CN114277307B - High-strength steel for 1100 MPa-level engineering machinery and production method thereof - Google Patents
High-strength steel for 1100 MPa-level engineering machinery and production method thereof Download PDFInfo
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Abstract
A1100 MPa grade high-strength steel for engineering machinery and a production method thereof are disclosed, which comprises the following chemical components in percentage by weight: 0.20 to 0.24 percent of C, 0.30 to 0.50 percent of Si, 0.80 to 1.60 percent of Mn, 0.20 to 0.70 percent of Cr, 0.40 to 0.70 percent of Mo, 0 to 0.80 percent of W, 0.30 to 0.80 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, 0.0005 to 0.0030 percent of B, al:0.02 to 0.06 percent of Ca, 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 inevitable impurities; meanwhile, the following relation is required:
Description
Technical Field
The invention relates to the field of high-strength steel for engineering machinery, in particular to 1100 MPa-level high-strength steel for engineering machinery and a production method thereof.
Background
The 1100 MPa-level engineering machinery hot-rolled ultrahigh-strength steel is mainly applied to manufacturing parts such as crane booms, pump truck distribution rods and the like, and has higher requirements on the strength, plasticity, low-temperature toughness and fatigue performance of steel plates. The quenching and tempering heating time and the tempering heating time of the quenching and tempering heat treatment type ultrahigh strength steel produced by the traditional hot rolling and medium plate production line are long, for example, a 10mm steel plate is quenched and heated for 30-50 minutes, the tempering heating time is 40-60 minutes, and the production period of one steel plate needs 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 carbides grow, and the strength, plasticity and toughness of the steel plate are reduced.
The rapid heat treatment technology can greatly shorten the occupied area of the 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 researched more and more at home and abroad in recent years. The rapid heat treatment can obtain a finer grain structure with finer carbide precipitates. In terms of performance, the rapid heat treatment can achieve the strength equivalent to that of the traditional heat treatment, and has better plasticity, toughness and fatigue performance.
For example, chinese patent CN108774681A discloses "an ultra-rapid heat treatment method for high-strength steel", in which the maximum heating rate exceeds 400 ℃/s, heating is carried out until Ac 3 The temperature is kept above 50 ℃ for 5-10s, and the steel is cooled to room temperature at the extremely high cooling speed of maximally over 3000 ℃/s, so that the steel 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". The fine-grain dual-phase steel is obtained by induction heating and rapid heat treatment.
Chinese patent CN102409144A discloses a continuous alloy steel heat treatment method, which aims at the preparation of a small-section ultra-long material workpiece and can improve the production efficiency.
The existing rapid heat treatment technology mainly focuses on the research of a heat treatment method, and relatively few researches about the influence of the rapid heat treatment method on the structure performance of the ultrahigh-strength steel are carried out.
Disclosure of Invention
The invention aims to provide high-strength steel for 1100 MPa-level engineering machinery and a production method thereof, wherein the metallographic structure of the high-strength steel is tempered sorbite, the grain size of the tempered sorbite is 3-5 mu m, and the width of a tempered sorbite sheet layer is 30-90 nm; the carbides in the high-strength steel are distributed in a dispersed particle mode, the size of more than 90% of the carbides is less than 10nm, the yield strength is more than or equal to 1100MPa, the tensile strength is more than or equal to 1150MPa, the elongation is more than 16%, and the impact energy at minus 60 ℃ is more than 100J.
In order to achieve the purpose, the technical scheme provided by the invention is as follows:
the high-strength steel for 1100 MPa-grade engineering machinery comprises the following chemical components in percentage by weight: c:0.20 to 0.24%, si:0.30 to 0.50%, mn: 0.80-1.60%, cr:0.20 to 0.70%, mo:0.40 to 0.70%, W:0 to 0.80%, ni:0.30 to 0.80%, cu:0 to 0.40%, nb:0.010 to 0.030%, ti: 0.010-0.030%, V: 0.010-0.050%, B:0.0005 to 0.0030%, al: 0.02-0.06%, ca:0.001 to 0.004%, N: 0.002-0.005 percent of Fe, 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 inevitable impurities; and, the above elements simultaneously need to satisfy the following relations:
the metallographic structure of the high-strength steel is tempered sorbite, wherein the grain size of the tempered sorbite is 3-5 mu m, and the width of a tempered sorbite sheet layer is 30-90 nm; the carbides in the high-strength steel are distributed in a dispersion particle shape, and the size of more than 90 percent of the carbides is less than 10 nm.
