V:0.028%, P: less than or equal to 0.015 percent, less than or equal to 0.008 percent of S, al:0.026%, B:0.0015 percent, and the balance of Fe and inevitable impurity elements.
The metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 75% of bainite and 25% of martensite. The thickness of the plate is 8mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, quenching, distribution and tempering, specific technical parameters of process control are shown in a table 1, and the rest is the same as that of the embodiment 1.
Example 5
A high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.30%, mn:2.10%, si:1.40%, cr:1.2%, mo:0.45%, ti:0.28%, V:0.028%, P: less than or equal to 0.015 percent, less than or equal to 0.008 percent of S, al:0.026%, B:0.0015 percent, and the balance of Fe and inevitable impurity elements.
The metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 72% bainite, 28% martensite. The thickness of the plate is 8mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating, rolling, primary cooling, straightening, slow cooling, quenching, distributing and tempering of a plate blank, wherein specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Example 6
A high-strength bainite wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.30%, mn:2.10%, si:1.40%, cr:1.2%, mo:0.45%, ti:0.28%, V:0.028%, P: less than or equal to 0.015 percent, less than or equal to 0.008 percent of S, al:0.026%, B:0.0015 percent, and the balance of Fe and inevitable impurity elements.
The metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 74% bainite, 26% martensite. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, quenching, distribution and tempering, wherein specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Example 7
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:2.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:0.92%, mo:0.30%, V:0.03%, al:0.029%, ti:0.2%, B:0.0023 percent, and the balance of Fe and inevitable impurity elements. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating, rolling, primary cooling, straightening, slow cooling, quenching, distributing and tempering of a plate blank, wherein specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Example 8
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:2.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:0.92%, mo:0.30%, V:0.03%, al:0.029%, ti:0.2%, B:0.0023 percent, and the balance of Fe and inevitable impurity elements. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, quenching, distribution and tempering, specific technical parameters of process control are shown in a table 1, and the rest is the same as that of the embodiment 1.
Comparative example 1
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:2.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:0.92%, mo:0.30%, V:0.03%, al:0.029%, ti:0.2%, B:0.0023 percent, and the balance of Fe and inevitable impurity elements. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, off-line heating, air cooling and tempering at 280 ℃, specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Comparative example 2
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:1.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:1.6%, mo:0.30%, V:0.03%, al:0.029%, ti:0.1%, B:0.0005% and the balance of Fe and inevitable impurity elements. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling, off-line heating, quenching to room temperature and tempering at 280 ℃, specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
Comparative example 3
A high-strength bainite wear-resistant steel plate with the thickness of 12mm comprises the following chemical components: c:0.23%, si:1.47%, mn:1.1%, P is less than or equal to 0.012%, si:1.40%, S is less than or equal to 0.004%, cr:0.7%, mo:0.30%, V:0.03%, al:0.029%, ti:0.1%, B:0.0023 percent, and the balance of Fe and inevitable impurity elements. The thickness of the plate is 12mm.
The production method of the high-strength bainite wear-resistant steel plate sequentially comprises the steps of heating a plate blank, rolling, primary cooling, straightening, slow cooling to room temperature, tempering at 280 ℃, specific technical parameters of process control are shown in a table 1, and the rest is the same as that in example 1.
TABLE 1 Rolling and Heat treatment Process parameters of high Strength Bainite Steel plates
TABLE 2 mechanical properties of high-strength bainite wear-resistant steel plates obtained in examples and comparative examples
As can be seen from the comparison of the mechanical properties in the table 2, the plasticity and toughness of the wear-resistant steel plates subjected to quenching, partitioning and tempering in the examples 6 to 8 are remarkably improved, and more residual austenite in the structure is retained; comparative examples 1 to 3 are the tempering after direct cooling to room temperature after rolling or the air cooling or the water cooling to room temperature after off-line heating again to complete austenitization, and finally the tempering treatment is carried out. The comparative example process does not adopt a quenching-partitioning process to regulate and control the structure and the performance, and the overall mechanical performance is general.
In examples 6 to 8, after rolling, the steel is heated off-line again to complete austenitization, and is treated by different quenching, partitioning and tempering processes to obtain different tissues.
As can be seen from FIG. 1, (a) is a structure obtained by air cooling in a comparative example, the structure mainly comprises a complex phase structure of lower bainite/martensite, the residual austenite content in the whole structure is low, and the ductility and toughness are general. (b) The structure of the drawing is shown under a scanning electron microscope SEM under different quenching, distribution and tempering processes, the structure presents a carbide-free bainite/martensite complex phase structure, and simultaneously, the bainite laths or martensite laths contain membranous residual austenite, and the structure has a positive effect on improving the toughness and plasticity.
