WO2014019353A1 - 一种超高强度高韧性耐磨钢板及其制造方法 - Google Patents

一种超高强度高韧性耐磨钢板及其制造方法 Download PDF

Info

Publication number
WO2014019353A1
WO2014019353A1 PCT/CN2013/071185 CN2013071185W WO2014019353A1 WO 2014019353 A1 WO2014019353 A1 WO 2014019353A1 CN 2013071185 W CN2013071185 W CN 2013071185W WO 2014019353 A1 WO2014019353 A1 WO 2014019353A1
Authority
WO
WIPO (PCT)
Prior art keywords
wear
resistant steel
steel plate
plate according
rolling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/CN2013/071185
Other languages
English (en)
French (fr)
Inventor
李红斌
姚连登
苗雨川
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Baoshan Iron and Steel Co Ltd
Original Assignee
Baoshan Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Priority to KR1020157005295A priority Critical patent/KR102128026B1/ko
Priority to AU2013299254A priority patent/AU2013299254B2/en
Priority to EP13826542.6A priority patent/EP2881487B1/en
Priority to JP2015524603A priority patent/JP6254160B2/ja
Priority to NZ630918A priority patent/NZ630918A/en
Priority to US14/418,417 priority patent/US9816165B2/en
Publication of WO2014019353A1 publication Critical patent/WO2014019353A1/zh
Priority to ZA2015/00275A priority patent/ZA201500275B/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • 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
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/22—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
    • C22C38/24—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
    • 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
    • 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

