CN110527907B - 550-grade wear-resistant composite board and production method thereof - Google Patents

550-grade wear-resistant composite board and production method thereof Download PDF

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CN110527907B
CN110527907B CN201910821785.1A CN201910821785A CN110527907B CN 110527907 B CN110527907 B CN 110527907B CN 201910821785 A CN201910821785 A CN 201910821785A CN 110527907 B CN110527907 B CN 110527907B
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composite
wear
blank
base material
welding
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CN110527907A (en
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蒋健博
张涛
刘芳芳
韩严法
胡奉雅
王佳骥
傅博
付魁军
及玉梅
林田子
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Angang Steel Co Ltd
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • B21B2001/386—Plates

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Abstract

The invention discloses a 550-grade wear-resistant composite board and a production method thereof. The composite board consists of a base material and a composite material, wherein the base material is low-carbon low-alloy steel; the composite material is 550-grade wear-resistant steel. Vacuumizing the composite blank, and then carrying out vacuum electron beam sealing welding, wherein the welding process is double-gun linkage, and each welding seam is divided into N sections when being welded, wherein N is more than or equal to 5, and the length of each section is 200-400 mm; when the composite blank is heated, a central heating mode is adopted, so that the composite blank is heated directly from the center and is heated to the periphery in a conduction mode; 1-2 hours before the composite blank is discharged from the furnace, and the temperature of flame holes on the upper surfaces of the head and the tail of the composite blank is increased by 40-50 ℃; the thickness of the finished composite board is 20-100 mm. The composite surface shear strength of the composite plate is not less than 502MPa, the bonding rate is 100%, the Brinell hardness of the composite layer is not less than 535, and the impact energy at room temperature is not less than 118J, and the composite plate is applied to easily-worn equipment.

Description

550-grade wear-resistant composite board and production method thereof
Technical Field
The invention belongs to the technical field of metal material processing, and particularly relates to a 550-grade wear-resistant composite plate produced by applying a vacuum compounding and rolling technology and a preparation method of the composite plate.
Background
The composite wear-resistant steel plate is a wear-resistant composite material produced by adopting an advanced composite manufacturing technology, and is an advanced wear-resistant composite material in the industrial field. Because the base plate of the wear-resistant composite steel plate is made of ordinary carbon low alloy steel with good plasticity and toughness, the base plate can absorb energy in the process of being impacted, and therefore, the wear-resistant composite steel plate has stronger impact resistance and crack resistance compared with simple substance wear-resistant steel, and can be applied under the working conditions of stronger vibration and impact. Meanwhile, the wear-resistant composite steel plate can be made into a steel plate with a standard size, and is light in weight and convenient and flexible to process. Because the soft substrate is adopted, the material can be formed by inward cold bending, and can be cut by a heat source such as plasma arc, carbon arc and the like. In addition, although the price of the composite steel plate is higher than that of the common steel plate due to the material and process reasons, the service life of the composite steel plate is greatly prolonged, and the equipment shutdown overhaul time and the maintenance cost applied to the abrasion environment are greatly reduced. According to estimation, the cost performance of the composite steel plate is about 2-4 times higher than that of a common wear-resistant steel plate, the larger the material handling capacity is, the more serious the equipment wear of an enterprise is, and the more obvious the economic benefit of using the composite steel plate is. Therefore, the composite wear-resistant steel plate is widely applied to various easily-worn devices in the industries of metallurgical machinery, building material machinery, electric machinery, mining machinery and the like.