The yield strength of the high-strength steel is more than or equal to 1100MPa, the tensile strength is more than or equal to 1150MPa, the elongation is more than 16%, and the impact energy at minus 60 ℃ is more than 100J.
In the composition design of the high-strength steel of the invention:
carbon: solid solution strengthening, adjusting the strength, plasticity and toughness of a sorbite structure, and testing, wherein the relationship between the tensile strength and the content of C of the low-carbon sorbite after reheating and quenching is as follows: rm =2510C (%) +790 (MPa), rm is tensile strength, and the strength, plasticity and toughness are further adjusted by tempering after quenching; the C content is higher, so that the whole C equivalent is improved, cracks are easy to generate during welding, and the C content is controlled to be 0.20-0.24%.
Silicon: more than 0.30 percent of Si can play a better role in deoxidation, simultaneously, the precipitation of carbide is inhibited in the tempering process, the toughness of steel is improved, and the red iron sheet is easily generated due to too high Si content, therefore, the Si content is controlled to be 0.30 to 0.50 percent.
Manganese: the Mn content of more than 0.8 percent can improve the hardenability of the steel, and the Mn content of more than 1.6 percent is easy to generate inclusions such as segregation, mnS and the like, and deteriorates the toughness of the sorbite high-strength steel, so the Mn content is controlled to be 0.80 to 1.60 percent.
Chromium: the Cr element of more than 0.2 percent can improve the hardenability of the steel, is beneficial to forming a full sorbite structure during quenching, can form Cr carbide during tempering, has the function of resisting tempering and softening, and can generate larger sparks during welding when the Cr content exceeds 0.70 percent to influence the welding quality, so the Cr content is controlled to be 0.20 to 0.70 percent.
Molybdenum: mo element can improve the hardenability of the steel and is beneficial to forming a full sorbite structure during quenching; mo reacts with C at high temperature to form carbide particles, the carbide particles have the effects of resisting high-temperature tempering softening and softening a welding joint, the carbon equivalent is improved and the welding performance is deteriorated due to too high Mo content, and meanwhile, the cost is improved due to the fact that Mo belongs to a noble metal, so that the Mo content is controlled to be 0.40-0.70%.
Tungsten: the W element can improve the hardenability of steel, forms carbide particles during tempering, has obvious tempering softening resistance and tempering brittleness resistance, and therefore, the content of W is controlled to be 0-0.80 percent.
Nickel: more than 0.10 percent of Ni element has the functions of refining sorbite structure and improving the toughness of steel, the carbon equivalent is improved and the welding performance is deteriorated due to too high Ni content, and meanwhile, the cost is improved due to Ni belonging to noble metal, so the Ni content is controlled to be 0.30 to 1.50 percent.
Copper: the Cu element can generate a certain precipitation strengthening effect during tempering, and in addition, the corrosion resistance of the high-strength steel for engineering machinery can be improved by adding a certain Cu element, so that the Cu content is controlled to be 0-0.40 percent.
Niobium, titanium and vanadium: nb, ti and V are microalloy elements, form a nano-scale precipitate with elements such as C, N and the like, and inhibit the growth of austenite grains during heating; nb can increase the critical temperature Tnr of non-recrystallization, and enlarge the production window; fine precipitate particles of Ti can improve welding performance; v reacts with N and C in the tempering process to separate out nano-scale 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 percent, the Ti content to be 0.010-0.030 percent and the V content to be 0.010-0.050 percent.
Boron: the trace amount of B can improve the hardenability and the strength of the steel, and the B exceeding 0.0030 percent is easy to generate segregation to form a carborundum compound to seriously deteriorate the toughness of the steel, and the content of B is controlled to be 0.0005 to 0.0030 percent.