Definitions

  • the invention relates to wear-resistant steel, in particular to a low-alloy ultra-high strength and high-toughness wear-resistant steel plate and a manufacturing method thereof. Background technique
  • Wear-resistant steel plates are widely used in engineering products with high working strength, high wear resistance, engineering, antimony, agriculture, cement production, ports, electricity and metallurgy. Such as bulldozers, loaders, excavators, dump trucks and grabs, stackers and reclaimers, and feed bending structures.
  • wear-resistant steel In recent decades, the development and application of wear-resistant steel has developed rapidly. Generally, the carbon content is increased and appropriate trace elements such as chromium, molybdenum, nickel, vanadium, tungsten, cobalt, boron and titanium are added to make full use of precipitation strengthening. Different strengthening methods such as fine grain strengthening, phase transformation strengthening and dislocation strengthening improve the mechanical properties of wear-resistant steel. Most wear-resistant steels are medium-carbon, medium-high-carbon and high-carbon alloy steels. The increase in carbon content leads to a decrease in the toughness of the steel, and too high carbon seriously deteriorates the weldability of the steel. In addition, increasing the alloy content leads to an increase in cost and The welding performance is degraded, and these shortcomings restrict the further development of wear-resistant steel.
  • trace elements such as chromium, molybdenum, nickel, vanadium, tungsten, cobalt, boron and titanium are added to make full use of precipitation strengthening.
  • Different strengthening methods such as fine grain strengthening
  • the wear resistance of a material depends mainly on its hardness, and toughness also has a very important influence on the wear resistance of the material. Simply increasing the hardness of the material does not guarantee a better wear resistance and a longer service life under complex conditions.
  • the hardness and toughness of the low alloy wear-resistant steel are controlled to be reasonably matched, and excellent comprehensive mechanical properties are obtained to meet the needs of different wear conditions.
  • Welding can solve the connection of various steels. It is a very important processing technology and plays an important role in engineering applications. Cold cracking of welds is the most common defect in the welding process, especially when welding high-strength steels, the tendency of cold cracks to occur is large. In order to prevent the occurrence of cold cracks, it is usually pre-weld preheating and post-weld heat treatment, which causes the complexity of the welding process, the inoperability under special circumstances, and the safety and reliability of the welded structure. For high-strength, high-hardness wear-resistant steel plates, the welding problem is particularly noticeable.
  • CN1140205A discloses a medium carbon medium alloy wear-resistant steel whose carbon and alloying elements (Cr, Mo, etc.) content are much higher than the present invention, which inevitably leads to poor welding performance and mechanical processing performance.
  • CN1865481 A discloses a bainite wear-resistant steel which has alloying elements compared to the present invention. (Si, Mn, Cr, Mo, etc.) have a high content and low weldability and mechanical properties. Summary of the invention
  • the object of the present invention is to provide a low-alloy ultra-high strength and high-toughness wear-resistant steel plate, which achieves high strength, high hardness and high toughness matching on the basis of adding a small amount of alloying elements, has good mechanical processing performance, and is very beneficial to engineering. widely used.
  • the chemical composition weight percentage of the low alloy ultra high strength and high toughness wear resistant steel plate of the present invention is: C: 0.22-0.35%, Si: 0.10-0.40%, Mn: 0.60-1.35%, P: ⁇ 0.015 % , S : ⁇ 0.010% , Nb : 0.010-0.040% , Al: 0.010-0.080% , B : 0.0006-0.0014%, Ti: 0.005-0.050%, Ca: 0.0010-0.0080wt.%, V ⁇ 0.080%, Cr ⁇ 0.60%, W ⁇ 1.00wt.%, N ⁇ 0.0080%, 0 ⁇ 0.0060%, H ⁇ 0.0004%, and satisfy: 0.025% ⁇ Nb + Ti ⁇ 0.080%, 0.030% ⁇ Al+Ti ⁇ 0.12%, The balance is Fe and unavoidable impurities.
  • the microstructure of the steel wear-resistant steel of the present invention is mainly martensite and retained austenite, wherein the residual austenite volume fraction is 5%.
  • Another object of the present invention is to provide a method for producing the low alloy ultra high strength and high toughness wear resistant steel sheet, which comprises the steps of smelting, casting, heating, rolling, and direct cooling after rolling.
  • heating step heating to a temperature of 1000-1200 ° C
  • rolling step rolling temperature: 950-1150 ° C
  • finishing rolling temperature 800-950 ° C
  • direct cooling step after rolling ⁇ water cooling
  • Cooling temperature room temperature to 300 ° C.
  • the fineness and strengthening effect of the microalloying elements and the refinement and strengthening effect of controlling the cooling process of the rolling control make the steel sheet have excellent mechanical properties (strongness, hardness, elongation, Impact properties, etc.), weldability and wear resistance.
  • the chemical composition of the wear-resistant steel according to the present invention in addition to elements such as C, Si, Mn, etc., is added with a small amount of elements such as Nb, and has the characteristics of simple composition and low cost;
  • the wear-resistant steel plate of the present invention is produced by the TMCP process, and does not require heat treatment processes such as off-line quenching and tempering, and has the characteristics of short production process, high production efficiency, energy saving, and low production cost;
  • the wear-resistant steel plate of the present invention has high strength and high hardness, especially in terms of product performance. It has better low temperature toughness.
  • the wear-resistant steel of the present invention mainly has fine martensite and retained austenite, wherein the residual austenite volume fraction is 5%, which is beneficial to the hardness and toughness of the wear-resistant steel plate. Good match.
  • the wear-resistant steel plate of the invention has obvious advantages. Controlling the content of carbon and alloying elements, researching and developing low-cost, good mechanical properties and simple process wear-resistant steel is an inevitable trend in the development of the social economy and the steel industry. DRAWINGS
  • Figure 1 shows the shape and dimensions of the weld crack specimen of the oblique Y groove in the welding test.
  • Fig. 2 shows the microstructure of the steel sheet of Example 3, which is fine martensite and a small amount of retained austenite, which ensures that the steel sheet has better mechanical properties.
  • the steel species involved in the present invention achieves high strength, high hardness and high toughness matching on the basis of the addition of trace alloy elements through scientific design of element types and contents.
  • Carbon is the most basic and important element in wear-resistant steel. It can improve the strength and hardness of steel and improve the wear resistance of steel. However, it is unfavorable to the toughness and weldability of steel. Therefore, it should be controlled in steel.
  • the carbon content is 0.22-0.35%, preferably 0.23-0.33%
  • Silicon solid solution increases their hardness and strength in ferrite and austenite.
  • too high a silicon content leads to a sharp drop in the toughness of steel.
  • the affinity of silicon and oxygen is stronger than that of iron, it is easy to produce low-melting silicate during welding, increasing the fluidity of molten slag and molten metal, affecting the quality of the weld, so the content is not easy to be excessive, and the control silicon in the present invention is 0.10-0.40%, preferably 0.10-0.35%.
  • Manganese strongly increases the hardenability of steel and reduces the transition temperature of wear-resistant steel and the critical cooling rate of steel. However, when the manganese content is high, there is a tendency to coarsen the crystal grains, and the tempering and brittle sensitivity of the steel is increased, and segregation and cracking in the cast slab are easily caused, and the performance of the steel sheet is lowered, and the controlled manganese content in the present invention is 0.60. -1.35%, preferably 0.65 - 1.30%.
  • ⁇ The refined grain and precipitation strengthening effect of Nb is extremely significant for improving the toughness and toughness of the material. It is a strong, N-forming element that strongly inhibits austenite grain growth.
  • Nb improves the strength and toughness of steel through grain refinement. Nb mainly improves and improves the properties of steel through precipitation strengthening and phase transformation strengthening. Nb has been used as one of the most effective strengthening agents in HSLA steel.
  • the enthalpy is 0.010-0.040%, preferably 0.010-0.035%.
  • Nitrogen in aluminum and steel forms fine, insoluble A1N particles that refine the grain of steel.
  • Aluminum can refine the grain of steel, fix nitrogen and oxygen in steel, reduce the sensitivity of steel to the notch, reduce or eliminate the aging phenomenon of steel, and improve the toughness of steel.
  • the A1 content is controlled at 0.010-0.080. %, preferably from 0.010 to 0.060%.
  • the boron content is controlled to be 0.0006-0.0014%, preferably It is 0.0008-0.0014%.
  • Titanium is one of the strong carbide forming elements and forms fine TiC particles with carbon.
  • the TiC particles are fine and distributed at the grain boundaries to achieve the effect of refining the crystal grains, and the hard TiC particles improve the wear resistance of the steel.
