CN115725892B - Brinell hardness 550 HB-grade wear-resistant steel and production method thereof - Google Patents
Brinell hardness 550 HB-grade wear-resistant steel and production method thereof Download PDFInfo
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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Abstract
The brinell hardness 550HB grade wear-resistant steel and the production method thereof comprise the following chemical components in percentage by weight: 0.28 to 0.32 percent of C, 1.30 to 1.80 percent of Si, 0.80 to 1.60 percent of Mn, 1.50 to 2.50 percent of Cr, 0.20 to 0.50 percent of Mo, 0 to 0.80 percent of W, 2.5 to 3.5 percent of Ni, 0 to 0.40 percent of Cu, 0.010 to 0.030 percent of Nb, 0.010 to 0.030 percent of Ti, 0.010 to 0.050 percent of V, less than or equal to 0.0004 percent of B, 0.02 to 0.06 percent of Al, 0.001 to 0.004 percent of Ca, 0.002 to 0.005 percent of N, less than or equal to 0.020 percent of P, less than or equal to 0.0050 percent of S, less than or equal to 0.0040 percent of O, and the balance of Fe and other unavoidable impurities. The elements need to satisfy the following relations: 15 to less than or equal to (1.97 Si) 2 +0.65Mo+0.52W+0.26Cr)/C is less than or equal to 25. The invention controls the composition design, the rapid heat treatment heating speed, the heat preservation time, the cooling speed and the like, and produces the wear-resistant steel with the Brinell hardness more than or equal to 550HB and the elongation percentage>15 percent, impact energy at minus 60 ℃ is more than 70J.
Description
Technical Field
The invention relates to the field of wear-resistant steel for engineering machinery, in particular to brinell hardness 550 HB-grade wear-resistant steel and a production method thereof.
Background
The rapid heat treatment technology can greatly shorten the occupied area of a unit, improve the production efficiency, reduce the energy consumption and reduce the environmental pollution, and is a green production technology. The rapid heat treatment technology comprises rapid heating, short-time heat preservation, rapid cooling and rapid tempering in the quenching process, and the rapid heat treatment technology and the steel structure performance thereof are increasingly researched at home and abroad in recent years. The rapid thermal treatment can result in finer grain structure with finer carbide precipitation. In terms of performance, the rapid heat treatment can reach the strength equivalent to that of the traditional heat treatment, and has better plasticity, toughness and fatigue performance.
The hot-rolled wear-resistant steel is mainly used for manufacturing wear-resistant parts of dumper carriages and mining machinery, and has high requirements on strength, plasticity, low-temperature toughness and fatigue performance of steel plates. The time for quenching and tempering the wear-resistant steel produced by the traditional hot rolling and medium plate production line is long, for example, the quenching and tempering time for 10mm steel plates is 30-50min, the tempering time for 40-60min, and the production period of one steel plate is more than one hour. This results in higher energy costs and lower production efficiency. The long-time heating in the aspect of performance also easily causes coarse grains, precipitated carbide grows up, and strength, plasticity and toughness of the steel plate are reduced.
The prior rapid heat treatment for producing wear-resistant steel is disclosed in Chinese patent CN108774681A, which discloses an ultra-rapid heat treatment method for high-strength steel, wherein the maximum heating speed exceeds 400 ℃/s and the steel is heated to Ac 3 The temperature is kept above 50 ℃ for 5-10s, and the steel is cooled to room temperature at an extremely high cooling speed of maximally more than 3000 ℃/s, and is used for heat treatment strengthening of thin-specification strip steel and small-specification wire rods.
Chinese patent CN1039621a discloses "a heat treatment method for preparing fine grain dual phase steel". And obtaining the fine-grain dual-phase steel through induction heating and rapid heat treatment.
Chinese patent CN102409144a discloses a "method for heat treatment of continuous alloy steel", which aims at preparing a workpiece with a small cross section and ultra-long material, so as to improve production efficiency.
