CN111378900B - Steel for wear-resistant and corrosion-resistant chain plate and manufacturing method thereof - Google Patents

Steel for wear-resistant and corrosion-resistant chain plate and manufacturing method thereof Download PDF

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CN111378900B
CN111378900B CN202010364033.XA CN202010364033A CN111378900B CN 111378900 B CN111378900 B CN 111378900B CN 202010364033 A CN202010364033 A CN 202010364033A CN 111378900 B CN111378900 B CN 111378900B
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CN111378900A (en
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杨玉
谷春阳
王英海
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Angang Steel Co Ltd
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    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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
    • Y02P10/20—Recycling

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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention provides wear-resistant corrosion-resistant steel for a chain plate and a manufacturing method thereof, wherein the steel comprises the following components in percentage by weight: c: 0.48% -0.63%, Si: less than or equal to 0.40%, Mn: 0.4-1.1%, Cr: less than or equal to 0.50 percent, and less than or equal to 0.5 percent of Nb; al: 0.015% -0.1%, V: 0.05-0.5%, Ti: 0.03-0.1%, 0.05-0.5% of Cu, Sb: 0.05 to 0.2 percent of the total weight of the alloy, less than or equal to 0.0015 percent of O, less than or equal to 0.020 percent of impurity element P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities. The manufacturing method comprises smelting, slab continuous casting and rolling and hot rolling, and the average corrosion rate of the steel plate produced by the invention is not more than 20g/m2H, various non-metallic inclusions are less than 1.5 grade, the depth of a single-side surface decarburized layer is less than 1.5 percent of the plate thickness, no crystal boundary oxidation exists, the hardness after heat treatment is more than 45HRC, the wear resistance, the corrosion resistance and the fatigue performance of the processed chain plate are obviously improved, and the service life is prolonged by more than 60 percent.

Description

Steel for wear-resistant and corrosion-resistant chain plate and manufacturing method thereof
Technical Field
The invention belongs to the field of metal materials, and particularly relates to wear-resistant and corrosion-resistant steel for a chain plate and a manufacturing method thereof.
Background
At present, chain plates are mostly processed by 40Mn and 45Mn steel plates, the surface hardness of raw material steel plates is generally required to be 85 HRB-90 HRB so as to ensure the quality of the parts after stamping, the hardness after heat treatment is 38-42HRC, and the problems of chain extension, reduction of the efficiency of a power system, short service life, frequent replacement and the like are caused by easy abrasion deformation in the long-term use process. Especially for some automobile power chains, the service life of the chain directly influences the service life of an automobile engine and even the whole automobile. On the other hand, the surface of the chain plate is easy to corrode in corrosive environments such as marine climate and the like, and under the using condition, the chain plate is easy to impact, wear and damage, and the service life is seriously influenced.
The invention discloses a low-carbon microalloyed steel and a method for producing a chain link plate by using the same (99100724.7), and discloses a cold-rolled sheet with low carbon content, high manganese content and high vanadium content for the chain link plate. Low carbon content, relatively low hardness after heat treatment, and insufficient wear resistance.
The invention discloses a continuous casting process for processing a round chain by a square billet (CN103252466A), belonging to the production process of profiles, wherein the square billet has small size, the continuous casting billet is easy to produce, and the parameters of a smelting casting billet cooling process and the like are completely different from the continuous casting of a plate blank. And the finished product is a round chain, which has different purposes from the chain plate.
The invention relates to a chain steel material (CN103422034A), and the invention relates to a chain plate material of a pipeline chain plate conveyor (CN109881128A), both the invention and the invention add unconventional compounds or elements, need a special production method, and have high cost and complex production process.
The invention discloses steel for circular chain and a manufacturing method thereof (CN102653834A), and discloses mining large-specification high-strength chain steel and a preparation method thereof (CN 201410800419.5). A90-grade chain steel (CN201811242708.2) is an annular chain processed by section bars, the steel for chain has low carbon content, high alloy contents of Ni, Cr, Mo and the like, and high cost, and the conventional heat treatment process cannot meet the requirements of high hardness and high wear resistance of the chain plate.
The outer chain plate of chain (CN 2206868Y) describes the improvement of the shape of chain plate, and does not mention the material.
