CN108220806B - Ultrahigh-strength high-toughness wear-resistant steel and manufacturing method thereof - Google Patents
Ultrahigh-strength high-toughness wear-resistant steel and manufacturing method thereof Download PDFInfo
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- 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
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- 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
- C21D1/26—Methods of annealing
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- 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
- C21D2211/002—Bainite
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- 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
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Abstract
The invention discloses ultra-high strength and high toughness wear resistant steel and a preparation method thereof, wherein the chemical components of the steel comprise, by weight, 0.25-0.55% of C, 1.50-2.50% of Si, 1.50-2.20% of Mn, 0.3-1.0% of Cr, 0.2-0.8% of Mo, 0.01-0.1% of Re, less than 0.01% of S, less than 0.01% of P and the balance of Fe. The scrap steel or molten iron is mixed with alloy material, smelted in an electric arc furnace or a medium frequency induction furnace, refined in VOD and LF, and formed by continuous casting or die casting. After rolling or forging forming of a continuous casting billet or an ingot and special heat treatment, the tensile strength of the part is 1800-2000 MPa, the elongation is 16-18%, and the impact toughness aku is 60-80J/cm2And the hardness is HRC 55-62. The super-strong wear-resistant steel not only has welding performance, but also has outstanding plasticity, and is 2000 MPa-grade super-strong steel with the elongation percentage after fracture reaching 18 percent.
Description
Technical Field
The invention relates to 1800-2000 MPa grade SiMnCrMoRe system medium-carbon low-alloy ultrahigh-strength high-toughness wear-resistant steel, in particular to ultrahigh-strength high-toughness wear-resistant steel and a manufacturing method thereof.
Background
The metallurgical coal mine field has a huge demand for wear-resistant materials. Compared with wear-resistant cast iron, wear-resistant steel is a wear-resistant material which is most widely applied due to the comprehensive properties of hardness, strength and toughness. In the history of the development of wear resistant steels, it has been concluded that bainitic steels, austenite/bainite dual phase steels, martensite/bainite dual phase steels, etc. all exhibit the most excellent overall properties. In recent years, by using silicon as a main alloying element and utilizing the characteristic that the silicon strongly inhibits carbide precipitation in the bainite transformation process, an austenite-bainite dual phase structure composed of carbide-free bainitic ferrite and residual austenite stabilized by carbon and silicon can be obtained, because no carbide eliminates the inducement of cracks or peeling, the alloy has excellent comprehensive mechanical property of toughness and toughness, is the most favored new generation of high-strength high-toughness wear-resistant steel in the world at present, but, carrying out super-cooled austenite low-temperature bainite isothermal transformation for a long time (1-3 weeks) at the temperature slightly higher than the martensitic transformation temperature of the steel, although a nanostructured carbide-free bainitic structure consisting of 30100 nm thick lath bainitic ferrite and residual austenite was obtained, and has ultrahigh strength, higher fracture toughness and better compression plasticity, but the isothermal transformation speed is extremely slow. Because the industrial production has long period and low efficiency, and the carbon content of the alloy steel exceeds 0.6 percent, the alloy steel belongs to high-carbon alloy steel, has poor welding performance and is difficult to apply. Although in subsequent studies, the addition of Co and Al accelerates the bainite transformation rate, and the reduction of Mn ratio and the increase of Co can accelerate the bainite transformation more effectively, and bring about significant cost reduction, in mass production, particularly in the isothermal quenching process of large-sized workpieces, the realization of the isothermal quenching process in industrial production is difficult.
The simultaneous improvement of the obdurability of the steel materials is one of the goals pursued by material researchers, and the tissue refinement is almost the only way. The low-temperature bainite with excellent performance is the lath with thickness of tens of nanometers, so that the toughness is simultaneously improved. How to accelerate the transformation speed of bainite-martensite and ensure that the obtained nano-scale carbide-free bainite-martensite structure is the key for realizing industrial application and popularization of high-strength and high-toughness steel. Besides the proper design of the chemical components of the steel, the steel has good welding performance and low MS transformation temperature, the low-temperature bainite transformation condition is ensured to be obtained, more interface defects formed by phase transformation are utilized, more bainite nucleation positions are provided, the isothermal bainite transformation speed of the retained austenite is accelerated, and the industrial production efficiency is improved.