The existing rapid heat treatment technology is mainly focused on the research of a heat treatment method, and the research on the influence of the rapid heat treatment method on the structural performance of the wear-resistant steel is relatively little.
Disclosure of Invention
The invention aims to provide the wear-resistant steel with the Brinell hardness of 550HB and the production method thereof, wherein the wear-resistant steel with the Brinell hardness of 550HB has the advantages that the ultra-high hardness is ensured, the plasticity and the toughness of the steel are obviously improved, the Brinell hardness of the wear-resistant steel is more than or equal to 550HB, the elongation is more than 15%, and the impact energy at the temperature of minus 60 ℃ is more than 70J.
In order to achieve the above purpose, the technical scheme provided by the invention is as follows:
the brinell hardness 550HB grade wear-resistant steel comprises the following chemical components in percentage by weight: c:0.28 to 0.32 percent, si:1.30 to 1.80 percent, mn:0.80 to 1.60 percent, cr:1.50 to 2.50 percent, mo:0.20 to 0.50 percent, W:0 to 0.80 percent, ni:2.5 to 3.5 percent, cu:0 to 0.40 percent, nb:0.010 to 0.030 percent, ti:0.010 to 0.030 percent, V:0.010 to 0.050 percent, B is less than or equal to 0.0004 percent, al:0.02 to 0.06 percent, ca:0.001 to 0.004 percent, N: 0.002-0.005%, P less than or equal to 0.020%, S less than or equal to 0.0050%, O less than or equal to 0.0040%, and the balance Fe and other unavoidable impurities; the elements simultaneously satisfy the following relations:
15≤(1.97Si 2 +0.65Mo+0.52W+0.26Cr)/C≤25。
the metallographic structure of the wear-resistant steel is fine self-tempering martensite+3-4% film-shaped austenite, wherein the original austenite size is 3-7 mu m, and the width of a martensite lath is 30-90 nm; the carbide in the wear-resistant steel is in dispersion particle distribution, and the average size of the precipitate is below 12 nm.
The Brinell hardness of the wear-resistant steel is more than or equal to 550HB, the elongation is more than 15%, and the impact energy at minus 60 ℃ is more than 70J.
In the composition design of the present invention:
carbon: solid solution strengthening, and adjusting the strength, plasticity and toughness of a martensitic structure, wherein the relationship between the tensile strength and the C content of the low-carbon martensite after reheating quenching is as follows: r is R m ＝2510C(％)+790(MPa)，R m For tensile strength, the strength is further adjusted by self-tempering after quenchingDegree, plasticity and toughness; the higher C content can lead to the improvement of the whole C equivalent, and cracks are easy to generate during welding, and the C content is controlled to be 0.28-0.32 percent.
Silicon: in the invention, higher Si is added, and mainly in consideration of the fact that Si has a strong effect of inhibiting diffusion of carbon element in the cooling process, the precipitation and growth speed of carbide can be inhibited in the tempering process by adding higher Si, the toughness of steel is improved, and the welding performance of the steel is influenced by too high Si, so that the content of Si is controlled to be 1.30-1.80%.
Manganese: mn element more than 0.8% can improve the hardenability of steel, mn content more than 1.6% is easy to produce segregation and MnS inclusion, and the toughness of martensitic steel is deteriorated, therefore, the Mn content is controlled to be 0.80-1.60%.
Chromium: cr is a carbide influencing element, cr forms Cr carbide in the slow cooling process, and has precipitation strengthening effect when the precipitated carbide is finer. Certain Cr element is beneficial to improving the hardenability of steel, and a martensitic structure is obtained during quenching. When the Cr content is high, larger spark can appear during welding to influence the welding quality, so the invention controls the Cr content to be 1.50-2.50%.
Tungsten: the W element can improve the hardenability of steel, and forms carbide particles in tempering, has obvious tempering softening resistance and tempering brittleness resistance, so that the W content is controlled to be 0-0.80%.