A caterpillar band steel with high strength, high antiwear nature and long fatigue life and its production process (CN201610507885.3) disclose a round bar rolled from continuous casting square billet, which is not suitable for making chain plate. And the C content is 0.28-0.32%, which is lower, the hardness after heat treatment is difficult to reach more than 37HRC, the Mn content is more than 1.45%, segregation is easy to form, the structure is not uniform, and the fatigue performance is influenced.
The documents of 18MnZL hot rolled strip steel for bicycle chains, chemical component design of steel for racing chains, development and application of steel for cold rolled chain of Wu steel and the like all introduce cold rolled steel plate steel. The 16Mn chain steel introduced in the 16Mn steel chain plate fracture analysis has low carbon content, can meet the hardness requirement after carburization, and has complex process.
The steel grades mentioned in the above documents and inventions are not suitable for directly processing the high-wear-resistant chain plate by using the hot rolled plate. Therefore, the hot rolled steel strip is suitable for directly processing various chain plates, and has high hardness after heat treatment, good wear resistance and long service life.
Disclosure of Invention
The invention aims to overcome the problems and the defects and provide the steel for the wear-resistant and corrosion-resistant chain plate and the manufacturing method thereof, the steel for the chain plate has the hardness of more than 45HRC after heat treatment, is corrosion-resistant, and has the wear-resistant life of more than 60 percent longer than that of a common chain plate.
The purpose of the invention is realized as follows:
the steel for the wear-resistant corrosion-resistant chain plate comprises the following components in percentage by weight: c: 0.48% -0.63%, Si: less than or equal to 0.40 percent, Mn: 0.4% -1.1%, Cr: less than or equal to 0.50 percent and less than or equal to 0.5 percent of Nb; al: 0.015% -0.1%, V: 0.05-0.5%, Ti: 0.03-0.1%, 0.05-0.5% of Cu, Sb: 0.05 to 0.2 percent of the total weight of the alloy, less than or equal to 0.0015 percent of O, less than or equal to 0.020 percent of impurity element P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities.
The microstructure of the steel for the wear-resistant corrosion-resistant chain plate is uniform and fine ferrite and pearlite, the proportion of the ferrite is 28-38%, the yield strength is 380-480MPa, the grain size is more than 8 grade, the surface roughness of the steel plate is less than 1.8 mu m, and the average corrosion rate is not more than 20g/m2H, various non-metallic inclusions are less than 1.5 grade, and the depth of the decarburized layer on the single-side surface of the steel plate is less than 1.5 percent of the plate thickness.
The invention has the following design reasons:
c is a main solid solution strengthening element in steel. If the C content is less than 0.48%, it is difficult to ensure a hardness of 45HRC or more after the heat treatment, while if the C content is more than 0.63%, the toughness and plasticity of the steel deteriorate and the chain is liable to brittle failure. Therefore, the C content is controlled to be 0.48-0.63%.
Mn is a good deoxidizer and desulfurizer, and is an essential element for ensuring the strength and toughness of steel. Manganese and iron form a solid solution, which can increase the hardness and strength of ferrite and austenite in steel. Mn and S are combined to form MnS, so that the influence of hot cracks caused by FeS formed at the grain boundary on the hot formability of the steel for the saw blade is avoided. Meanwhile, Mn is also a good deoxidizer and increases hardenability. The Mn content is too low to meet the requirement of high strength and hardness after heat treatment, and the Mn content is too high to form segregation zones to influence the welding performance and increase the production cost, so the Mn content should be controlled to be 0.4-1.1% by comprehensively considering the factors of cost, performance requirements and the like.
Si is one of common elements in steel and is used as a reducing agent and a deoxidizing agent in the steelmaking process, and Si in a solid solution form can improve the yield strength and the ductile-brittle transition temperature, but if the content of Si exceeds the upper limit, the toughness and the welding performance are reduced. On the other hand, Si is a ferrite forming element, and the high content of Si can cause serious decarburization on the steel surface, so that the content of Si is not easy to be too high, and the content of Si is less than or equal to 0.40 percent.
Cr is an element for remarkably improving the hardenability of steel, a proper amount of Cr is added into the steel to enable a C curve to move to the right, and the spacing between pearlite pieces obtained at the same cooling speed is more refined. For high carbon steel, Cr can increase the activation energy of carbon diffusion and reduce the decarburization tendency of steel. On the other hand, Cr can also increase the ferrite electrode potential, promote the formation of a dense oxide film on the surface of steel, and improve the corrosion resistance. The Cr content is too high, the alloy cost is increased, and the shape of the steel plate is poor and difficult to level, so the Cr content is controlled to be less than or equal to 0.50 percent.