At present, the domestic wear-resistant composite board mainly adopts a surfacing method, such as wear-resistant electrode surfacing, flux-cored wire surfacing and plasma surfacing. Meanwhile, related research and development work has also been conducted with respect to the powder method, the brazing method, the diffusion method, and the like. However, the processes have respective limitations, and the surfacing welding of the wear-resistant welding rods adopts high-Cr and high-C cast iron welding rods, is limited by the length of the cast iron welding rods, and is difficult to realize automatic welding; the performance of a surfacing layer of the flux-cored wire is influenced by the filling rate of the flux core and the dilution of a peripheral iron sheet, the content of a strengthening phase is difficult to improve, and the performance of an abrasion-resistant plate is further influenced; the wear-resistant plate prepared by plasma surfacing has the characteristics of high hardness and wear resistance, but the surfacing efficiency of the process is low, and the process is difficult to popularize on a large scale. Under the background, a great deal of research and development work on the preparation technology of the wear-resistant composite board is carried out by broad scholars.
CN101774288A discloses a 'metal part wear-resistant composite board and a repair process thereof', and a 'research on a manufacturing process method of a wear-resistant composite board' (a permitted resource, Chengge nationality, Liujianwei and the like, published in No. 8 of welding 2010, pages 37 to 40) and a 'wear-resistant composite board prepared by strip surfacing' (a land peak, a king element, a king Ling armor published in No. fourteenth national wear-resistant material meeting 2015 to 394) adopt a mode of surfacing a wear-resistant weld seam on a base steel plate to prepare the wear-resistant composite board, wherein the wear resistance of the wear-resistant composite board is 12 to 18 times higher than that of low-carbon steel, 5 times higher than that of stainless steel and high-manganese steel and 1 time higher than that of cast high-chromium iron. But the production efficiency is lower, the production cost is higher, and the method is not suitable for industrial mass production.
CN102212821A discloses "a method for preparing reinforced tungsten carbide wear-resistant composite plate", CN102212822A discloses "a method for processing metal wear-resistant composite plate and a processing device thereof", and CN102218615A discloses "a method for preparing thickened wear-resistant layer composite plate", all of the above three patents adopt a method for preparing wear-resistant composite plate by spreading relevant powder on a base steel plate and forming wear-resistant composite plate after heat treatment in a heating furnace, and the wear-resistant alloy of the working layer is not only smooth and beautiful in surface, but also can be directly used in the working conditions (such as baffle plate, etc.) requiring smooth surface. However, the wear-resistant composite plate prepared by the process has poor compactness of the wear-resistant layer, low wear resistance and short service life, and cannot meet the increasing actual requirements of engineering application.
CN107557537A discloses a method for preparing a high-toughness high-wear-resistance composite plate, and CN103264259A discloses a method for preparing a wear-resistance refractory brick mould plate and a rapid preparation method thereof, wherein the two patents adopt a mode of heating or adding transition metal to form metallurgical connection between a wear-resistance plate and a base steel plate for preparing the wear-resistance composite plate, and the wear-resistance and corrosion-resistance composite plate is high in wear resistance and corrosion resistance, high in production efficiency, long in service life, low in cost, energy-saving and environment-friendly. However, the process depends on the preparation of the wear-resistant composite plate in a non-pressure diffusion or brazing filler metal connection mode, the shearing resistance of a composite interface is low, the defects of layering, peeling and the like are easy to occur, the application under a high-load use environment cannot be met, and the service life is not reliably guaranteed.
In summary, the conventional surfacing welding method is still the main preparation process of the wear-resistant composite plate, and although related research and development work is also gradually carried out on other production processes, the wear-resistant composite plate still has more problems and has greater limitations. Meanwhile, the wear-resistant composite plates commonly used in domestic markets are in the grade of 360-450, the development work of the wear-resistant composite plates above the grade of 450 is less, a large amount of research data support is lacked, and the application of the wear-resistant composite plates is greatly limited. Against this background, in the face of the increasing demand for wear-resistant composite boards in the field of engineering applications, especially for wear-resistant composite boards with high hardness levels, an efficient and stable preparation process for producing high-level wear-resistant composite boards is urgently needed.