Disclosure of Invention
The invention aims to provide low-cost ultrahigh-strength high-toughness wear-resistant steel which has weldability and forgeability and can realize industrial production and a manufacturing method thereof. The following presents a simplified summary in order to provide a basic understanding of some aspects of the disclosed embodiments. This summary is not an extensive overview and is intended to neither identify key/critical elements nor delineate the scope of such embodiments. Its sole purpose is to present some concepts in a simplified form as a prelude to the more detailed description that is presented later.
The invention is realized by the following technical scheme:
the chemical components of the steel in percentage by weight are 0.25-0.45% of C, 1.50-2.20% of Si, 1.50-2.20% of Mn, 0.30-1.0% of Cr, 0.20-1.0% of Mo, 0.01-0.1% of Re, less than 0.01% of S, less than 0.01% of P and the balance of Fe.
A preparation method of ultrahigh-strength high-toughness wear-resistant steel comprises the following steps:
(1) smelting in an electric arc furnace or a medium frequency induction furnace, refining LF and VOD, and pouring into an ingot mould or a continuous casting crystallizer, wherein the tapping temperature is 1550 +/-20 ℃;
(2) rolling or forging the steel ingot or the continuous casting blank into a section or a forge piece, heating to 930 +/-20 ℃, keeping the temperature for 1.5-3 h, cooling to below 400 ℃ along with the furnace, discharging, and annealing;
(3) heating the machined part or forging to 940 +/-20 ℃, and carrying out heat preservation for 20min to 3 hours and then quenching;
(4) tempering the quenched high-strength wear-resistant steel at 150-450 ℃ for 2-10 h, and air-cooling the tempered high-strength wear-resistant steel after tempering to prepare the ultra-high-strength high-toughness wear-resistant steel, wherein the microstructure is a carbide-free bainite-martensite complex phase structure, the thickness of the lath of the steel is 10-50 nm, and the tensile strength of the steel is 10-50 nm
σb1800-2000 MPa, yield strength sigmas1300 to 1520MPa, elongation delta 16 to 18 percent and reduction of area
Impact toughness aku 60-80J/cm2Hardness HRC 55-62.
Compared with the prior art, the invention has the following beneficial effects:
in the prior art, the high-carbon (% C0.7-0.9) low-temperature bainite high-strength steel has poor welding performance, is easy to form brittle phase cementite, and has potential brittle danger. The present invention fully overcomes the deficiencies of the prior art. After forging, heat treatment is carried out to obtain a carbide-free bainite-martensite mixed structure with the thickness of 10-30 nm laths, the carbide-free bainite-martensite mixed structure has the product of strength and elongation of 33 GPa%, the tensile strength of 1800-2000 MPa, the elongation after fracture of 16.5-18%, the reduction of area of 38-42/%, and the impact toughness aku of 60-80J/cm2The hardness is HRC 55-62; especially, when the strength is 2000MPa, the elongation after fracture can still reach 18 percent.
In the invention, the steel has good weldability and forgeability, has outstanding plasticity, obvious elongation, impact toughness and hardness, and has wide application fields; meanwhile, the quenching and tempering process overcomes the defects of long isothermal transformation process time and low efficiency.
It is to be understood that both the foregoing general description and the following detailed description are exemplary and explanatory only and are not restrictive of the invention, as claimed.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
FIG. 1 is a structural view of a bainite-martensite lath structure in the present invention;
FIG. 2 is a schematic view of a heat treatment process in the present invention;
Detailed Description
The following description sufficiently illustrates specific embodiments of the invention to enable those skilled in the art to practice them.
FIG. 1 shows a structure diagram of a bainite-martensite lath structure in the present invention; FIG. 2 is a schematic view of the heat treatment process of the present invention.
On the basis of designing the components of the steel, isothermal and continuous transformation curves are measured, and the heat treatment process after forging is determined. After quenching and tempering heat treatment processes, the volume fractions of martensite, bainite and residual austenite are analyzed by an EBSD technology. The lath thicknesses of bainite, martensite and austenite were determined using high-resolution transmission electron microscopy. And the tensile property, the impact toughness and the hardness value of the sample after heat treatment are measured, and finally the heat treatment process is determined, so that the process is suitable for industrial production and overcomes the inoperability of the isothermal quenching process in the industrial production.