Nb is a micro-alloy element for fine grain strengthening and precipitation strengthening, and the toughness and plasticity of the hot-rolled steel plate and the strength and toughness of the steel after heat treatment can be improved by adding a proper amount of Nb into the steel. Usually, the microalloyed Nb content in the steel is 0.01-0.05%, and the Nb content less than or equal to 0.5% is more than ten times of the normal addition amount in the invention. By adding Nb to steel, fine carbonitride two-phase particles such as NbC and NbCN can be precipitated during hot working, thereby suppressing the deformation recrystallization of austenite, preventing the growth of austenite grains, and refining the grains. The type and size of the generated particles directly influence the service performance of the steel, such as wear resistance and the like. For example, NbC particles smaller than 30um are produced, the effect of grain refinement is obvious, the hardness after heat treatment is obviously improved, the wear resistance is enhanced, and the service life is prolonged. When the length of a timing chain in an engine extends by 50% due to severe wear after a current automobile is used for several years, the engine is judged to be useless. After 0.1% -0.5% of Nb is added into the chain steel, the wear resistance is obviously improved, when a common engine is scrapped due to other reasons, the length of the chain is only extended by 20% to the maximum extent, namely, the engine cannot be scrapped due to the problem of abrasion and extension of the timing chain, and the service life of the engine is prolonged equivalently. On the other hand, Nb can suppress the oxidation and decarburization of the steel surface. Therefore, Nb is controlled to be less than or equal to 0.5 percent.
V, Ti is also a fine-grain strengthening and precipitation strengthening microalloy element, V, Ti is added into steel, fine carbonitride two-phase particles can be separated out in the hot working process, the deformation recrystallization of austenite is inhibited, the growth of austenite grains is prevented, and the grains are refined. On the other hand, V also improves hardenability and thermal stability. Therefore, the addition of appropriate amounts of Ti and V to the steel can improve the toughness and plasticity of the hot-rolled steel sheet and the strength and toughness of the steel after heat treatment. Of course, too high a content increases the cost, and therefore, controlling V: 0.05-0.5%, Ti: 0.03 to 0.1 percent.
Cu:0.05 percent to 0.5 percent; the prominent effect of Cu in the steel is to improve the atmospheric corrosion resistance of the steel, and simultaneously, the addition of the copper can improve the strength and yield ratio of the steel and does not deform during stamping. Cu in the corrosion-resistant steel is often used together with P, and both Cu and P can be concentrated in a rust layer, so that the rust layer is compact and stable, and the rust expansion can be inhibited. When [ Cu ] is low (about 0.01%), the corrosion resistance of the steel is improved by more than 2 times after 0.06-0.10% of P is added. When [ Cu ] is high (about 0.4%), 0.10% of P is added, and the corrosion resistance is only improved by 20% -40%, which shows that P and Cu have extremely complex relationship. In order to ensure the punching property, the P content in the invention is not easily too high, so that a small amount of Cu is added.
Sb: the addition of 0.05-0.2% of antimony into the steel generally reduces the strength of the steel and increases the brittleness, but the addition of a certain amount of antimony improves the corrosion resistance and wear resistance of the steel, so that the addition of 0.05-0.2% of antimony into the steel of the invention improves the corrosion resistance and wear resistance.
Al: 0.015-0.1%, Al is generally used as deoxidizer during smelting, crystal grains can be refined, the strength is improved, but Al-containing oxide inclusion is easily formed at the same time, and the fatigue performance of steel is influenced. Therefore, the Al content is controlled to be 0.015-0.10%.
O: o is less than or equal to 0.0015 percent, oxygen is a residual element in steel making, the oxygen content is high, a large amount of non-metallic inclusions exist, and the fatigue performance is seriously influenced. In order to ensure the strength and hardness of the steel for the chain plate after heat treatment, the steel for the chain plate has medium C content and overhigh oxygen content in high-carbon steel, and non-metallic inclusions are not easy to float up during smelting, so that the inclusions in the steel are excessive, and the fatigue life is influenced, therefore, the invention requires that O in a finished steel plate is less than or equal to 0.0015 percent.
P and S are inevitable harmful impurities in steel, and the existence of P and S can seriously deteriorate the toughness of the steel, influence the fatigue performance and shorten the service life. Measures are therefore taken to keep the P and S contents in the steel as low as possible. According to the invention, the maximum P content is limited to 0.020% and the maximum S content to 0.010%.