  • the controlled titanium is 0.005-0.050%, preferably 0.010-0.045%.
  • niobium and titanium can obtain better grain refining effect, reduce the original austenite grain size, and facilitate the refinement of the martensite strip after quenching, improve the strength and wear resistance, TiN, etc.
  • the undissolved at high temperature can prevent the coarsening of grains in the heat-affected zone, improve the toughness of the heat-affected zone, and improve the weldability of the steel. Therefore, the content of niobium and titanium is as follows: 0.025% ⁇ Nb+Ti ⁇ 0.080% , preferably 0.035% ⁇ Nb + Ti ⁇ 0.070%.
  • Titanium can form fine particles and refine grains. Aluminum can ensure the formation of fine titanium particles and fully exert the grain refinement effect of titanium. Therefore, the contents of aluminum and titanium are as follows: 0.030% A1+Ti 0.12%, preferably 0.040% ⁇ A1+Ti ⁇ 0.11% 0
  • Calcium has a significant effect on the deterioration of inclusions in cast steel.
  • the addition of appropriate amount of calcium in the cast steel can transform the long strip of sulfide inclusions in the cast steel into spherical CaS or (Ca, Mn) S inclusions, which are formed by calcium.
  • the oxide and sulfide inclusions have a low density and are easy to remove.
  • Calcium also significantly reduces the segregation of sulfur at the grain boundaries, which are beneficial for improving the quality of the cast steel and thereby improving the properties of the steel.
  • Calcium is added when the inclusions are large, which is beneficial to ensure the mechanical properties of the steel, especially toughness.
  • the controlled calcium in the present invention is from 0.0010 to 0.0080%, preferably from 0.0010 to 0.0060%.
  • Vanadium The addition of vanadium is mainly to refine the grains, so that the austenite grains do not grow too coarse during the heating stage, so that in the subsequent multi-pass rolling process, the steel crystals can be made. The granules are further refined to increase the strength and toughness of the steel.
  • the vanadium is controlled to be 0.080%, preferably 0.035 to 0.080%, and more preferably 0.060%.
  • Chromium can reduce the critical cooling rate and increase the hardenability of steel. Chromium can form in steel
  • Chromium can prevent or slow the precipitation and aggregation of carbides during tempering, and can improve the tempering stability of steel.
  • the controlled chromium content is 0.60%, preferably 0.20-0.60%, and more preferably 0.40%.
  • Tungsten can increase the tempering stability and thermal strength of steel, and can play a role in refining crystal. Further, tungsten may form a hard carbide to increase the wear resistance of the steel, and in the present invention, the tungsten content is controlled to be 1.00%, preferably 0.30 to 1.00%, and more preferably 0.80%.
  • Phosphorus and sulfur In wear-resistant steel, sulfur and phosphorus are harmful elements, and their content should be strictly controlled.
  • the controlled phosphorus content in the steels involved in the present invention is 0.015%, preferably 0.010%;
  • Nitrogen, oxygen and hydrogen Excessive oxygen and nitrogen in steel can be very detrimental to the properties of steel, especially weldability and toughness, but excessive control can greatly increase production costs. Therefore, control of steels involved in the present invention
  • the nitrogen content is 0.0080%, preferably 0.0050%; the oxygen content is 0.0060%, preferably
  • the method for manufacturing the above-mentioned low-alloy ultra-high strength and high-toughness wear-resistant steel sheet of the present invention comprises the steps of smelting, casting, heating, rolling, and direct cooling after rolling.
  • heating step heating to a temperature of 1000-1200 ° C; in the rolling step, rolling temperature: 950-1150 ° C, finishing rolling temperature: 800-950 ° C; in the cooling step, ⁇ water cooling, stop cooling Temperature: from room temperature to 300 °C.
  • the heating temperature is 1000-1150 ° C, more preferably the heating temperature is 1000-1130 ° C, in order to ensure sufficient diffusion of carbon and alloy elements, anti-austenite grains excessively grow and billet The surface is heavily oxidized, and the most preferred heating temperature is 1050-1130 °C.
  • the rolling temperature is: 950-1100 ° C
  • the finishing rolling temperature is 800-900 ° C
  • the rolling temperature is 950-1080 ° C
  • the finishing rolling temperature is 810-900 ° C, most preferably , rolling temperature:
  • the shutdown temperature is from room temperature to 280 ° C, more preferably the shutdown temperature is from room temperature to 250 ° C, and most preferably the shutdown temperature is from room temperature to 200 ° C.
  • the invention strictly controls the content of carbon and microalloy by rationally designing chemical components (contents and ratios of elements such as C, Si, Mn, Nb).
  • the wear-resistant steel plate obtained by such a component has weldability and is suitable for use in a mechanical field requiring welding.
  • the wear-resistant steel sheet of the invention has high strength, high hardness, good impact toughness, etc., and is easy to be machined by cutting, bending, etc., and has strong applicability.
  • the low alloy ultra high strength and high toughness wear-resistant steel plate produced by the invention has the tensile strength: 1400-1700 MPa, the elongation: 13-14%; the Brinell hardness: 470-570HBW; preferably, the -40 °C Charpy V type Longitudinal impact work: 50-80J, with good welding performance and excellent mechanical properties, enhances the applicability of wear-resistant steel.
  • the smelting raw materials are produced according to the steps: smelting, casting, heating, rolling, and direct cooling after rolling.
  • Test Example 1 Mechanical properties test
  • the hardness of the low-alloy super high-strength and high-strength wear-resistant steel plate of the embodiment 1-7 of the present invention is measured; the impact test is carried out according to the GB/T229 test method; /T228 test method for tensile test; bending test according to GB/T232 test method; the results are shown in Table 3.
  • the tensile strength of the steel sheet of Example 1-7 of the present invention 1400-1700 MPa, elongation: 13%-14%, Brinell hardness: 470-570HBW, -40 °C Charpy V-shaped longitudinal Impact energy: 50-80J, It is explained that the steel sheet according to the present invention has high strength, high hardness, good elongation, and the like, and has excellent low-temperature impact toughness. The strength, hardness and elongation of the steel sheet according to the invention are obviously superior to the comparative example 1 .
  • Fig. 2 shows the microstructure of the steel sheet of Example 3, which is fine martensite and a small amount of retained austenite, which ensures that the steel sheet has better mechanical properties.
  • Test Example 2 Weldability test
  • the invention is wear-resistant
  • the steel plate was subjected to the oblique Y-groove welding crack test, and the test was carried out in five groups.
  • the shape and dimensions of the weld crack test piece of the bevel groove are shown in Fig. 1.
  • the welding constrained weld is welded, and the weld is welded with Ar gas-enhanced welding.
  • the JM-58 welding wire of ⁇ 1.2 is used, and the angular deformation of the test piece is strictly controlled during the welding process.
  • the weld of the test weld was carried out after cooling the room temperature after welding.
  • the test welds were welded at room temperature and the weld surface cracks, section cracks and root cracks were examined after 48 hours of test weld completion. After the anatomical test, the surface, section and root of the weld were inspected by the coloring method.
  • the welding specification is 170A x 25V x 160mm/minfact
  • the abrasion resistance test was carried out on an ML-100 abrasive wear tester.
  • the axis of the sample is perpendicular to the surface of the steel plate, and the wear surface of the sample is the rolling surface of the steel plate.
  • the sample is processed into a stepped cylinder as required, and the test part has a size of C>4 mm, and the clamping part of the fixture has a size of C>5 mm.
  • the sample was washed with alcohol before the test, then blown dry with a hair dryer, weighed on a balance of one thousandth of a precision, and the weight of the sample was measured as the original weight, and then mounted on a flexible jig.
  • the test was carried out under a load of 42 N using a sandpaper having a particle size of 80 mesh. After the test, due to the wear between the sample and the sandpaper, the sample draws a spiral on the sandpaper, and calculates the length of the spiral according to the starting and ending radius of the spiral.
  • the calculation formula is
  • the chemical composition of the wear-resistant steel according to the present invention has a small amount of Nb and the like added in addition to elements such as C, Si, Mn, etc., and has the characteristics of simple composition, low cost, etc.
  • the invention is produced by the TMCP process without off-line quenching and tempering.
  • the heat treatment process has the characteristics of short production process, high production efficiency, energy saving, and low production cost.
  • the wear resistant steel sheet of the invention has high strength, high hardness and especially good low temperature toughness.
  • the wear-resistant steel of the present invention has a microstructure mainly composed of fine martensite and retained austenite, wherein the retained austenite volume fraction is 5%, tensile strength: 1400-1700 MPa, elongation: 13%-14%, Brinell hardness: 470-570HBW, -40°C Charpy V-type longitudinal impact energy: 50-80J, which is good for the good matching of the hardness and toughness of the wear-resistant steel plate. Therefore, the wear-resistant steel plate of the invention has obvious advantages. .