Aluminum: al is used as deoxidizer, al above 0.02% is added into steel to refine crystal grains and improve impact toughness, and Al content over 0.06% is easy to generate oxide inclusion defect of Al, and the Al content is controlled to be 0.02-0.06%.
Calcium: more than 0.001 percent of trace Ca element can play a role of a purifying agent in the steel smelting process, so that the toughness of the steel is improved; when the Ca content exceeds 0.004%, a compound of Ca having a large size is easily formed and the toughness is deteriorated, and the Ca content is controlled to be 0.001 to 0.004%.
Nitrogen: the invention requires strict control of the range of N element, more than 0.002 percent of N element can react with V and C to form nano-scale V (C, N) particles in the tempering process to play a role in precipitation strengthening, and the softening of a heat affected zone can be resisted through precipitation strengthening in the welding process; an N content exceeding 0.005% tends to cause formation of coarse precipitate particles and deterioration of toughness, and the N content is controlled to 0.002 to 0.005%.
Phosphorus, sulfur and oxygen: p, S and O are taken as impurity elements to influence the plasticity and toughness of the steel, and the invention controls P to be less than or equal to 0.020%, S to be less than or equal to 0.010% and O to be less than or equal to 0.008%.
A certain amount of Mo, W and Cr elements can improve the hardenability of steel, and carbide precipitation is formed during tempering to produce precipitation strengthening. Mo, W, cr and Si can inhibit the diffusion of carbon elements during tempering, avoid forming thick cementite during rapid tempering, and the addition of more Mo, W, cr and Si can deteriorate the welding performance, so the Mo, W, cr, si and C elements need to meet the following requirements: more than or equal to (Mo +0.93W +0.52Cr +0.21Mn + 0.55)/C is less than or equal to 10.
The invention relates to a production method of high-strength steel for 1100 MPa-level engineering machinery, which comprises the following steps:
1) Smelting and casting
Smelting steel by a converter or an electric furnace, refining and casting to form a casting blank according to the chemical components;
2) Heating of
The heating temperature of the casting blank is 1150-1270 ℃, and the heat preservation is started after the core part of the casting blank reaches the heating temperature, and the heat preservation time is more than 1.5h;
3) Rolling of
Rolling the casting blank to a 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 finishing temperature is 820-920 ℃;
4) Cooling
Cooling the steel plate after final rolling to 430-520 ℃, and then coiling or air-cooling to room temperature; the cooling speed is more than or equal to 60 ℃/s;
5) Thermal treatment
Quenching, heating the cooled steel plate to Ac at a heating rate of 15-80 ℃/s 3 The temperature is 30-80 ℃, the core part of the steel plate is kept for 5-40 min after reaching the heating temperature, and then the steel plate is cooled to the room temperature at the cooling speed of more than or equal to 150 ℃/s; ac 3 Austenite transformation end temperature:
Ac 3 ＝955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；
tempering, heating the quenched steel plate to 600-650 ℃ at a heating speed of 15-80 ℃/s, keeping the temperature for 30-60 s for a short time, and then cooling to room temperature at a cooling speed of more than or equal to 40 ℃/s.
Preferably, in the step 5), the heating mode is electromagnetic induction heating, resistance heating or direct fire heating.
Preferably, in the step 5), the cooling is performed by using high-pressure water, gas mist or water mist.
In the production method of the 1100 MPa-level high-strength steel for mechanical engineering, which is disclosed by the invention, the production method comprises the following steps:
in the casting blank heating process, the alloy elements can be ensured to be fully dissolved in the solution by controlling the heating temperature to be more than 1150 ℃ and the heat preservation time to be more than 1.5h; when the heating temperature exceeds 1270 ℃, austenite grains excessively grow to cause the intercrystalline bonding force to weaken, and cracks are easy to generate during rolling; in addition, the heating temperature of the steel billet is higher than 1270 ℃, so that the surface of the steel billet is easy to be decarburized, and the mechanical property of the steel is influenced.