The rolling method is a novel high-efficiency composite board preparation process, and generally comprises vacuum assembly, heating and rolling processes. However, in the preparation process of the high-grade wear-resistant composite plate, due to the difference of the physical and chemical properties of the wear-resistant steel and the base steel, the problems of joint failure and plate shape control often occur. Firstly, because the carbon content of the wear-resistant steel is high, welding cracks are easy to occur during assembly sealing welding, and particularly, during large-size composite blank sealing welding, the welding deformation and the welding stress are concentrated obviously, and joint cracking and failure are easy to occur. Secondly, in the heating process of the composite blank, because the heating deformation of the composite blank is inconsistent, the stress directly acts on the position of the welding joint, and the problem of cracking and failure of the sealing joint is easy to occur. In the process of preparing the high-wear-resistance composite plate by adopting a conventional rolling method, the situation that a sealing joint of a composite blank is cracked and fails after sealing or in the heating process often occurs. In addition, in the process of rolling the composite blank, the problems of inconsistent deformation and warping of the wear-resistant steel and the base steel often occur, and even the rolling cannot be continued due to overlarge warping. Based on the problems, the success rate of preparing the high-grade wear-resistant steel composite plate by the conventional rolling method composite process is only about 50%.
The invention provides a method for efficiently and stably preparing 550-grade wear-resistant composite boards, which regulates and controls the stress distribution state and the temperature field distribution state of composite blanks in the assembly welding process by optimizing the assembly welding and heating processes, obtains obvious control effect and greatly improves the success rate of preparing 550-grade wear-resistant composite boards.
Disclosure of Invention
Based on the defects of the prior art, the invention aims to provide a high-efficiency and stable preparation method of a high-grade wear-resistant composite board, which reduces the crack sensitivity of a sealing joint, improves the success rate of the high-grade wear-resistant composite board, adopts special assembly sealing and heating processes to ensure that the shearing strength of a composite surface is more than or equal to 500MPa and the hardness of a wear-resistant layer reaches 550 grade, ensures the success rate of the wear-resistant composite board and has the wear-resistant characteristic of 550 grade. The success rate of the 550-grade wear-resistant composite board produced by the method can reach more than 80%, the board shape is smooth, the composite interface performance is stable, and the 550-grade wear-resistant composite board has excellent wear resistance.
A550-grade wear-resistant composite board is formed by compounding low-carbon low-alloy steel and 550-grade wear-resistant steel, wherein the low-carbon low-alloy steel is low-carbon low-alloy steel with the C content of less than or equal to 0.22% by mass percent; 550 grade wear-resistant steel comprises the following chemical components in percentage by mass: 0.25% -0.30%, Si: 0.3% -0.5%, Mn: 0.40% -1.00%, Cr: 0.6-1.2%, Mo: 0.15% -0.4%, Nb: 0.01-0.03%, Ni is less than or equal to 0.50%, Cu is less than or equal to 0.50%, B: 0.0005% -0.0022%, Ti: 0.025% -0.04%, Als: 0.020-0.045%, less than or equal to 0.015% of P, less than or equal to 0.005% of S, less than or equal to 0.0080% of N, less than or equal to 0.0020% of O, more than or equal to 3.4% of Ti/N, and the balance of Fe and inevitable impurities.
The carbon content in the base material is required to be below 0.22 percent, so that on one hand, the lower carbon content can ensure the quality of the sealing and welding joint of the wear-resistant composite blank and reduce the crack tendency of the welding joint; on the other hand, the lower carbon content can ensure that the base layer has better impact resistance in the single-side online ultra-fast cooling treatment process.
The action mechanism of elements in 550-grade wear-resistant steel is as follows:
c: the steel plate has ultrahigh surface hardness, and the hardenability of a thick steel plate during water cooling needs to be ensured by equivalent carbon content, the hardness of the steel is correspondingly increased along with the increase of the carbon content in a certain range, and simultaneously, a certain carbon content can be precipitated with Nb, Ti, Cr, Mo and the like to form carbide, so that the wear resistance is improved. If the carbon content is too high, the plasticity and toughness are reduced, and the welding performance is reduced, and in order to ensure the high hardness, the welding performance and the low-temperature toughness of the steel plate, the C content is controlled to be 0.25-0.30 percent.