Nickel: the Ni element has the functions of refining the martensite structure and improving the toughness of the steel, and the higher the carbon content in the martensite, the higher Ni is required to be added to ensure the toughness. The too high Ni content results in an increase in carbon equivalent, deteriorating welding performance, and the Ni belongs to noble metal, which increases cost, so the present invention controls the Ni content to 2.5-3.5%.
Copper: the Cu element can generate certain precipitation strengthening effect during tempering, and the corrosion resistance of the high-strength steel for engineering machinery can be improved by adding certain Cu element, so that the Cu content is controlled to be 0-0.40%.
Niobium, titanium and vanadium: nb, ti and V are microalloy elements, form nano-scale precipitates with C, N and other elements, and inhibit the growth of austenite grains when heated; nb can raise the non-recrystallization critical temperature Tnr and enlarge the production window; fine precipitate particles of Ti can improve the welding performance; v reacts with N and C in the tempering process to separate out nanoscale V (C, N) particles, so that the strength of the steel can be improved; the invention controls the Nb content to be 0.010-0.030%, the Ti content to be 0.010-0.030% and the V content to be 0.010-0.050%.
Boron: b has strong grain boundary segregation effect, forms carbon boron compound, worsens toughness of martensitic steel after quenching, and as impurity element, the content of B is controlled below 0.0004%.
Aluminum: al is used as deoxidizer, and the steel is added with more than 0.02 percent of Al to refine grains, so that the impact toughness is improved, the oxide inclusion defect of Al is easy to generate when the Al content exceeds 0.06 percent, and the content of Al is controlled to be 0.02 to 0.06 percent.
Calcium: the trace Ca element exceeding 0.001 percent can play a role of a purifying agent in the steel smelting process, and improve the toughness of the steel; the Ca content exceeding 0.004% tends to form a compound of Ca having a large size, but rather deteriorates toughness, and the Ca content is controlled to be 0.001 to 0.004% in the present invention.
Nitrogen: the invention requires strict control of the range of N element, more than 0.002% of N element can react with V and C to form nanoscale V (C, N) particles in the tempering process to play a role in precipitation strengthening, and softening of a heat affected zone can be resisted by precipitation strengthening in the welding process; the N content exceeding 0.005% tends to cause coarse precipitate particles to be formed, deteriorating toughness, and the present invention controls the N content to 0.002 to 0.005%.
Phosphorus, sulfur and oxygen: p, S and O are used as impurity elements to influence the plasticity and toughness of steel, and the invention controls P to be less than or equal to 0.020%, S to be less than or equal to 0.0050% and O to be less than or equal to 0.0040%.
Si, mo, W and Cr are self-tempering control elements, wherein Si has a strong function of inhibiting carbide diffusion in the quenching and cooling process, mo, W and Cr are carbide affinity elements, and carbon elements can be fixed or carbide can be formed in the temperature range of 200-400 ℃. Researches show that the proper proportion of carbide influencing elements such as Si, mo, W, cr and the like is fullFoot: 15 to less than or equal to (1.97 Si) 2 +0.65Mo+0.52W+0.26Cr)/C is less than or equal to 30, the martensite start transition temperature Ms temperature of the steel grade is 400-450 ℃, and the martensite transition end temperature M f When the steel plate is cooled to 250-300 ℃ and kept for 5-15 seconds in a short time at 100-200 ℃, most of martensite is converted, self-tempering occurs in the period of heat preservation, nano-sized carbide particles are separated out in the self-tempering process, and the average size of the carbide particles can be controlled below 12 nm. The nano-sized carbide precipitates, which can produce a precipitation strengthening effect and avoid deterioration of toughness due to coarse carbide. Meanwhile, carbon elements in the formed martensite can diffuse into supercooled austenite, so that the carbon elements in the rest supercooled austenite are increased, the austenite is stabilized, and finally, a small amount of film-shaped austenite of 3-4% can be remained between martensite laths, and the film-shaped austenite can effectively improve the plasticity and toughness of the steel plate.