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

一种耐磨钢板，其化学成分（重量％）为：C：0.22-0.35%、Si：0.10-0.40%、Mn：0.60-1.35%、Ρ≤0.015%、S≤0.010%、Nb：0.010-0.040%、Al：0.010-0.080%、B：0.0006-0.0014%、Ti：0.005-0.050%、Ca：0.0010-0.0080wt.%、V≤0.080%、Cr≤0.60%、W≤1.00wt.%，N≤0.0080%、O≤0.0060%、H≤０.0004%，且满足：0.025%≤Nb+Ti≤0.080%，0.030%≤A1+Ti≤0.12%，余量为Fe和不可避免的杂质。该耐磨钢板的制造方法，包括冶炼、铸造、轧制及轧后直接冷却等步骤。通过以上成分及方法得到的耐磨钢板强硬度高，低温韧性佳，机械加工性能优异，适用于工程、矿山机械中易磨损设备，如抓斗、刮板运输机等。

Description

一种超高强度高韧性耐磨钢板及其制造方法 技术领域
本发明涉及耐磨钢，特别是涉及一种低合金超高强度高韧性耐磨钢板 及其制造方法。 背景技术
耐磨钢板广泛应用于工作条件特别恶劣， 要求高强度， 高耐磨性能的 工程、 釆矿、 农业、 水泥生产、 港口、 电力以及冶金等机械产品上。 如推 土机， 装载机， 挖掘机， 自卸车及抓斗、 堆取料机、 输料弯曲结构等。
近几十年来， 耐磨钢的开发与应用发展很快， 一般增加碳含量并加入 适量的微量元素， 如铬、 钼、 镍、 钒、 钨、 钴、 硼和钛等， 充分利用析出 强化、 细晶强化、 相变强化和位错强化等不同强化方式提高耐磨钢的力学 性能。 大多数耐磨钢为中碳、 中高碳和高碳合金钢， 碳含量增加会导致钢 的韧性下降， 且过高的碳严重恶化了钢的焊接性能， 另外， 增加合金含量 会导致成本提高和焊接性能下降， 这些缺点制约了耐磨钢的进一步发展。
材料的耐磨性主要取决于其硬度， 而韧性对材料的耐磨性也有着非常 重要的影响。 单单提高材料的硬度并不能保证材料在复杂工况下具有较佳 的耐磨性和较长的使用寿命。 通过调整成分与热处理工艺， 控制低合金耐 磨钢硬度和韧性的合理匹配， 得到优良的综合机械性能， 使其满足不同磨 损工况的需要。
焊接可以解决各种钢材的连接， 是十分重要的加工工艺， 在工程应用 中具有十分重要的作用。 焊接冷裂纹是最常出现的焊接工艺缺陷， 尤其是 当焊接高强度钢时， 冷裂纹出现的倾向很大。 为防止冷裂纹产生， 通常是 焊前预热、 焊后热处理， 造成了焊接工艺的复杂性， 特殊情况下的不可操 作性， 危及焊接结构的安全可靠性。 对于高强度、 高硬度的耐磨钢板， 焊 接问题尤为明显。
CN1140205A公开了一种中碳中合金耐磨钢， 其碳及合金元素 （ Cr、 Mo等）含量均远高于本发明， 这必然导致焊接性能与机械加工性能较差。
CN1865481 A公开了一种贝氏体耐磨钢， 与本发明相比， 其合金元素 ( Si、 Mn、 Cr、 Mo等）含量较高， 焊接性能、 力学性能较低。 发明内容
本发明的目的是提供一种低合金超高强高韧耐磨钢板，在添加微量合 金元素基础上实现高强度、 高硬度和高韧性的匹配， 具有良好的机械加工 性能， 十分有益于工程上的广泛应用。
为实现上述目的， 本发明的低合金超高强高韧耐磨钢板的化学成分重 量百分比含量为： C: 0.22-0.35%, Si: 0.10-0.40%, Mn: 0.60-1.35%、 P: < 0.015% , S : < 0.010% , Nb : 0.010-0.040% , Al: 0.010-0.080% , B : 0.0006-0.0014%, Ti: 0.005-0.050%, Ca: 0.0010-0.0080wt.%, V < 0.080%, Cr < 0.60%, W < 1.00wt.%, N < 0.0080%, 0 < 0.0060%, H < 0.0004%, 且 满足： 0.025% < Nb+Ti < 0.080%, 0.030% < Al+Ti < 0.12%, 余量为 Fe和 不可避免的杂质。
本发明钢耐磨钢显微组织主要为马氏体和残余奥氏体， 其中残余奥氏 体体积分数 5%。
本发明的另一个目的在于提供该低合金超高强高韧耐磨钢板的制造 方法， 该方法依次包括冶炼、 铸造、 加热、 轧制和轧后直接冷却等步骤。 其中加热步骤中， 加热到温度为 1000-1200°C ; 轧制步骤中， 开轧温度： 950-1150°C , 终轧温度： 800-950°C ; 轧后直接冷却步骤中， 釆用水冷， 停 冷温度： 室温至 300°C。
由于本发明中科学设计了碳及合金元素含量， 通过微合金元素的细化 强化作用及控制轧制控制冷却过程的细化强化效果， 使得钢板具有优异的 力学性能 （强、 硬度、 延伸率、 冲击性能等） 、 焊接性能和耐磨性能。
本发明与现有技术的不同之处主要体现在以下几方面：
从化学成分上看， 本发明涉及的耐磨钢的化学成分除 C、 Si、 Mn等 元素外， 添加了少量 Nb等元素， 具有成分简单、 成本低廉等特点；
从生产工艺上看， 本发明涉及的耐磨钢板釆用 TMCP工艺生产， 无需 离线淬火和回火等热处理工序， 具有生产流程短， 生产效率高， 节约能源， 降低生产成本等特点；
从产品性能上看， 本发明涉及的耐磨钢板具有高强度、 高硬度尤其具 有较佳的低温韧性。
从显微组织上看， 本发明涉及的耐磨钢， 显微组织主要为细的马氏体 和残余奥氏体，其中残余奥氏体体积分数 5% ,有益于耐磨钢板强硬度及 韧性的良好匹配。
本发明涉及的耐磨钢板具有较明显的优势。 控制碳和合金元素含量， 研发低成本、 力学性能佳、 工艺简单的耐磨钢是社会经济和钢铁工业发展 的必然趋势。 附图说明
图 1是焊接试验中， 斜 Y坡口焊接裂纹试件的形状和尺寸。
图 2为实施例 3钢板显 组织， 为细的马氏体和少量残余奥氏体， 这 保证了钢板具有较佳的力学性能。 具体实施方式
以下结合实施例详述本发明所涉及的低合金超高强高韧耐磨钢板的 特点。
本发明所涉及的钢种通过元素种类及含量的科学设计， 在添加微量合 金元素基础上实现了高强度、 高硬度和高韧性的匹配。
碳： 碳是耐磨钢中最基本、 最重要的元素， 可以提高钢的强度和硬度， 进而提高钢的耐磨性， 但其对钢的韧性和焊接性能不利， 因此， 应合理控 制钢中的碳含量为 0.22-0.35% , 优选为 0.23-0.33 %„
硅： 硅固溶在铁素体和奥氏体中提高它们的硬度和强度， 然而硅含量 过高会导致钢的韧性急剧下降。 同时考虑到硅与氧的亲和力比铁强， 焊接 时容易产生低熔点的硅酸盐， 增加熔渣和熔化金属的流动性， 影响焊缝质 量， 因此含量不易过多， 本发明中控制硅为 0.10-0.40% , 优选地为 0.10-0.35%。