Si: the main functions are solid solution strengthening and deoxidation, and are non-carbide forming elements, and when the content of Si is more, the precipitation of carbide can be inhibited, but when the content of Si is more, the welding performance can be reduced, and the toughness can be influenced, so that the content of Si is controlled to be 0.3% -0.5%.
Mn: the steel plate has the main effects of solid solution strengthening, the hardenability can be improved when the content is more than 0.4%, the carbon supersaturation degree in martensite is improved, the strength and the hardness are favorably improved, the cost is low, but the center segregation is easy to form when the content is more than 1.0, and the plate blank has the tendency of easy cracking; therefore, the Mn content in the invention is controlled to be 0.4-1.0%.
Nb: the steel is a strong carbon and nitrogen compound forming element, and mainly has the main functions of inhibiting the growth of crystal grains during heating by forming fine carbonitride in the steel and has a certain precipitation strengthening function during air cooling; nb is added to the steel to increase the recrystallization temperature of the steel sheet by inhibiting the austenite grain boundary motion. A proper amount of Nb is added into the steel plate, and when the steel plate is austenitized at high temperature, the undissolved NbC plays a role in nailing and rolling austenite grain boundaries, thereby preventing the austenite grain boundaries from being coarsened excessively. Nb dissolved in austenite suppresses austenite recrystallization and refines austenite grains in the two-stage rolling process. However, if the Nb content is too high, coarse NbC is formed, which affects the mechanical properties of the steel sheet. Therefore, the addition amount of Nb in the invention is 0.01-0.03%.
Ti: can form compounds with nitrogen, carbon and sulfur, and has the main functions of inhibiting the growth of crystal grains during heating by forming fine carbonitride in steel, enabling the titanium and the nitrogen compounds to have higher forming temperature, enabling the precipitation temperature of vanadium carbide and niobium carbide to be lower than that of titanium carbide and titanium nitride, enabling niobium to be mainly combined with carbon by controlling the proportion of titanium and nitrogen (Ti/N is more than or equal to 3.4) during titanium addition, preventing free N in the steel from forming compounds with B, improving the yield of acid-soluble boron, fully exerting the effect of improving the hardenability of B, but forming coarse TiN when the content is too high, and reducing the low-temperature toughness and fatigue performance of a steel plate, so that the addition amount of Ti is controlled to be 0.025-0.04 percent and the Ti/N is more than or equal to 3.4.
Mo, Cr: the method has the main effects of reducing the critical cooling speed, improving the hardenability of the steel plate, forming a completely fine martensite structure, forming various carbides of chromium and molybdenum in steel, improving the strength and hardness of the steel plate, ensuring that the hardness of the thick steel plate is more than 550HB, the content of Mo is more than 0.15 percent, the effect is obvious when the content of Cr is more than 0.6 percent, the content of Mo and Cr is properly increased along with the increase of the thickness, but the price of Mo is high, and the weldability is reduced when Mo and Cr are excessively added, so that the method controls the Cr: 0.6-1.2%, Mo: 0.15 to 0.4 percent.
B: the quenching hardenability can be greatly improved by adding a trace amount of boron into the steel, and the boron is very small in addition amount and has strong affinity with oxygen and nitrogen in the molten steel, so that the boron and the oxygen and nitrogen are easy to carry out chemical combination reaction with the molten steel, and the effect of improving the hardenability is lost. Therefore, the content of oxygen and nitrogen in the molten steel is reduced as much as possible before adding boron during smelting, but when the content of B is too much (more than or equal to 0.0025%), the enrichment is easy at a crystal boundary, the bonding energy of the crystal boundary is reduced, the steel plate is more prone to fracture along the crystal when being subjected to impact load, and the low-temperature impact absorption power of the steel plate is reduced. Therefore, the adding amount of B in the invention is 0.0005-0.0022%, and [ N ] is less than or equal to 0.0080% and [ O ] is less than or equal to 0.0020%.