The invention relates to a production method of a Brinell hardness 550 HB-grade wear-resistant steel, which comprises the following steps:
1) Smelting and casting
Adopting a converter or an electric furnace to make steel and refine according to the chemical components, and casting to form a casting blank;
2) Heating
The heating temperature of the casting blank is 1150-1270 ℃, and the heat preservation is started after the core of the casting blank reaches the heating temperature, and the heat preservation time is more than 1.5h;
3) Rolling
Rolling the casting blank to the target thickness by adopting single-frame reciprocating rolling or multi-frame hot continuous rolling, wherein the rolling reduction rate of the last rolling pass is more than 15%; the final rolling temperature is 820-920 ℃;
4) Cooling
Cooling the steel plate after finish rolling to 430-520 ℃ at a cooling speed of more than or equal to 60 ℃/s, coiling, and slowly cooling to room temperature;
5) Heat treatment of
The steel plate is quickly heated to A at the speed of 100-200 ℃/s c3 Heating at 110-150 deg.c, fast cooling to 250-300 deg.c at speed greater than or equal to 150 deg.c/s, short-term heat preservation for 5-15 s, fast cooling to room at 10-50 deg.c/sTemperature.
Preferably, in step 5), the heating mode is electromagnetic induction heating, resistance heating or direct fire heating.
Preferably, in step 5), the cooling is performed by using high-pressure water, aerosol or water mist.
In the production method of the Brinell hardness 550HB grade wear-resistant steel, the invention comprises the following steps:
in the casting blank heating process, the heating temperature is controlled to be higher than 1150 ℃ and the heat preservation time is controlled to be more than 1.5h, so that the alloy elements can be ensured to be fully dissolved in solid; when the heating temperature exceeds 1270 ℃, austenite grains grow excessively, so that the inter-crystal binding force is weakened, and cracks are easy to generate during rolling; in addition, the heating temperature exceeds 1270 ℃ is easy to cause decarburization of the surface of the steel billet, and the mechanical property of the finished product is influenced.
In the rolling process, the reduction rate of the last pass of rolling is more than 15%, the final rolling temperature is 820-920 ℃, and austenite grains can be refined.
In the cooling process, the hot rolled steel is cooled to 430-520 ℃ at a cooling speed of more than or equal to 60 ℃/s and coiled at a low temperature, so that fine sorbite tissues are obtained, carbide is dispersed and distributed, and the dissolving time of the carbide in the subsequent quenching and heating process is shortened.
Adopting a rapid heat treatment process to rapidly heat the steel plate to A at a speed of 100-300 ℃/s c3 The temperature is not kept at 110-150 ℃, then the austenite grains are refined and austenitized rapidly under the condition that the temperature is not kept at 150 ℃/s, the rapid heat treatment time is shortened, and the efficiency is improved. Heating to A c3 High temperature of plus (110-150) deg.C replaces traditional A c3 The low temperature of plus (30-50) DEG C can lead carbide in bainite to be quickly dissolved, further refine the martensitic structure after quenching, reduce the grain size of 550 HB-grade wear-resistant steel to 3-7 mu m, reduce the width of martensite lath to 30-90nm, and lead the grain size of the wear-resistant steel with the same grade produced under the traditional heat treatment condition to be more than 15 mu m, and lead the width of martensite lath to be more than 150 nm. Too high a heating rate or too low a heating temperature may result in insufficient austenitization, insufficient carbide dissolution or non-uniform carbon element, too low a heating rate or too high a heating temperatureWhich leads to coarsening of austenite grains and deteriorates plasticity and low-temperature toughness of the quenched steel. Therefore, the rapid heat treatment is realized by replacing time with temperature, the production efficiency is greatly improved, and meanwhile, the toughness and the plasticity of the steel are improved by refining the structure.