锰： 锰强烈增加钢的淬透性， 降低耐磨钢转变温度和钢的临界冷却速 度。 但锰含量较高时， 有使晶粒粗化的倾向， 并增加钢的回火脆敏感性， 而且容易导致铸坯中出现偏析和裂纹， 降低钢板的性能， 本发明中控制锰 含量为 0.60-1.35% , 优选地 0.65- 1.30%。 铌： Nb 的细化晶粒和析出强化作用， 对提高材料强韧性贡献是极为 显著的， 是强烈的 、 N化物的形成元素， 强烈地抑制奥氏体晶粒长大。 Nb通过晶粒细化同时提高钢的强度和韧性， Nb主要通过析出强化和相变 强化来改善和提高钢的性能， Nb 已经被作为 HSLA钢中最有效的强化剂 之一， 本发明中控制铌为 0.010-0.040%, 优选地为 0.010-0.035%。
铝： 铝和钢中氮能形成细小难溶的 A1N颗粒， 细化钢的晶粒。 铝可细 化钢的晶粒， 固定钢中的氮和氧， 减轻钢对缺口的敏感性， 减小或消除钢 的时效现象， 并提高钢的韧性， 本发明中 A1含量控制在 0.010-0.080%, 优选地为 0.010-0.060%。
硼： 硼增加钢的淬透性但含量过高将导致热脆现象， 影响钢的焊接 性能及热加工性能， 因此需要严格控制 B 含量， 本发明中控制硼含量为 0.0006-0.0014%, 优选地为 0.0008-0.0014%。
钛： 钛是强碳化物形成元素之一， 与碳形成细微的 TiC颗粒。 TiC颗 粒细小， 分布在晶界， 达到细化晶粒的效果， 较硬的 TiC颗粒提高钢的耐 磨性， 本发明中控制钛为 0.005-0.050%, 优选地为 0.010-0.045%。
铌和钛的复合加入， 可以获得更好的晶粒细化效果， 减小原奥氏体晶 粒尺寸， 有利于细化淬火后的马氏体条， 提高强度和耐磨性， TiN等在高 温下的未溶解性， 可阻止热影响区晶粒的粗化， 提高热影响区的韧性， 从 而改善钢的焊接性，故铌和钛的含量范围如下： 0.025% < Nb+Ti < 0.080% , 优选地为 0.035% < Nb+Ti < 0.070%。
钛均能形成细小颗粒进而细化晶粒， 铝可以保证细小钛颗粒的形成， 充分发挥钛的细化晶粒作用， 故铝和钛的含量范围如下： 0.030% A1+Ti 0.12%, 优选地为 0.040% < A1+Ti < 0.11%0
钙： 钙对铸钢中夹杂物的变质具有显著作用， 铸钢中加入适量钙可将 铸钢中的长条状硫化物夹杂转变为球状的 CaS或 （Ca, Mn ) S夹杂， 钙 所形成的氧化物及硫化物夹杂密度小， 易于上浮排除。 钙还显著降低硫在 晶界的偏聚， 这些都有益于提高铸钢的质量， 进而提高钢的性能。 钙在夹 杂物较多时添加效果明显， 有利于保证钢的力学性能， 尤其韧性。 本发明 中控制钙为 0.0010-0.0080%, 优选地为 0.0010-0.0060%。
钒： 钒的加入主要是为了细化晶粒， 使钢坯在加热阶段奥氏体晶粒不 至于生长的过于粗大， 这样， 在随后的多道次轧制过程中， 可以使钢的晶 粒得到进一步细化， 提高钢的强度和韧性， 本发明中控制钒为 0.080 %, 优选地为 0.035-0.080%, 还优选地为 0.060 %。
铬： 铬可以降低临界冷却速度、 提高钢的淬透性。 铬在钢中可以形成
(Fe,Cr)3C、 （Fe,Cr)7C3和 (Fe,Cr)23C7等多种碳化物， 提高强度和硬度。 铬在 回火时能阻止或减緩碳化物的析出与聚集， 可以提高钢的回火稳定性， 本 发明中控制铬含量为 0.60%, 优选地为 0.20-0.60%, 还优选为 0.40%。
钨： 钨可以增加钢的回火稳定性和热强性， 并可以起到一定的细化晶 粒作用。 另外， 钨可以形成硬质碳化物而增加钢的耐磨性， 本发明中控制 钨含量为 1.00%, 优选地为 0.30-1.00%, 还优选为 0.80%。
磷与硫： 在耐磨钢中，硫与磷均为有害元素， 它们的含量要严格控制， 本发明所涉及钢种中控制磷含量 0.015% , 优选 0.010% ; 硫含量
0.010%, 优选 0.005%。
氮、 氧与氢： 钢中过多的氧和氮对钢的性能尤其是焊接性和韧性能是 十分不利的， 但控制过严会大幅增加生产成本， 因此， 本发明所涉及钢种 中控制氮含量 0.0080%, 优选 0.0050%; 氧含量 0.0060%, 优选
0.0040%; 氢含量 0.0004%, 优选 0.0003%。
本发明的上述低合金超高强高韧耐磨钢板的制造方法， 依次包括冶 炼、 铸造、 加热、 轧制和轧后直接冷却等步骤。 其中加热步骤中， 加热到 温度为 1000-1200 °C ; 轧制步骤中， 开轧温度： 950-1150 °C , 终轧温度： 800-950°C ; 冷却步骤中， 釆用水冷， 停冷温度： 室温至 300°C。
优选地， 在所述加热过程中， 加热温度为 1000-1150°C , 更优选加热 温度为 1000-1130°C , 为保证碳及合金元素充分扩散， 防奥氏体晶粒过分 长大及钢坯表面严重氧化， 最优选加热温度为 1050-1130°C。
优选地， 开轧温度： 950-1100 °C , 终轧温度： 800-900 °C , 更优选地， 开轧温度： 950-1080 °C , 终轧温度： 810-900 °C , 最优选地， 开轧温度：
980-1080°C , 终轧温度： 810-890°C。
优选地， 停冷温度为室温至 280°C , 更优选停冷温度为室温至 250°C , 最优选停冷温度为室温至 200 °C。
本发明通过合理设计化学成分（ C、 Si、 Mn、 Nb等元素的含量及配比；)， 严格控制了碳和微合金含量。 这样的成分设计得到的耐磨钢板具有易焊 性， 适合需要焊接的机械领域使用。 另外， 由于不含有 Mo和 Ni等元素， 可大幅降低耐磨钢生产成本。
本发明的耐磨钢板具有高强度、 高硬度及较佳的冲击韧性等， 易进行 切割、 弯曲等机械加工， 具有很强的适用性。
本发明生产的低合金超高强高韧耐磨钢板：抗拉强度： 1400-1700MPa, 延伸率： 13-14%; 布氏硬度： 470-570HBW; 优选地， 其 -40°C夏比 V 型 纵向冲击功： 50-80J, 具有良好的焊接性能和优异的力学性能， 增强了耐 磨钢的适用性。 实施例
本发明的实施例 1-7和对比例 1 (专利 CN1865481A ) 的钢板化学元 素质量百分配比如表 1所示。
将冶炼原料按照步骤： 冶炼→铸造→加热→轧制→轧后直接冷却进行 制造。
表 1 本发明实施例 1-7及对比例 1的化学成分（wt.% )