Cu and Ni: 0.3 to 0.5 percent of copper is added into a steel plate with the thickness of more than 50mm, epsilon-Cu precipitation can be formed in the self-tempering process after quenching, the strength and the hardness of the steel are effectively improved, but the Cu-containing steel is easy to cause surface quality defects such as edge overburning, surface warping and the like due to copper brittleness in the heating and hot rolling processes. In order to improve the surface quality of Cu-containing steel, a high-melting-point Ni element is often added to the steel to form a high-melting-point Cu-Ni binary alloy phase, reduce a low-melting-point Cu-rich phase, and increase the solubility of Cu in the steel. For the purpose of completely inhibiting the copper brittleness defect of the Cu-containing steel, the weight ratio of Ni: controlling the Cu ratio to be more than 1: ni is also an element for simultaneously improving the hardness and low-temperature toughness of the steel plate with the thickness of more than 50mm, Ni and Fe form FeNi compounds, and when the steel plate is subjected to low-temperature impact load at lower temperature, the solid-dissolved Ni can improve the low-temperature impact absorption power of the steel plate, but the Ni cost is higher, so that the mechanical property, especially the low-temperature toughness at minus 40 ℃, of the steel plate can be ensured by adding Ni of less than or equal to 0.5 percent into the steel plate with the thickness of more than 50mm, and the steel plate has market competitiveness.
The production method comprises the steps of material selection, surface treatment, composite blank assembly, vacuum welding, rolling and surface grinding, and comprises the following steps:
(1) selecting a base material and a composite material as raw materials for assembly.
The base material and the composite material can be continuous casting blanks, intermediate blanks, steel plates and the like, the length of the base material is 2-4 m, the width of the base material is 1-3 m, the length and the width of the base material are the same as those of the composite material, the thickness ratio of the base material to the composite material is 1-2, the thickness of the base material is 100-150 mm, and the thickness of the composite material is 50-100 mm. The thickness ratio of the base material to the composite material limits the proportion of the composite material in the composite blank, ensures that the high wear resistance of the composite layer and the impact resistance of the base layer can be obtained in the subsequent heat treatment process, and limits the total thickness of the composite blank, thereby limiting the stress amplitude in the assembly sealing and welding process and ensuring the deformation consistency in the heating process of the composite blank. Structurally reducing the crack sensitivity of the composite blank seal weld joint during welding and heating.
(2) And processing the surfaces to be contacted of the base material and the composite material, polishing the surfaces of the base material and the composite material in machining modes such as a planer or a milling machine and the like, and removing the rust layer and the oxide layer of the surface to be contacted.
And removing the oxide layer on the surface to be compounded of the base material and the composite material by using a planing machine or a milling machine and other machining methods, wherein the machining depth is 5-10 mm, and no cooling liquid is added in the machining process. The surface to be compounded of the blank is polished before assembly, a rust layer and an oxide layer are removed, the surface to be compounded of the blank is contacted with each other by fresh metal in the rolling process, metallurgical bonding between the surface to be compounded of the blank and the oxide layer is facilitated, the bonding quality is improved, and the defects of inclusion, air holes, non-bonding and the like are avoided.
(3) And (3) carrying out degreasing treatment on the surfaces to be compounded of the base material and the composite material.
And (3) performing degreasing treatment on the interface to be compounded of the base material and the composite material by using 99.99% high-purity alcohol, and wiping by using non-woven fabrics. After the machining treatment of the surfaces to be compounded of the base material and the composite material is finished, degreasing treatment is further performed by using high-purity alcohol, and the non-woven fabric is used for wiping, so that the cleanliness of the surfaces to be compounded can be effectively improved, and good metallurgical bonding can be formed between the composite interfaces of the wear-resistant composite plate.
(4) And (3) sequentially and centrally stacking the base material and the composite material from top to bottom to form a composite blank.
(5) And vacuumizing the assembled composite blank, and then carrying out vacuum electron beam sealing welding to ensure that the interface between the base material and the composite material to be compounded is in a vacuum environment.