The high-strength high-toughness wear-resistant steel can be used as novel high-performance steel for heading machine tools (high tensile strength)
The degree is more than 2000MPa, the heat treatment hardness is more than 56HRC, and the impact toughness Aku is more than 20J), and the high-strength bolt can be manufactured, or the third-generation automobile high-strength steel (the product of strength and elongation is 20-40 GPa%) can be manufactured, so that the light weight and the safety of an automobile can be realized, and the high-strength track shoe can be forged, so that the light weight of an armor can be realized.
Example 1
The technique of the drill rod produced by the invention comprises the following steps: the chemical components comprise, by weight, 0.35% of C, 1.50% of Si, 1.50% of Mn, 0.80% of Cr0.20% of Mo and 0.01% of Re0S is less than 0.01 percent, P is less than 0.01 percent, and the balance is Fe; the manufacturing process comprises the following steps: smelting in a medium-frequency induction furnace, and LF refining; after refining, the steel is tapped at 1550 ℃ and poured into an ingot mold; removing the head of the steel ingot, forging and forming, and then annealing and machining; heating the part to 930 ℃, preserving heat for 3h, and then quenching in a quenching liquid at 20-40 ℃; after quenching, the steel is reheated to 320 ℃, and then air cooled after heat preservation for 5 hours. After the heat treatment, a carbide-free bainite-martensite mixed structure with a lath thickness of 14nm can be obtained, the tensile strength is 1950MPa, the elongation after fracture is 18 percent, and the impact toughness is 87.5J/cm2Hardness HRC 55.
Example 2
The technique of the cutter bar of the advanced development machine produced by the invention comprises the following steps: the chemical components comprise, by weight, 0.45% of C, 2.1% of Si, 1.95% of Mn, 0.40% of Cr, 0.20% of Mo, 0.02% of Re, less than 0.01% of S, less than 0.01% of P and the balance of Fe; the manufacturing process comprises the following steps: smelting in a medium-frequency induction furnace, and LF refining; after refining, the steel is discharged at the temperature of 1560 ℃ and poured into an ingot mould; forging the steel ingot into a bar, and forging the bar into a cutter bar; high-frequency induction heating to 920 ℃, keeping the temperature for 3 minutes, and then quenching; then heating to 350 ℃, preserving heat for 3 hours, and then cooling in air. After the heat treatment, a carbide-free bainite-martensite mixed structure with a lath thickness of 20nm, a tensile strength of 1960MPa and an impact toughness of 60J/cm can be obtained2Elongation after fracture 16.5%, hardness HRC 61.
Example 3
The process of the armored track shoe produced by the invention comprises the following steps: the chemical components comprise, by weight, 0.40% of C, 1.88% of Si, 1.50% of Mn1, 0.40% of Cr, 0.40% of Mo, 0.02% of Re, less than 0.01% of S, less than 0.01% of P and the balance of Fe; the manufacturing process comprises the following steps: smelting in a medium-frequency induction furnace, and LF refining; after refining, the steel is discharged at the temperature of 1560 ℃ and poured into an ingot mould; forging steel ingots into bars, and forging the bars into the armored track shoe at the initial forging temperature of 1200 ℃ and the final forging temperature of 920 ℃, and directly quenching; heating to 400 ℃, preserving heat for 3h, and then cooling in air. After the heat treatment, a carbide-free bainite-martensite mixed structure with a lath thickness of 30nm, a tensile strength of 1880MPa and an impact toughness of 68J/cm can be obtained2Elongation after fracture of 17% and hardness HRC 56.
It is to be understood that the present invention is not limited to the procedures and structures described above and shown in the drawings, and that various modifications and changes may be made without departing from the scope thereof. The scope of the invention is limited only by the appended claims.