The components are designed to have medium and high carbon content, and alloy elements such as Mn, Cr and the like are added, so that the hardenability and hardenability are improved, the hardness of the steel plate after heat treatment is ensured to be more than 45HRC, and the wear resistance is improved. The addition of Nb, V and Ti further refines crystal grains and improves the hardness and wear resistance of the steel plate after heat treatment. A certain amount of Cu and Sb are added to form a compact oxidation film on the surface of the steel plate, so that the atmospheric corrosion resistance of the chain plate is improved, the content of impurity elements such as P, S, O and the like is strictly controlled, the fatigue performance of the steel is improved, and the service life of the chain plate is prolonged.
The second technical proposal of the invention provides a manufacturing method of the steel for the wear-resistant and corrosion-resistant chain plate, which comprises smelting, slab casting and rolling, and hot rolling,
(1) smelting:
converter smelting and LF or RH external refining are carried out, and the refining treatment time is required to be more than 30min so that nonmetallic inclusions can float sufficiently, the quality of molten steel is ensured, and the fatigue performance of a finished steel plate is improved; the O content of the middle package is required to be less than or equal to 0.0020 percent so as to ensure that the O content of a finished product is less than or equal to 0.0015 percent;
(2) slab continuous casting and rolling:
continuously casting by adopting a vertical bending or vertical continuous casting machine, slightly reducing the solidification rate of a slab at 55-75%, wherein the temperature of the casting blank is above 930 ℃ during continuous casting and secondary cooling of the vertical bending casting machine, the thickness of the slab is not more than 230mm, continuously casting and rolling the slab, directly heating the slab in a heating furnace without falling down a roller way after the slab is cut off, and rolling; the slab is put into a heating furnace and the temperature is above 700 ℃.
(3) The hot rolling process comprises the following steps:
(a) the heating furnace adopts a reducing atmosphere stepping heating furnace, the heating temperature of the casting blank is 1100-1250 ℃, the temperature of the furnace is 4-6h, the surface decarburization is reduced as much as possible while the uniform heating of the casting blank is ensured, the surface grain boundary oxidation is inhibited,
(b) the fine and rough rolling adopts high-pressure water for descaling, and the water pressure is more than 15MPa, so that the surface quality of the finished steel plate is ensured;
(c) the first pass reduction rate of rough rolling is more than 40 percent, and the rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 85 percent, and the finish rolling temperature is 750-900 ℃;
(e) after the strip steel is discharged from the finishing mill, the strip steel is cooled to below 680 ℃ at a cooling speed of more than 15 ℃/S and coiled so as to control the size of two-phase particles.
Converter smelting and LF or RH external refining treatment are adopted, the treatment time is more than 30min, the floating of nonmetallic inclusions is facilitated to be sufficient, the purity of molten steel is ensured, and the fatigue performance of a finished steel plate is improved; the content of O in the medium package is required to be less than or equal to 0.0020 percent so as to ensure that the content of O in the finished product is less than or equal to 0.0015 percent and various non-metallic inclusions are less than 1.5 grades.
Continuous casting is carried out by adopting a vertical bending type or vertical type continuous casting machine, and soft reduction is carried out at the position with 55% -75% of the solidification rate of a casting blank in continuous casting. The continuous casting process is too early in reduction, the liquid core is too small in thickness, inclusion floating is not facilitated, the reduction is too late, the liquid core at the reduction position is too large in thickness, and the casting blank is prone to crack, segregation and other defects. The casting blank temperature is above 930 ℃ during the continuous casting secondary cooling of the vertical bending type casting machine, and cracks are avoided when the casting blank is bent and cooled.
In order to control the size of the two-phase particles, the thickness of the slab cannot be larger than 230mm, so that the cooling of the slab is promoted, the storage energy is reduced, and the growth of the two-phase particles is inhibited. On the other hand, the temperature of the plate blank in the heating furnace is more than 700 ℃, so that serious surface decarburization and oxidation caused by long-time secondary heating are avoided, meanwhile, the solid solution of two-phase particles in the casting blank is promoted, so that fine two-phase particles are generated again in the rolling process, crystal grains are refined, the hardness and the wear resistance after heat treatment are improved, and the service life of the chain plate is prolonged.