The vacuum degree of the environment of the composite blank is less than or equal to 4.5 multiplied by 10-2Pa; the composite blank is subjected to vacuum electron beam packaging welding in a vacuum environment, so that the gas content between joint surfaces can be reduced to the maximum extent, and the phenomenon that the joint rate is not qualified due to gas residue after rolling is avoided. In addition, the reduction of the gas content between the joint surfaces also contributes to preventing secondary oxidation of the joint surfaces and to improving the joint performance. The effective fusion depth of the vacuum electron beam seal welding is 30-40 mm, the depth-to-width ratio is 7-8, and the cokeThe point position deviates 1-2 mm towards the base material side; the method adopts an electron beam welding process for packaging and welding, can finish welding with large fusion depth under the condition of lower heat input, has larger depth-to-width ratio of the obtained welding joint, and reduces the influence of the welding process on the structure and the performance of the composite blank. Meanwhile, the cost control of industrial mass production is facilitated without using welding materials and reducing welding energy consumption. The welding process of offsetting towards the substrate side is adopted, chemical components in a welding molten pool can be regulated, a joint structure is prevented from being subjected to a martensite region, the joint strength is ensured, and the joint crack sensitivity is reduced.
The vacuum electron beam welding sequence is that the double gun linkage firstly carries out the sealing welding of two long sides and then carries out the sealing welding of two short sides. And when each welding line is welded, the welding line is divided into N sections, N is more than or equal to 5, the length of each section is 200-400 mm, and the welding sequence is that the middle section is welded firstly and then the rest sections are welded in a left-right alternating sequence. The deformation consistency of the composite blank can be ensured by adopting a double-gun linkage process, and the stress concentration degree is reduced; the welding deformation and stress can be gradually released by firstly welding the long side and then welding the short side, and firstly welding the middle section and then welding the rest sections in a left-right sequence, so that the amplitude of the welding stress is reduced. The crack sensitivity of the wear-resistant composite blank in the assembly and seal welding process is reduced through a special seal welding process.
(6) And heating the combined blank subjected to vacuum treatment to 1200-1250 ℃, and preserving heat, wherein the heat preservation time is calculated according to the thickness of the composite blank multiplied by 1 min/mm.
The composite blank is heated by a flame chamber furnace, and a central heating mode is adopted during heating, namely a heating flame hole is positioned at the upper and lower central positions of the long and wide planes of the composite blank, so that the composite blank is heated directly from the center and is heated in a mode of conducting to the periphery. The central heating process is carried out by adopting the flame chamber furnace, so that the composite blank can be subjected to expansion deformation from the center, the conditions that the deformation is inconsistent and the sealing joint is subjected to stress concentration to further crack failure due to the fact that the surface layer of the composite blank is heated and the center is heated slowly are avoided, and the crack sensitivity of the composite blank in the heating process is reduced.
The composite blank is discharged for 1-2 hours before being discharged from the furnace, and the temperature of flame holes on the upper surfaces of the head and the tail of the composite blank is increased by 40-50 ℃. The method for heating the upper surfaces of the head and the tail can improve the temperature of the base materials in a certain range of the upper surfaces of the head and the tail, improve the deformation degree of the base materials in the rolling process, effectively avoid the problem that the composite blanks are easy to warp in the rolling process, and improve the rolling success rate of the composite blanks.
(7) The initial rolling temperature is 1180-1200 ℃, the first pass reduction rate is 15-20%, and the total reduction rate is more than or equal to 50%. Rolling the composite blank in a mode that the base material is arranged on the upper part and 550 wear-resistant steel is arranged on the lower part; the 550-level wear-resistant composite plate is rolled in an asymmetric assembly mode, so that the process complexity of industrial mass production can be effectively simplified, the production efficiency is improved, and the steps of coating a separant of a symmetric assembly and separating the rolled composite plate are avoided.