In the rolling process, the rolling reduction 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, after hot rolling, the steel is cooled to 430-520 ℃ at a cooling speed of more than or equal to 60 ℃/s, and then coiled or air-cooled to room temperature, so as to obtain a fine sorbite structure, ensure that carbides are distributed in a dispersed manner, and shorten the dissolution time of the carbides in the subsequent quenching and heating process.
The rapid heat treatment process is adopted, and the heat treatment period is greatly shortened through rapid heating, short-time heat preservation and rapid cooling. In the quenching stage, the steel plate is rapidly heated to Ac at the speed of 15-80 ℃/s 3 The reason why the temperature is kept for 20-40 s for a short time after the heating temperature is reached in the core part of the steel plate is 50-100 ℃, is to quickly austenize, prevent austenite grains from growing large, dissolve carbide in bainite through short-time soaking, and uniformly diffuse carbon elements. Too fast heating speed and too short holding time can result in insufficient austenitization, insufficient carbide dissolution or non-uniform carbon element; too slow heating rate and too long holding time may cause austenite grains to coarsen, deteriorating plasticity and low-temperature toughness of the steel after quenching. After the heat preservation is finished, the mixture is rapidly cooled to the room temperature at the cooling speed of more than or equal to 150 ℃/s to obtain the totalSorbite tissue.
In the tempering heat treatment process, the steel is rapidly heated to 600-650 ℃ at the speed of 15-80 ℃/s, is kept for 30-60 s for a short time, and is rapidly cooled to room temperature at the cooling speed of more than or equal to 40 ℃/s, so that fine granular carbide precipitates can be obtained. After the traditional heat treatment steel is tempered for a long time, carbides in the traditional heat treatment steel are precipitated in a large sheet shape, and the toughness and the plasticity are poor.
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: more than or equal to 6 (Mo +0.93W +0.52Cr +0.21Mn + 0.55)/C less than or equal to 10, can inhibit aggregation and growth of carbides, enables the carbides in high-strength steel to be distributed in a dispersed granular manner, enables the size of more than 90% of the carbides to be less than 10nm, further improves the plasticity and toughness on the basis of ensuring that the steel has high strength, and has the yield strength more than or equal to 1100MPa, the tensile strength more than or equal to 1150MPa, the elongation more than 16%, and the impact energy at minus 60 ℃ more than 100J.
On the basis of component design, the cooling speed and temperature are controlled in the cooling process, and a rapid heat treatment process is combined, rapid austenitization is carried out, austenite grains are prevented from growing to be large, the metallographic structure of high-strength steel is tempered sorbite, the grain size of the tempered sorbite is 3-5 mu m, and the width of a tempered sorbite layer is 30-90 nm; the carbides are distributed in a dispersed particle shape, the size of more than 90 percent of the carbides is less than 10nm, the plasticity and the toughness of the steel are obviously improved while the high strength of the steel is ensured, and the 1100MPa grade high-strength steel suitable for the engineering machinery industry is obtained.
Drawings
FIG. 1 is a metallographic structure diagram of a typical optical microscope showing the metallographic structure of a high-strength steel according to example 3 of the present invention.
FIG. 2 is a typical SEM metallographic structure of a high-strength steel in example 3 of the present invention.
Detailed Description
The present invention will be further described with reference to the following examples.
The production process flow of the high-strength steel comprises the following steps: smelting, casting → heating → rolling → cooling → heat treatment.
The specific components and process parameters are shown in tables 1 and 2, and the properties of the steel sheets of the examples are shown in table 3.
FIGS. 1 and 2 show the metallographic structure photograph of an optical microscope and the metallographic structure photograph of a scanning electron microscope, respectively, of example 3 of the high-tensile steel. As can be seen from figure 1, the metallographic structure of the finished steel plate is tempered sorbite, the structure is fine, the grain size of the tempered sorbite is 3-5 micrometers, the width of a tempered sorbite sheet layer is 30-90 nanometers, the grain size of the tempered sorbite of the same components is about 15-20 micrometers according to the conventional heat treatment process, and the width of the tempered sorbite sheet layer is hundreds of nanometers. As can be seen from FIG. 2, the carbide precipitates in the form of particles, in which 90% or more of the carbide particles have a size of 10nm or less, are formed in a long time by conventional heat treatment, and coarse lamellar carbide precipitates having a size of several tens to several hundreds of nm are formed.