C Si Mn P s Nb Al B Ti Ca V Cr W N 0 H 其他 实施例 1 0.22 0.25 1.35 0.009 0.005 0.027 0.020 0.0013 0.010 0.0030 0.060 0.23 0.32 0.0038 0.0040 0.0003 - 实施例 2 0.23 0.40 1.30 0.015 0.004 0.040 0.051 0.0012 0.005 0.0060 0.080 1 1.00 0.0080 0.0025 0.0004 - 实施例 3 0.25 0.35 1.05 0.010 0.010 0.035 0.038 0.0008 0.045 0.0010 0.038 0.60 0.80 0.0037 0.0021 0.0002 - 实施例 4 0.28 0.23 0.93 0.008 0.003 0.010 0.080 0.0006 0.040 0.0050 1 0.40 1 0.0025 0.0060 0.0002 - 实施例 5 0.30 0.28 0.88 0.009 0.003 0.020 0.060 0.0014 0.050 0.0080 1 1 1 0.0050 0.0027 0.0003 - 实施例 6 0.33 0.10 0.65 0.008 0.002 0.018 0.010 0.0013 0.030 0.0030 0.051 0.27 0.50 0.0033 0.0033 0.0002 - 实施例 7 0.35 0.22 0.60 0.009 0.003 0.021 0.045 0.0012 0.027 0.0020 0.035 0.38 0.46 0.0029 0.0029 0.0002 -
Mo: 对比例 1 0.40 1.12 2.26 < 0.04 < 0.03 - - - - - 1.0 - - -
表 2本发明实施例 1-7中的具体工艺参数
Figure imgf000010_0001
试验例 1 : 力学性能试验
按照 GB/T2975取样方法取样， 并按照 GB/T231.1试验方法对本发明 实施例 1-7的低合金超高强高韧耐磨钢板进行硬度测定；按照 GB/T229试 验方法进行冲击试验； 按照 GB/T228 试验方法进行拉伸试验； 按照 GB/T232试验方法进行弯曲试验； 其结果见表 3。
表 3 本发明实施例 1-7及对比例 1的力学性能
Figure imgf000011_0001
从表 3可以看出，本发明实施例 1-7的钢板抗拉强度： 1400-1700MPa, 延伸率： 13%-14%, 布氏硬度： 470-570HBW, -40°C夏比 V型纵向冲击功： 50-80J, 以上说明本发明所涉及钢板不但具有高强度、 高硬度、 延伸率佳 等特点， 而且具有优异的低温冲击韧性。 本发明所涉及钢板强、 硬度、 延 伸率均明显优于比对比例 1。
图 2为实施例 3钢板显 组织， 为细的马氏体和少量残余奥氏体， 这 保证了钢板具有较佳的力学性能。
其他实施例也能得到类似的显微组织。 试验例 2 ： 焊接性试验
按照 《斜 Y坡口焊接裂纹试验方法》 （GB4675.1-84 )对本发明耐磨 钢板进行斜 Y坡口焊接裂纹试验， 分五组进行试验。 斜 Υ坡口焊接裂纹 试件的形状和尺寸见图 1。
首先焊接拘束焊缝， 拘束焊缝釆用富 Ar气体保护焊焊接， 使用 Φ 1.2 的 JM-58焊丝， 焊接过程中严格控制了试件的角变形。 焊后冷却室温后进 行试验焊缝的焊接。 试验焊缝在室温下进行焊接， 试验焊缝完成 48小时 后， 检测焊缝表面裂纹、 断面裂纹和根部裂纹。 经过解剖试验， 利用着色 法对焊缝的表面、 断面、 根部分别进行检查。 焊接规范为 170A x 25V x 160mm/min„
对本发明实施例 1-7 的低合金超高强高韧耐磨钢板进行焊接性能试 验， 试验结果如表 4所示。
表 4 本发明实施例 1-7的焊接性能试验结果
Figure imgf000012_0001
5 0 0 0
实 1 0 0 0
施 2 0 0 0
例 137 3 0 0 0 35 °C 66%
5 4 0 0 0
5 0 0 0
实 1 0 0 0
施 2 0 0 0
例 153 3 0 0 0 29 °C 63%
6 4 0 0 0
5 0 0 0
实 1 0 0 0
施 2 0 0 0
例 175 3 0 0 0 33 °C 65%
7 4 0 0 0
5 0 0 0
由表 4可知， 本发明实施例 1-7的耐磨钢板在一定预热条件下焊接后 均未出现裂纹， 说明本发明耐磨钢板具有较好的焊接性能。 试验例 3 : 耐磨性试验
耐磨性试验在 ML-100磨粒磨损试验机上进行。 截取试样时， 令试样 的轴线垂直于钢板表面， 试样的磨损面即钢板的轧制面。 将试样按要求加 工成台阶状圓柱体，测试部分尺寸为 C>4mm,卡具夹持部分尺寸为 C> 5mm。 试验前用酒精清洗试样， 然后用吹风机吹干， 在万分之一精度的天平上称 重， 测得试样重量作为原始重量， 而后安装在弹性夹具上。 用粒度为 80 目的砂纸 ,在 42N载荷作用下进行试验。试验后由于试样与砂纸间的磨损 , 试样在砂纸上画出一条螺旋线， 根据螺旋线的起始和终止半径来计算螺旋 线的长度， 计算公式为
_ π (τλ 2 - r2 2 ) rl为螺旋线的起始半径， r2为螺旋线的终止半径， a为螺旋线的进给 量。 每次实验称重三次取平均值， 然后计算失重， 用每米失重来表示试样 的磨损率 （mg/M ) 。
对本发明的实施例 1-7 的低合金超高强高韧耐磨钢板进行耐磨性试 验。 本发明的实施例钢种与对比例 2钢 （对比例 2钢板硬度为 450HBW ) 的磨损试验结果见表 5。 表 5 本发明实施例 1-7与对比例 2的磨损试验结果
Figure imgf000014_0001
从表 5可知， 在此磨损条件下， 本发明的低合金超高强高韧耐磨钢板 的耐磨性能优于对比例 2钢板耐磨性。
本发明涉及的耐磨钢的化学成分除 C、 Si、 Mn 等元素外， 添加了少 量 Nb等元素， 具有成分简单、 成本低廉等特点； 本发明釆用 TMCP工艺 生产， 无需离线淬火和回火等热处理工序， 具有生产流程短， 生产效率高， 节约能源， 降低生产成本等特点； 本发明的耐磨钢板具有高强度、 高硬度 尤其具有较佳的低温韧性。 本发明的耐磨钢， 显微组织主要为细的马氏体 和残余奥氏体，其中残余奥氏体体积分数 5%,抗拉强度： 1400-1700MPa, 延伸率： 13%-14%, 布氏硬度： 470-570HBW, -40°C夏比 V型纵向冲击功： 50-80J, 有益于耐磨钢板强硬度及韧性的良好匹配， 因此， 本发明的耐磨 钢板具有较明显的优势。