Refining, continuous casting and rolling by adopting a hot continuous rolling unit. The heating temperature of a casting blank is 1100-1250 ℃, the furnace time is 4-5h, the solid solution speed of Nb particles is obviously increased at the temperature of more than 1100 ℃, the solid solution amount is obviously increased, and more than 70 percent of Nb is dissolved in the steel after the temperature reaches 1200 ℃. According to the characteristics of the stepping heating furnace, the casting blank is calculated to have enough time to promote the solid solution of Nb at 1100-1250 ℃ after being put into the furnace at 700 ℃ for more than 4 hours. After the furnace time exceeds 5 hours, the surface of the casting blank is seriously oxidized and decarburized, and the surface hardness and the fatigue performance after heat treatment are influenced. The surface scale is removed by adopting a high-pressure water descaling technology, so that the surface decarburization oxidation of the finished steel plate is reduced, the depth of a single-surface decarburized layer is ensured to be less than 1.5 times of the plate thickness, no crystal boundary oxidation exists, the surface roughness is below 1.8 mu m, a compact oxidation film is easily formed on the surface of the steel plate, and the atmospheric corrosion resistance of the chain plate is further improved.
The large reduction rate of the first time which is more than 40 percent is adopted, the final rolling temperature is 750-900 ℃, the austenite region is rolled, the large reduction rate of the first time is adopted, the segregation of the casting blank structure is broken, the banding of the finished product is reduced, and the uniformity of the finished product structure is improved. The total reduction rate of the Nb-containing steel in finish rolling is more than 85%, recrystallization is promoted, a new austenite grain zone is formed, grains are refined, and the surface hardness and the wear resistance are ensured. After rolling, the steel plate is rapidly cooled to below 680 ℃ at a cooling speed of more than 15 ℃/S for coiling, so that on one hand, the growth of Nb-containing particles can be inhibited, the particle size is controlled to be below 50 mu m, austenite grains are refined, on the other hand, the surface oxidation can be inhibited, the surface of the steel plate is promoted to form a compact oxide layer, the corrosion resistance is improved, and the fatigue performance is further improved. The cooling speed is lower than 15 ℃/S, the formed particles are large, after coiling at the temperature of more than 680 ℃, the particles grow obviously, and the corrosion resistance of an oxide layer formed on the surface of the steel plate is poor. The grain is larger than 50um, not only can austenite grain not be refined, but also the mechanical property of steel can be influenced, and the surface of the steel plate is easy to oxidize and decarbonize, the surface grain boundary is seriously oxidized, surface microcracks are easy to form, and the fatigue property is seriously influenced.
A heat treatment method of wear-resistant corrosion-resistant steel for a chain plate comprises the following steps of processing the steel for the chain plate into a semi-finished product of the chain plate, and carrying out heat treatment on the semi-finished product:
heating at the temperature of 820-.
The chain plate structure is tempered martensite with the hardness of more than 45 HRC.
The invention has the beneficial effects that: the steel plate produced by applying the technical scheme disclosed by the invention adopts a continuous casting production process, so that the yield is high and the production cost is low; austenite grains are fine and uniform, and the grain size is more than 8 grades; the hot rolled plate structure is uniform and fine ferrite and pearlite, the proportion of the ferrite is 28-38%, the yield strength is 380-480MPa, and the surface roughness is below 1.8 mu m, so that a compact oxidation film is easily formed on the surface of the steel plate, and the atmospheric corrosion resistance of the chain plate is further improved; average corrosion rate not more than 20g/m2H, various non-metallic inclusions are less than 1.5 grades, the depth of a single-side surface decarburization layer is less than 1.5 percent of the thickness of the plate, and the non-metallic inclusions are not oxidized in a crystal boundary. The hardness after heat treatment is more than 45HRC, the wear resistance, corrosion resistance and fatigue performance of the processed chain plate are obviously improved, and the service life is prolonged by more than 60%.
Detailed Description
The present invention is further illustrated by the following examples.
According to the embodiment of the invention, smelting, slab continuous casting and rolling and hot rolling are carried out according to the component proportion of the technical scheme.
(1) Smelting:
converter smelting, LF or RH external refining, wherein the refining treatment time is required to be more than 30min, and the middle package O is required to be less than or equal to 0.0020% so as to ensure that the finished product O is less than or equal to 0.0015%;
(2) slab continuous casting and rolling:
carrying out soft reduction at the position with the solidification rate of 55-75% of the plate blank, wherein the thickness of the plate blank is not more than 230mm, carrying out continuous casting and rolling on the plate blank, directly heating the plate blank in a heating furnace without going down a roller way after the plate blank is cut off, and waiting for rolling; the slab is put into a heating furnace and the temperature is above 700 ℃.