The content of Si, mo, W, cr and other elements in the wear-resistant steel is controlled, and the relation is satisfied: 15 to less than or equal to (1.97 Si) 2 +0.65Mo+0.52W+0.26Cr)/C is less than or equal to 30, and the steel plate is heated to A c3 Immediately after the temperature of plus (110-150) ℃, the steel is quickly cooled to 250-300 ℃ at a cooling speed of more than or equal to 150 ℃/s, and is kept for 5-15 s for a short time, the martensite start transition temperature Ms of the steel is 400-450 ℃, the martensite transition end temperature Mf is 100-200 ℃, and the martensite structure can be formed and self-tempered by controlling the temperature of 250-300 ℃ for 5-15 s and the cooling speed of 10-50 ℃/s, carbide precipitation with the average size of less than 12nm and 3-4% of film austenite are controlled to be formed in the self-tempering process, so that the plasticity and toughness of the steel plate are effectively improved.
The invention has the beneficial effects that:
the invention strictly controls the contents of Mo, W, cr, si, C and other elements in the aspect of component design, and satisfies the relation: 15 to less than or equal to (1.97 Si) 2 The +0.65Mo+0.52W+0.26Cr)/C is less than or equal to 25, martensite in the wear-resistant steel can be self-tempered, formed carbides such as Mo, W, cr and the like are distributed in a dispersed particle shape, most of precipitates are below 12nm in size, the nano-sized carbides can produce precipitation strengthening effect, and deterioration of toughness due to coarse carbides can be avoided. In the self-tempering process, carbon elements in martensite are diffused into supercooled austenite, so that the carbon elements in the rest supercooled austenite are increased, and finally, a small amount of film-shaped austenite of 3-4% can remain between martensite laths, thereby effectively improving the plasticity and toughness of the steel plate. The Brinell hardness of the wear-resistant steel is more than or equal to 550HB, and the elongation percentage is higher than or equal to>15 percent of impact energy at minus 60 DEG C>70J。
On the basis of component design, the invention adopts a rapid heat treatment process, and the temperature of the heated steel plate reaches A c3 High temperature of plus (110-150) deg.C replaces traditional A c3 Low temperature of plus (30-50) deg.C, without heat preservationAnd the method can quickly austenitize, refine austenite grains, shorten the production period of the steel plate and improve the production efficiency. And then the cooling speed after heat treatment is controlled to form a martensitic structure, so that the austenite grain size of the ultra-high strength structural steel can be reduced to 3-7 mu m, the width of a martensite lath is reduced to 30-90nm, the austenite grain size of the ultra-high strength steel obtained under the traditional heat treatment condition is more than 15 mu m, the width of the martensite lath is more than 150nm, the self tempering of the martensitic structure is realized in the cooling process, carbide precipitation is refined, and the plasticity and toughness of the steel plate are obviously improved while the ultra-high hardness of the steel plate is ensured.
Drawings
FIG. 1 is a drawing showing a metallographic structure of a typical optical microscope of example 3 of the abrasion-resistant steel according to the present invention.
FIG. 2 is a metallographic view of a typical scanning electron microscope of example 3 of the wear-resistant steel according to the invention.
Detailed Description
The invention is further illustrated below with reference to examples.
The production process flow of the wear-resistant steel comprises the following steps: smelting, casting, heating, rolling, cooling and quick heat treatment.
Specific components and process parameters of the examples of the invention are shown in tables 1 and 2, and the properties of the steel plates of the examples are shown in Table 3.
Fig. 1 and 2 show photographs of optical microscope metallographic structures and scanning electron microscope metallographic structures of the steel of example 3, respectively.