Claims

权利要求书
1. 一种耐磨钢板， 其重量百分比组成为： C : 0.22-0.35%、 Si : 0.10-0.40%, Mn: 0.60-1.35%、 P < 0.015%, S < 0.010%, Nb: 0.010-0.040%, Al： 0.010-0.080% 、 B： 0.0006-0.0014% 、 Ti： 0.005-0.050% 、 Ca： 0.0010-0.0080%, V < 0.080%, Cr < 0.60%, W < 1.00%, N < 0.0080%, O < 0.0060%, H < 0.0004%, 且满足： 0.025% < Nb+Ti < 0.080%, 0.030% < Al+Ti < 0.12%, 余量为 Fe和不可避免的杂质。
2. 如权利要求 1所述的耐磨钢板， 其特征在于， C: 0.23-0.33%。
3. 如权利要求 1或 2所述的耐磨钢板， 其特征在于， Si: 0.10-0.35%。
4.如权利要求 1-3任一所述的耐磨钢板，其特征在于， Mn: 0.65-1.30%。
5. 如权利要求 1-4任一所述的耐磨钢板， 其特征在于， P 0.010%。
6. 如权利要求 1-5任一所述的耐磨钢板， 其特征在于， S 0.005%。
7. 如权利要求 1-6 任一所述的耐磨钢板， 其特征在于， Nb : 0.010-0.035%。
8. 如权利要求 1-7 任一所述的耐磨钢板， 其特征在于， A1 :
0.020-0.060%。
9. 如权利要求 1-8 任一所述的耐磨钢板， 其特征在于， B : 0.0008-0.0014%。
10. 如权利要求 1-9 任一所述的耐磨钢板， 其特征在于， Ti : 0.010-0.045%。
11 . 如权利要求 1-10 任一所述的耐磨钢板， 其特征在于， Ca: 0.0010-0.0060%。
12. 如权利要求 1-11任一所述的耐磨钢板，其特征在于， V 0.060%。
13. 如权利要求 1-12任一所述的耐磨钢板，其特征在于， Cr 0.40%。
14. 如权利要求 1-13 任一所述的耐磨钢板， 其特征在于， W
0.80wt.%。
15.如权利要求 1-14任一所述的耐磨钢板，其特征在于，N 0.0050%。
16.如权利要求 1-15任一所述的耐磨钢板，其特征在于， 0 0.0040%。
17. 如权利要求 1-16任一所述的耐磨钢板，其特征在于，H 0.0003%。
18. 如权利要求 1-17任一所述的耐磨钢板， 其特征在于， 0.035% Nb+Ti < 0.070%, 0.040% < Al+Ti 0.11%。
19. 如权利要求 1-18任一所述的耐磨钢板， 其特征在于， 抗拉强度为 1400-1700MPa, 延伸率为 13-14%; 布氏硬度为 470-570HBW; 其 -40°C夏 比 V型纵向冲击功为 50-80J 。
20.权利要求 1-19任一所述的耐磨钢板的制造方法，依次包括： 冶炼、 铸造、 加热、 轧制和轧后直接冷却等步骤；
在加热步骤中， 加热温度为 1000-1200°C , 保温时间为 1-2小时； 在轧制步骤中， 开轧温度为 950-1150 °C , 终轧温度为 800-950 °C ; 在轧后直接冷却步骤中， 釆用水冷， 停冷温度为室温至 300°C。
21. 如权利要求 20 所述的耐磨钢板的制造方法， 其特征在于， 保温 时间为 2小时。
22. 如权利要求 20或 21所述的耐磨钢板的制造方法， 其特征在于， 板坯加热温度为 1000-1150°C。
23. 如权利要求 20-22任一所述的耐磨钢板的制造方法， 其特征在于， 开轧温度为 950-1100 °C , 终轧温度为 800-900 °C。
24. 如权利要求 20-23任一所述的耐磨钢板的制造方法， 其特征在于， 停冷温度为室温至 280 °C。
PCT/CN2013/071185 2012-07-31 2013-01-31 一种超高强度高韧性耐磨钢板及其制造方法 Ceased WO2014019353A1 (zh)

Priority Applications (7)

Application Number Priority Date Filing Date Title
KR1020157005295A KR102128026B1 (ko) 2012-07-31 2013-01-31 초고강도 고인성 내마모성 강판 및 그의 제조 방법
AU2013299254A AU2013299254B2 (en) 2012-07-31 2013-01-31 Ultrahigh-strength, high-toughness, wear-resistant steel plate and manufacturing method thereof
EP13826542.6A EP2881487B1 (en) 2012-07-31 2013-01-31 Abrasion resistant steel plate with super-high strength and high toughness, and process for preparing same
JP2015524603A JP6254160B2 (ja) 2012-07-31 2013-01-31 超高強度高靭性耐摩耗鋼板及びその製造方法
NZ630918A NZ630918A (en) 2012-07-31 2013-01-31 Ultrahigh-strength, high-toughness, wear-resistant steel plate and manufacturing method thereof
US14/418,417 US9816165B2 (en) 2012-07-31 2013-01-31 Ultrahigh-strength, high-toughness, wear-resistant steel plate and manufacturing method thereof
ZA2015/00275A ZA201500275B (en) 2012-07-31 2015-01-14 Abrasion resistant steel plate with super high strength and high toughness, and process for preparing same

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201210270605.3 2012-07-31
CN201210270605.3A CN102876969B (zh) 2012-07-31 2012-07-31 一种超高强度高韧性耐磨钢板及其制造方法

Publications (1)

Publication Number Publication Date
WO2014019353A1 true WO2014019353A1 (zh) 2014-02-06

Family

ID=47478478

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2013/071185 Ceased WO2014019353A1 (zh) 2012-07-31 2013-01-31 一种超高强度高韧性耐磨钢板及其制造方法

Country Status (9)

Country Link
US (1) US9816165B2 (zh)
EP (1) EP2881487B1 (zh)
JP (1) JP6254160B2 (zh)
KR (1) KR102128026B1 (zh)
CN (1) CN102876969B (zh)
AU (1) AU2013299254B2 (zh)
NZ (1) NZ630918A (zh)
WO (1) WO2014019353A1 (zh)
ZA (1) ZA201500275B (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103949984A (zh) * 2014-04-10 2014-07-30 大丰市飞腾铸造机械有限公司 一种耐磨抗冲击型落砂管的制造工艺及其焊接方法
JP2015200015A (ja) * 2014-03-31 2015-11-12 Ｊｆｅスチール株式会社 高温環境における耐摩耗性に優れた厚鋼板