(3) The hot rolling process comprises the following steps:
(a) the heating furnace adopts a reducing atmosphere heating furnace, the heating temperature of a casting blank is 1100-1250 ℃, and the casting blank is heated in the furnace for 4-6 h;
(b) the fine and rough rolling adopts high-pressure water to remove scale, and the water pressure is more than 15 MPa;
(c) the first pass reduction rate of rough rolling is more than 40 percent, and the rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 85 percent, and the finish rolling temperature is 750-900 ℃;
(e) after the strip steel is taken out of the finishing mill, the strip steel is cooled to below 680 ℃ at a cooling speed of more than 15 ℃/S and coiled.
Furthermore, the continuous casting is carried out by adopting a vertical bending type or vertical type continuous casting machine, and the casting blank temperature is more than 930 ℃ when the vertical bending type casting machine carries out continuous casting and secondary cooling.
Further, the heating furnace is a walking beam heating furnace.
A heat treatment method of wear-resistant corrosion-resistant steel for a chain plate comprises the following steps of processing the steel for the chain plate into a semi-finished product of the chain plate, and carrying out heat treatment on the semi-finished product:
heating at the temperature of 820-.
The compositions of the steels of the examples of the invention are shown in table 1. The main process parameters of the steel of the embodiment of the invention are shown in Table 2. The heat treatment process of the steels of the examples of the present invention is shown in Table 3. The properties of the steels of the examples of the invention are shown in Table 4.
TABLE 1 composition (wt%) of steels of examples of the present invention
Examples C Si Mn P S Cr Nb V Ti Cu Sb Al Finished product O
1 0.55 0.25 0.40 0.015 0.005 0.02 0.10 0.1 0.03 0.05 0.05 0.015 0.0015
2 0.56 0.27 0.92 0.004 0.009 0.15 0.32 0.3 0.05 0.22 0.082 0.058 0.0012
3 0.58 0.08 0.91 0.008 0.02 0.22 0.015 0.22 0.07 0.15 0.055 0.029 0.0011
4 0.60 0.16 0.55 0.010 0.018 0.10 0.29 0.15 0.10 0.05 0.05 0.025 0.0005
5 0.59 0.40 0.60 0.012 0.004 0.45 0 0.20 0.04 0.28 0.08 0.078 0.0007
6 0.57 0.15 0.75 0.014 0.003 0.39 0 0.16 0.03 0.32 0.05 0.018 0.0008
7 0.52 0.16 0.88 0.013 0.008 0.50 0.35 0.18 0.05 0.27 0.075 0.055 0.00012
8 0.54 0.27 0.82 0.014 0.004 0.48 0.20 0.21 0.06 0.05 0.020 0.029 0.0008
9 0.59 0.30 0.99 0.012 0.007 0.25 0.15 0.12 0.07 0.35 0.010 0.038 0.00010
10 0.57 0.08 0.68 0.010 0.01 0.14 0.09 0.05 0.05 0.13 0.06 0.045 0.0008
11 0.63 0.09 0.70 0.008 0.007 0.48 0.062 0.5 0.04 0.45 0.073 0.098 0.0003
12 0.55 0.07 0.82 0.013 0.006 0.35 0.10 0.4 0.05 0.06 0.20 0.033 0.0009
13 0.54 0.16 1.08 0.013 0.008 0.25 0.25 0.35 0.03 0.27 0.085 0.035 0.0002
14 0.49 0.06 0.82 0.014 0.004 0.08 0.45 0.3 0.04 0.05 0.17 0.040 0.0009
15 0.53 0.10 0.79 0.012 0.007 0.15 0.5 0.32 0.05 0.15 0.038 0.058 0.00010
16 0.50 0.18 0.88 0.030 0.01 0.46 0.36 0.28 0.03 0.33 0.11 0.055 0.00013
17 0.52 0.15 0.80 0.025 0.025 0.32 0.27 0.45 0.05 0.25 0.18 0.049 0.00010
18 0.48 0.27 0.72 0.004 0.009 0.45 0.022 0.19 0.06 0.05 0.05 0.048 0.00012
TABLE 2 Main Process parameters of the steels of the examples of the invention
Figure BDA0002475969220000121
TABLE 3 Heat treatment Process of steels of examples of the invention
Numbering Heating temperature of Holding time min Cooling to a temperature of Tempering temperature DEG C Quenching oil temperature DEG C
1 825 20 180 350 55
2 830 30 195 320 45
3 840 25 150 330 50
4 828 29 170 360 65
5 830 15 180 300 55
6 845 22 160 380 44
7 820 30 180 355 56
8 833 40 178 388 59
9 840 35 180 450 65
10 820 33 150 390 75
11 830 43 150 320 80
12 850 40 145 440 55
13 826 25 180 360 20
14 830 30 165 375 55
15 845 28 180 350 35
16 825 27 170 425 45
17 838 30 180 400 55
18 840 40 165 390 50
TABLE 4 Properties of steels of examples of the invention
Figure BDA0002475969220000141
In order to express the present invention, the above embodiments are properly and fully described by way of examples, and the above embodiments are only used for illustrating the present invention and not for limiting the present invention, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the present invention, and any modifications, equivalent substitutions, improvements, etc. made by the persons skilled in the relevant art should be included in the protection scope of the present invention, and the protection scope of the present invention should be defined by the claims.