Claims (1)
1. The ultrahigh-strength high-toughness wear-resistant steel is characterized by comprising the following chemical components, by weight, 0.25-0.45% of C, 1.50-2.10% of Si, 1.50-1.95% of Mn, 0.30-1.0% of Cr0, 0.20-1.0% of Mo0, 0.01-0.1% of Re0, less than 0.01% of S, less than 0.01% of P and the balance of Fe;
the preparation method of the ultrahigh-strength high-toughness wear-resistant steel comprises the following steps:
(1) smelting in an electric arc furnace or a medium frequency induction furnace, refining LF and VOD, and pouring into an ingot mould or a continuous casting crystallizer, wherein the tapping temperature is 1550 +/-20 ℃;
(2) rolling or forging the steel ingot or the continuous casting blank into a section or a forge piece, heating to 930 +/-20 ℃, keeping the temperature for 1.5-3 h, cooling to below 400 ℃ along with the furnace, discharging, and annealing;
(3) heating the machined part or forging to 940 +/-20 ℃, and carrying out heat preservation for 20min to 3 hours and then quenching;
(4) tempering the quenched high-strength wear-resistant steel at 150-450 ℃ for 2-10 h, and air-cooling the tempered high-strength wear-resistant steel after tempering to prepare the ultra-high-strength high-toughness wear-resistant steel, wherein the microstructure is a carbide-free bainite-martensite complex phase structure, the thickness of a lath of the steel is 10-50 nm, and the tensile strength sigma of the steel isb1800-2000 MPa, yield strength sigmas1300 to 1520MPa, elongation delta 16 to 18 percent and reduction of area
Impact toughness aku 60-80J/cm2Hardness HRC 55-62.
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| CN108977631A (en) * | 2018-08-17 | 2018-12-11 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | A kind of high-performance pick and its manufacturing method |
| CN109750231B (en) * | 2019-03-26 | 2020-02-21 | 湖南力神新材料科技有限公司 | Alloy steel and preparation method and application thereof |
| CN112522610B (en) * | 2020-11-18 | 2022-03-25 | 北京交通大学 | V-Ti composite bainite non-quenched and tempered steel structure and manufacturing method thereof |
| CN112458261A (en) * | 2020-11-24 | 2021-03-09 | 高博扬 | Preparation method of high-strength steel and high-strength steel |
| CN112662957B (en) * | 2020-12-09 | 2021-09-17 | 暨南大学 | Bainite wear-resistant cast steel with strong wear hardening capacity and preparation method and application thereof |
| CN112813362B (en) * | 2020-12-14 | 2023-03-28 | 内蒙古科技大学 | Manufacturing method of high-strength steel and high-strength steel track shoe |
| CN116265594A (en) * | 2021-12-17 | 2023-06-20 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | High-strength steel for high-performance cutting pick and heat treatment process thereof |
| CN115011867B (en) * | 2022-04-19 | 2023-04-14 | 清华大学 | High-strength-toughness wear-resistant steel lining plate and preparation method thereof |
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| JPH07173571A (en) * | 1993-12-16 | 1995-07-11 | Nippon Steel Corp | High workability wear resistant steel and production thereof |
| CN1477226A (en) * | 2003-08-01 | 2004-02-25 | 清华大学 | Medium-low carbon manganese system self-hardening bainite steel |
| JP2015147962A (en) * | 2014-02-05 | 2015-08-20 | 新日鐵住金株式会社 | Sleeve dog gear |
| CN106544591A (en) * | 2016-10-21 | 2017-03-29 | 燕山大学 | Ultrahigh-intensity high-toughness carbides-free bainite wear resistant steel plate and preparation method thereof |
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| CN103255341B (en) * | 2013-05-17 | 2015-07-22 | 宝山钢铁股份有限公司 | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof |
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|---|---|---|---|---|
| JPH07173571A (en) * | 1993-12-16 | 1995-07-11 | Nippon Steel Corp | High workability wear resistant steel and production thereof |
| CN1477226A (en) * | 2003-08-01 | 2004-02-25 | 清华大学 | Medium-low carbon manganese system self-hardening bainite steel |
| JP2015147962A (en) * | 2014-02-05 | 2015-08-20 | 新日鐵住金株式会社 | Sleeve dog gear |
| CN106544591A (en) * | 2016-10-21 | 2017-03-29 | 燕山大学 | Ultrahigh-intensity high-toughness carbides-free bainite wear resistant steel plate and preparation method thereof |
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