(8) And carrying out on-line ultra-fast cooling treatment after rolling. And watering and cooling the 550 wear-resistant steel side by adopting on-line ultra-fast cooling to ensure that the cooling speed of the composite layer is 3-5 ℃/s, and measuring the temperature and the re-reddening temperature of the composite layer after cooling is less than 300 ℃. Wherein, the compound layer is watered and cooled by adopting on-line ultra-fast cooling, so that a high-hardness martensite structure can be obtained, and the wear resistance of the martensite structure is ensured. Meanwhile, the cooling speed of the base layer side is effectively controlled, so that the high impact resistance is obtained.
(9) And straightening, trimming and grinding the surface to obtain the wear-resistant composite board with the target thickness, wherein the thickness range is 20-100 mm.
Has the advantages that:
compared with the prior product, the 550-grade composite board of the invention has the following advantages:
1. the prepared wear-resistant composite plate has the composite interface shear strength of over 500MPa, the bonding rate of 100 percent, the Brahman hardness of the wear-resistant layer of over 530 and the room-temperature impact energy of over 118J;
2. the crack sensitivity of the wear-resistant composite blank in the processes of assembly sealing and heating is reduced, the head warping problem in the rolling process is improved, and the production efficiency is improved to more than 80% from about 50% originally.
Drawings
Fig. 1 is a schematic view of an NM550 abrasion resistant composite panel.
Detailed Description
The following examples are intended to illustrate the invention in detail, and are intended to be a general description of the invention, and not to limit the invention.
Table 1 shows the chemical composition of grade 550 wear resistant steel of example of the present invention; table 2 shows the specification of the raw materials of the 550-grade wear-resistant steel of the embodiment of the invention; table 3 shows the actual material and material specifications of the low-carbon low-alloy steel according to the embodiment of the invention; table 4 shows the information related to the composite blanks according to the embodiment of the present invention; table 5 shows the process and billet information before rolling in the examples; table 6 shows the rolling schedule of the examples of the present invention; table 7 shows the results of the performance tests of the examples of the present invention.
TABLE 1 chemical composition (wt%) of grade 550 abrasion resistant steel
Figure BDA0002187753830000111
Table 2 example 550 grade abrasion resistant steel raw material specification
Examples Steel grade Source Length/m Width/m Thickness/mm
1 NM550 Intermediate blank 4 3 80
2 NM550 Sheet material 3.6 2.8 60
3 NM550 Intermediate blank 3.6 2.8 70
4 NM550 Continuous casting billet 4 3 100
TABLE 3 practical materials and raw material specifications of the low-carbon low-alloy steel in the examples
Figure BDA0002187753830000112
Table 4 example composite blank related information
Figure BDA0002187753830000113
TABLE 5 example Pre-Rolling Process and billet information
Figure BDA0002187753830000121
TABLE 6 examples Rolling schedule
Figure BDA0002187753830000122
Table 7 mechanical property test results of examples
Figure BDA0002187753830000123
The embodiment shows that the yield strength, the tensile strength and the elongation of the 550-grade wear-resistant composite plate produced according to the invention all meet the requirements of relevant standards, the room temperature impact is more than or equal to 118J, the shearing strength of the composite surface is more than or equal to 502MPa, the Brinell hardness of the composite layer is more than or equal to 535, the ultrasonic inspection is 100% qualified, the sealing and welding joint does not crack in the welding and heating processes, and the composite blank does not have the problem of head warping in the rolling process.