The invention adopts the controlled rolling and controlled cooling and the off-line rapid heat treatment process, controls the chemical composition design, the heating speed, the heat preservation time, the cooling speed and the like in the heat treatment process, ensures that the steel plate has high strength and obviously improves the plasticity and the toughness.
Claims (4)
1. The high-strength steel for 1100 MPa-grade engineering machinery comprises the following chemical components in percentage by weight: c:0.20 to 0.24%, si:0.30 to 0.50%, mn: 0.80-1.60%, cr:0.20 to 0.70%, mo:0.40 to 0.70%, W:0 to 0.80%, ni:0.30 to 0.80%, cu:0 to 0.40%, nb:0.010 to 0.030%, ti:0.010 to 0.030%, V: 0.010-0.050%, B:0.0005 to 0.0030%, al: 0.02-0.06%, ca:0.001 to 0.004%, N: 0.002-0.005%, P is less than or equal to 0.020%, S is less than or equal to 0.0050%, O is less than or equal to 0.0040%, and the balance is Fe and other inevitable impurities; and, the above elements simultaneously need to satisfy the following relations:
the metallographic structure of the high-strength steel is tempered sorbite, wherein the grain size of the tempered sorbite is 3-5 mu m, and the width of a tempered sorbite sheet layer is 30-90 nm; the carbides in the high-strength steel are distributed in a dispersion particle shape, and the size of more than 90 percent of the carbides is less than 10 nm;
the yield strength of the high-strength steel is more than or equal to 1100MPa, the tensile strength is more than or equal to 1150MPa, the elongation is more than 16%, and the impact energy at-60 ℃ is more than 100J.
2. The production method of the high-strength steel for the 1100 MPa-level engineering machinery, according to claim 1, is characterized by comprising the following steps:
1) Smelting and casting
Smelting steel by a converter or an electric furnace, refining and casting to form a casting blank according to the chemical components in the claim 1;
2) Heating of
The heating temperature of the casting blank is 1150-1270 ℃, and the heat preservation is started after the core part of the casting blank reaches the heating temperature, and the heat preservation time is more than 1.5h;
3) Rolling of
Rolling the casting blank to a 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 finishing temperature is 820-920 ℃;
4) Cooling
Cooling the steel plate after final rolling to 430-520 ℃, and then coiling or air-cooling to room temperature; the cooling speed is more than or equal to 60 ℃/s;
5) Heat treatment of
Quenching, heating the steel plate to Ac at a heating rate of 15-80 ℃/s 3 30-80 deg.C, keeping the core of the steel plate at the heating temperature20-40 s, and then cooling to room temperature at a cooling speed of more than or equal to 150 ℃/s:
Ac 3 ＝955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；
tempering, heating the quenched steel plate to 600-650 ℃ at a heating speed of 15-80 ℃/s, keeping the temperature for 30-60 s for a short time, and then cooling to room temperature at a cooling speed of more than or equal to 40 ℃/s.
3. The method for producing the high-strength steel for the 1100 MPa-grade engineering machinery according to claim 2, wherein in the step 5), the heating mode is electromagnetic induction heating, resistance heating or direct fire heating.
4. The method for producing the high-strength steel for the 1100 MPa-level engineering machinery according to claim 2, wherein in the step 5), the cooling is performed by using high-pressure water, gas mist or water mist.
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| CN110499474A (en) * | 2019-08-23 | 2019-11-26 | 江阴兴澄特种钢铁有限公司 | High temperature resistant 400HB wear-resisting steel plate and its production method |
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| CN110499474A (en) * | 2019-08-23 | 2019-11-26 | 江阴兴澄特种钢铁有限公司 | High temperature resistant 400HB wear-resisting steel plate and its production method |
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