Claims (1)

1. The utility model provides a wear-resisting corrosion-resistant link joint uses steel which characterized in that, C: 0.54% -0.63%, Si: less than or equal to 0.40 percent, Mn: 0.4% -1.1%, Cr: 0.08-0.50% of Nb, 0.36-0.5% of Nb; al: 0.055% -0.1%, V: 0.3% -0.5%, Ti: 0.03-0.1%, 0.32-0.5% of Cu, Sb: 0.05-0.18 percent, less than or equal to 0.0015 percent of O, less than or equal to 0.020 percent of impurity element P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities, wherein the Nb-containing particle size in the steel is less than 50 mu m;
the microstructure of the steel for the wear-resistant corrosion-resistant chain plate is ferrite and pearlite, the ferrite volume percentage is 28-38%, the yield strength is 380-480MPa, the grain size is more than 8 grade, the surface roughness of a steel plate is less than 0.98 mu m, and the average corrosion rate is not more than 20g/m2H, various non-metallic inclusions are less than 1.5 grade, and the depth of a decarburized layer on the single-side surface of the steel plate is less than 1.5 percent of the plate thickness;
the manufacturing method of the steel for the wear-resistant corrosion-resistant chain plate comprises smelting, slab continuous casting and rolling and hot rolling;
(1) smelting:
converter smelting, LF or RH external refining, wherein the refining treatment time is required to be more than 30min, and the middle package O is required to be less than or equal to 0.0020% so as to ensure that the finished product O is less than or equal to 0.0015%;
(2) slab continuous casting and rolling:
carrying out soft reduction at the position with the solidification rate of 55-59% of the plate blank, wherein the thickness of the plate blank is not more than 230mm, carrying out continuous casting and rolling on the plate blank, directly heating the plate blank in a heating furnace without going down a roller way after the plate blank is cut off, and waiting for rolling; putting the plate blank into a heating furnace at the temperature of more than 700 ℃;
(3) the hot rolling process comprises the following steps:
(a) the heating furnace adopts a reducing atmosphere heating furnace, the heating temperature of a casting blank is 1100-1250 ℃, and the heating time in the furnace is 4-6 h;
(b) the fine and rough rolling adopts high-pressure water to remove scale, and the water pressure is more than 15 MPa;
(c) the first pass reduction rate of rough rolling is more than 40%, and the initial rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 85%, and the finish rolling temperature of the finish rolling is 750-860 ℃;
(e) after the strip steel is taken out of the finishing mill, cooling the strip steel to below 618 ℃ at a cooling speed of 15-48 ℃/s and coiling the strip steel;
the continuous casting is carried out by adopting a vertical bending type or vertical type continuous casting machine, and the casting blank temperature is more than 930 ℃ when the vertical bending type casting machine carries out continuous casting and secondary cooling; the heating furnace adopts a stepping heating furnace;
after the steel for the chain plate is processed into a semi-finished product of the chain plate, heat treatment is carried out, and the specific process comprises the following steps:
heating at 820-850 ℃, keeping the temperature for 15-40min, performing oil quenching, cooling to below 200 ℃, putting into a furnace, and tempering, wherein the tempering temperature is 300-450 ℃, and the temperature of quenching oil is not higher than 80 ℃;
the chain plate structure prepared after the heat treatment process is tempered martensite with the hardness of more than 45 HRC.
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