Claims (2)

1. A550-grade wear-resistant composite board is characterized in that the composite board is formed by compounding low-carbon low-alloy steel and 550-grade wear-resistant steel, wherein C in the low-carbon low-alloy steel is required to be less than or equal to 0.22% by mass percent; the 550-grade wear-resistant steel contains C: 0.25% -0.28%, Si: 0.32-0.38%, Mn: 0.56-0.98%, Cr: 0.84% -0.95%, Mo: 0.15% -0.4%, Nb: 0.01-0.03%, Ni is less than or equal to 0.50%, Cu is less than or equal to 0.50%, B: 0.0008% -0.0019%, Ti: 0.026% -0.038%, Als: 0.020-0.045%, not more than 0.015% of P, not more than 0.005% of S, not more than 0.0080% of N, not more than 0.0020% of O, not less than 3.4% of Ti/N, and the balance of Fe and inevitable impurities, wherein the shearing strength of the composite surface of the composite plate is not less than 502MPa, the bonding rate is 100%, the Brinell hardness of the composite layer is not less than 535, and the room-temperature impact energy is not less than 118J;
the preparation method of the 550-level wear-resistant composite plate comprises the steps of material selection, surface treatment, composite blank assembly, vacuum welding, rolling and surface polishing, wherein,
(1) selecting a base material and a composite material as raw materials for assembly; the base material is low-carbon low-alloy steel with the C content of less than or equal to 0.22% in percentage by mass, the composite material is 550-grade wear-resistant steel, the base material and the composite material are continuous casting blanks, intermediate blanks and steel plates, the length of the base material is 2-4 m, the width of the base material is 1-3 m, the length and the width of the base material are the same as those of the composite material, the thickness ratio of the base material to the composite material is 1-2, the thickness of the base material is 100-150 mm, and the thickness of the composite material is 50-100 mm;
(2) processing the surfaces to be contacted of the base material and the composite material, and removing a rust layer and an oxide layer on the surface to be contacted, wherein the processing depth is 7-10 mm;
(3) carrying out degreasing treatment on the surfaces to be compounded of the base material and the composite material;
(4) the base material and the composite material are stacked and assembled in the middle from top to bottom to form a composite blank;
(5) vacuumizing the assembled composite blank, and then carrying out vacuum electron beam sealing welding to enable the interface between the base material and the composite material to be composited to be in a vacuum environment; the vacuum degree of the environment of the composite blank is 3.0 multiplied by 10-2～4.4×10-2Pa; the effective penetration of vacuum electron beam sealing welding is 30-36 mm, the depth-to-width ratio is 7-8, and the focus position deviates 1-2 mm to the substrate side; the vacuum electron beam welding sequence is double-gun linkage, namely, firstly performing sealing welding on two long sides and then performing sealing welding on two short sides, and each welding seam is divided into N sections when being welded, wherein N is more than or equal to 5, the length of each section is 200-400 mm, the welding sequence is that firstly performing welding on the middle section number and then performing welding on the rest section number in a left-right alternating sequence;
(6) heating the combined blank after vacuum treatment to 1225-1240 ℃, and preserving heat, wherein the heat preservation time is calculated according to the thickness of the composite blank multiplied by 1 min/mm; when the composite blank is heated, a central heating mode is adopted, namely a heating flame hole is positioned at the upper and lower central positions of the long and wide planes of the composite blank, so that the composite blank is heated directly from the center and is heated in a mode of conducting to the periphery; 1-2 hours before the composite blank is discharged from the furnace, and the temperature of flame holes on the upper surfaces of the head and the tail of the composite blank is increased by 40-50 ℃;
(7) rolling the composite blank in a mode that the base material is arranged on the upper part and 550 wear-resistant steel is arranged on the lower part; the initial rolling temperature is 1180-1200 ℃, the first-pass reduction rate is 16-20%, and the total reduction rate is 50-70%;
(8) after rolling, carrying out online ultra-fast cooling treatment, adopting online ultra-fast cooling to water and cool the 550 wear-resistant steel side, enabling the cooling speed of the composite layer to be 3-5 ℃/s, and carrying out temperature measurement and re-reddening on the composite layer after cooling, wherein the temperature re-reddening temperature is less than 300 ℃;
(9) and obtaining the wear-resistant composite board with the target thickness after straightening, trimming and surface polishing.
2. The 550-grade abrasion resistant composite panel of claim 1, wherein the thickness of the finished composite panel is in the range of 36mm to 100 mm.
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