Fig. 2 shows TEM photographs of the corresponding structures in different processes, clearly comparing the relatively insignificant lath characteristics of the structures in the air-cooled process. After quenching, partitioning and tempering treatment, the characteristics of carbide-free bainite ferrite laths in the structure and membranous residual austenite in the ferrite laths are more remarkable. After isothermal treatment at 350 ℃, the quenching and distribution temperature is higher, and carbon atoms are fully diffused, so that the integral lath is longer, and the plasticity and toughness are influenced to a certain extent to reach the optimal state by the structure.
Fig. 3 and 4 show the morphology and content of Ti (C, N) carbides in the structure after quenching, partitioning and tempering in example 3. This shows that through the process technology of the invention, nano-scale carbide is precipitated in the structure, and the wear resistance of the wear-resistant steel can be effectively improved.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (9)
1. The high-strength bainite wear-resistant steel plate is characterized by comprising the following chemical components in percentage by mass: c:0.20 to 0.35%, mn:1.40 to 2.30%, si:1.20 to 1.60%, cr:0.8 to 1.4%, mo:0.20 to 0.50%, ti:0.12 to 0.32%, V:0.01 to 0.04%, P: less than or equal to 0.02 percent, S less than or equal to 0.02 percent, al:0.02 to 0.04%, B:0.0008 to 0.0025 percent, and the balance of Fe and inevitable impurity elements;
the metallographic structure of the wear-resistant steel plate is calculated by volume fraction as follows: 70-80% of bainite, 20-30% of martensite and 5-8% of residual austenite.
2. The wear-resistant steel plate according to claim 1, wherein the wear-resistant steel plate comprises the following chemical components in percentage by mass: c:0.19 to 0.24%, mn:1.70-2.10%, si:1.30-1.50%, cr:0.9-1.2%, mo:0.2-0.4%, ti:0.15-0.30%, V:0.01-0.04%, P:0-0.02%, S:0-0.02%, al:
0.02-0.04%, B:0.0008 to 0.0025 percent and the balance of Fe and inevitable impurities.
3. A method of producing a high strength bainitic wear resistant steel plate as claimed in any one of claims 1-2, comprising:
sequentially quenching, distributing and tempering the plate blank to obtain the wear-resistant steel plate;
the quenching comprises heating the plate blank cooled to below 60 ℃, keeping the temperature at 850-950 ℃, keeping the temperature for 2-3 min/mm multiplied by the plate thickness, and then quenching at 180-240 ℃;
the temperature of the distribution is 260-320 ℃, the distribution is kept warm, the time of the distribution is 15-40 min, and then the mixture is cooled to room temperature;
the tempering temperature is 200-350 ℃, and the time is 1-3 min/mm multiplied by the plate thickness.
4. The method for producing the ultra-high strength bainite wear-resistant steel plate according to claim 3, wherein the distribution is performed in a heat treatment furnace and/or a salt bath; the distribution heat preservation adopts an off-line heat preservation mode.
5. A method of producing ultra-high strength bainitic wear-resistant steel plates according to claim 3, wherein said quenching includes at least one of water cooling, oil cooling, and water air alternating.
6. The method of producing an ultra-high strength bainitic wear resistant steel plate according to claim 3, further comprising:
the quenching comprises heating, rolling and cooling of a plate blank in sequence before quenching;
the heating temperature of the plate blank is 1150-1240 ℃, and the heating time coefficient is 1-2 min/mm;
the rolling comprises rough rolling and finish rolling, wherein the single-pass reduction rate of the rough rolling is more than 15%, and the rolling is performed for 3-5 times after widening; the initial rolling temperature of the finish rolling is 870-9I 0 ℃, and the final rolling temperature is 840-870 ℃; the cooling sequentially comprises initial cooling, air cooling and slow cooling, wherein the initial cooling temperature is 800-840 ℃, the final cooling temperature is 300-400 ℃, and the cooling speed is not lower than 15 ℃/s; the air cooling is naturally cooling on a cooling bed after rolling; and the slow cooling comprises the step of carrying out slow cooling heat preservation after the slab is cooled to the final cooling temperature.
7. The method for producing an ultra-high strength bainite wear resistant steel plate according to claim 6 wherein the slab is straightened after the initial cooling, and wherein the straightening is performed by warm straightening and/or cold straightening.
8. The method for producing an ultra-high strength bainite wear resistant steel plate according to claim 6 wherein the initial cooling is by laminar flow cooling, and the initial cooling is by any one of water cooling, mist cooling and air cooling.
9. The method for producing an ultra-high strength bainite wear resistant steel plate according to claim 6 wherein the air cooling is cold bed air cooling, and the final cooling temperature of the cold bed air cooling is 200 ℃ to 500 ℃.
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