As can be seen from FIG. 1, the metallographic structure of the finished steel plate is self-tempered martensite and 3-4% film-like austenite, the structure is fine, the grain size of tempered sorbite is 3-7 mu m, the width of tempered martensite lath is 30-90nm, the original austenite size of the same components is about 15-20 mu m according to the conventional heat treatment process, and the width is hundred nanometers.
From fig. 2 it can be seen that the particulate carbide precipitates, most of which are below 12nm in size, are produced by conventional heat treatment for a long period of time, resulting in coarse lamellar carbide precipitates, which are tens to hundreds of nanometers in size.
The invention adopts the processes of rolling control, cooling control and rapid heat treatment, controls the chemical composition design, the heating speed, the heat preservation time, the cooling speed and the like in the rapid heat treatment process, ensures the ultra-high hardness of the steel plate and obviously improves the plasticity and the toughness of the steel plate.
Claims (5)
1. The brinell hardness 550HB grade wear-resistant steel comprises the following chemical components in percentage by weight: c:0.28 to 0.32 percent, si:1.30 to 1.80 percent, mn:0.80 to 1.60 percent, cr:1.50 to 2.50 percent, mo:0.20 to 0.50 percent, W:0 to 0.80 percent, ni:2.5 to 3.5 percent, cu:0 to 0.40 percent, nb:0.010 to 0.030 percent, ti:0.010 to 0.030 percent, V:0.010 to 0.050 percent, B is less than or equal to 0.0004 percent, al:0.02 to 0.06 percent, ca:0.001 to 0.004 percent, N: 0.002-0.005%, P less than or equal to 0.020%, S less than or equal to 0.0050%, O less than or equal to 0.0040%, and the balance Fe and other unavoidable impurities; the elements need to satisfy the following relations:
15≤(1.97Si 2 +0.65Mo+0.52W+0.26Cr)/C≤25
the metallographic structure of the wear-resistant steel is fine self-tempering martensite+3-4% film-shaped austenite, wherein the original austenite size is 3-7 mu m, and the width of a martensite lath is 30-90 nm; the carbide in the wear-resistant steel is in dispersion particle distribution, and the average size of the precipitate is below 12 nm.
2. The brinell hardness 550HB grade wear resistant steel of claim 1, wherein the wear resistant steel has a brinell hardness of greater than or equal to 550HB, an elongation of >15%, and an impact energy of > 70J at-60 ℃.
3. The method for producing a brinell hardness 550HB grade wear resistant steel as claimed in claim 1 or 2, comprising the steps of:
1) Smelting and casting
Adopting a converter or an electric furnace to make steel and refine according to the chemical components, and casting to form a casting blank;
2) Heating
The heating temperature of the casting blank is 1150-1270 ℃, and the heat preservation is started after the core of the casting blank reaches the heating temperature, and the heat preservation time is more than 1.5h;
3) Rolling
Rolling the casting blank to the target thickness by adopting single-frame reciprocating rolling or multi-frame hot continuous rolling, wherein the rolling reduction rate of the last rolling pass is more than 15%; the final rolling temperature is 820-920 ℃;
4) Cooling
Cooling the steel plate after finish rolling to 430-520 ℃ at a cooling speed of more than or equal to 60 ℃/s, coiling, and slowly cooling to room temperature;
5) Heat treatment of
The steel plate is quickly heated to A at the speed of 100-200 ℃/s c3 And (2) quickly cooling to 250-300 ℃ at a cooling speed of more than or equal to 150 ℃/s at the temperature of plus (110-150) DEG C, preserving heat for 5-15 s for a short time, and quickly cooling to room temperature at a speed of 10-50 ℃/s.
4. A process for producing a 550HB scale abrasion resistant steel having Brinell hardness as claimed in claim 3,
in the step 5), the heating mode is electromagnetic induction heating, resistance heating or direct fire heating.
5. A process for producing a 550HB scale abrasion resistant steel having Brinell hardness as claimed in claim 3,
in the step 5), the cooling is performed by adopting high-pressure water, aerosol or water mist.
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