Families Citing this family (30)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102876969B (zh) 2012-07-31 2015-03-04 宝山钢铁股份有限公司 一种超高强度高韧性耐磨钢板及其制造方法
CN103205639B (zh) * 2013-03-14 2015-02-18 长安大学 一种装载机铲刀刃及其制备方法
CN103205634B (zh) * 2013-03-28 2016-06-01 宝山钢铁股份有限公司 一种低合金高硬度耐磨钢板及其制造方法
CN103205627B (zh) * 2013-03-28 2015-08-26 宝山钢铁股份有限公司 一种低合金高性能耐磨钢板及其制造方法
CN103194674B (zh) * 2013-03-28 2015-08-26 宝山钢铁股份有限公司 一种hb360级耐磨钢板及其制造方法
CN104357747B (zh) * 2014-10-27 2017-11-03 中国科学院金属研究所 一种微合金化锰硼合金钢及其热处理方法和应用
GB2546809B (en) * 2016-02-01 2018-05-09 Rolls Royce Plc Low cobalt hard facing alloy
GB2546808B (en) * 2016-02-01 2018-09-12 Rolls Royce Plc Low cobalt hard facing alloy
CN105937008A (zh) * 2016-06-27 2016-09-14 江阴兴澄特种钢铁有限公司 一种薄规格耐磨钢及其制造方法
CN105908081B (zh) * 2016-06-30 2018-02-23 中车戚墅堰机车车辆工艺研究所有限公司 低合金铸钢及其冶炼方法、热处理方法和铁路机车零部件
CN113186465A (zh) * 2016-06-30 2021-07-30 中车戚墅堰机车车辆工艺研究所有限公司 低合金铸钢及其冶炼方法、热处理方法和铁路机车零部件
CN106555109A (zh) * 2016-10-31 2017-04-05 舞阳钢铁有限责任公司 兼具低温冲击性能nm550钢板及其生产方法
CN106893942B (zh) * 2017-04-02 2018-10-23 首钢集团有限公司 一种高强度贝氏体耐磨钢板及其生产方法
CN108950422B (zh) * 2017-05-26 2020-08-25 宝山钢铁股份有限公司 硬度550hb浆体疏浚管用耐磨蚀钢板及其生产方法
CN108950421B (zh) * 2017-05-26 2020-08-25 宝山钢铁股份有限公司 硬度600hb浆体疏浚管用耐磨蚀钢板及其生产方法
CN108930002B (zh) * 2017-05-26 2020-08-25 宝山钢铁股份有限公司 硬度500hb浆体疏浚管用耐磨蚀钢板及其生产方法
CN109835014B (zh) * 2017-11-28 2021-03-12 宝山钢铁股份有限公司 一种高强高韧耐磨复合钢板及其制造方法
CN108315645B (zh) * 2018-02-09 2019-12-10 天津荣程联合钢铁集团有限公司 一种耐磨钢及其生产工艺
CN108914009A (zh) * 2018-08-28 2018-11-30 宝钢湛江钢铁有限公司 Al+Ti系低成本高强船板钢及其制造方法
KR102119959B1 (ko) * 2018-09-27 2020-06-05 주식회사 포스코 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
WO2020239905A1 (de) * 2019-05-29 2020-12-03 Thyssenkrupp Steel Europe Ag Bauteil, hergestellt durch umformen einer stahlblechplatine und verfahren zu seiner herstellung
KR102250333B1 (ko) * 2019-12-09 2021-05-10 현대제철 주식회사 초고강도 냉연강판 및 이의 제조방법
CN113751499B (zh) * 2021-08-02 2024-01-05 浙江中箭工模具有限公司 一种耐磨型高速钢热轧工艺
CN118302546A (zh) * 2021-08-19 2024-07-05 蒂森克虏伯钢铁欧洲股份公司 用于在高温下成型的、具有改进加工特性的钢材
WO2023020932A1 (de) * 2021-08-19 2023-02-23 Thyssenkrupp Steel Europe Ag Stahl mit verbesserten verarbeitungseigenschaften zur umformung bei erhöhten temperaturen
CN114606434A (zh) * 2022-01-26 2022-06-10 南京钢铁股份有限公司 一种低碳当量高韧性耐磨钢板及其制造方法
CN115125439B (zh) * 2022-06-16 2023-10-31 唐山钢铁集团高强汽车板有限公司 一种锌基镀层1800Mpa级热冲压成型钢及制备方法
JP7666477B2 (ja) * 2022-09-29 2025-04-22 Ｊｆｅスチール株式会社 鋼板
CN116411224B (zh) * 2023-03-30 2025-06-24 武汉科技大学 一种高温强度持久的高强度高韧性钢及其制造方法和应用
CN118996274B (zh) * 2024-07-10 2025-11-18 江阴兴澄特种钢铁有限公司 一种制造破碎锤大规格钎杆用合金钢棒及其制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1140205A (zh) 1995-03-28 1997-01-15 王宇辉 一种中碳中合金耐磨钢
CN1865481A (zh) 2005-05-19 2006-11-22 宝钢集团上海梅山有限公司 一种贝氏体耐磨钢板制备工艺
CN101258257A (zh) * 2005-09-09 2008-09-03 新日本制铁株式会社 使用中的硬度变化小的高韧性耐磨耗钢及其制造方法
JP2012031510A (ja) * 2010-06-30 2012-02-16 Jfe Steel Corp 溶接部靭性および耐遅れ破壊特性に優れた耐磨耗鋼板
CN102876969A (zh) * 2012-07-31 2013-01-16 宝山钢铁股份有限公司 一种超高强度高韧性耐磨钢板及其制造方法

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3273404B2 (ja) * 1995-10-24 2002-04-08 新日本製鐵株式会社 厚手高硬度高靱性耐摩耗鋼の製造方法
JP3654470B2 (ja) * 1996-09-13 2005-06-02 日本電信電話株式会社 サブバンド多チャネル音声通信会議用反響消去方法
JP2002115024A (ja) * 2000-10-06 2002-04-19 Nkk Corp 靭性および耐遅れ破壊性に優れた耐摩耗鋼材ならびにその製造方法
JP4443910B2 (ja) * 2003-12-12 2010-03-31 Ｊｆｅスチール株式会社 自動車構造部材用鋼材およびその製造方法
EP1930460B1 (en) * 2005-09-06 2011-03-23 Sumitomo Metal Industries, Ltd. Low alloy steel
JP2007260705A (ja) 2006-03-27 2007-10-11 Sumitomo Metal Ind Ltd 継目無鋼管の製造方法
JP5145805B2 (ja) * 2007-07-26 2013-02-20 Ｊｆｅスチール株式会社 ガス切断面性状および耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板
CN101775545B (zh) * 2009-01-14 2011-10-12 宝山钢铁股份有限公司 一种低合金高强度高韧性耐磨钢板及其制造方法
CN101775539B (zh) * 2009-01-14 2012-03-28 宝山钢铁股份有限公司 一种高韧性耐磨钢板及其制造方法
CN101748346B (zh) * 2009-12-25 2012-02-01 舞阳钢铁有限责任公司 一种高等级别耐磨钢板及其生产方法
CN101748333B (zh) * 2009-12-25 2012-02-01 舞阳钢铁有限责任公司 一种低碳当量高强度耐磨钢板及其生产方法
JP5655356B2 (ja) 2010-04-02 2015-01-21 Ｊｆｅスチール株式会社 低温焼戻脆化割れ性に優れた耐摩耗鋼板
JP2012031511A (ja) * 2010-06-30 2012-02-16 Jfe Steel Corp 多層盛溶接部靭性と耐遅れ破壊特性に優れた耐磨耗鋼板
CN101948987B (zh) * 2010-09-21 2012-05-30 武汉钢铁(集团)公司 一种高强度高韧性钢板的制造方法
CN102002645B (zh) * 2010-12-01 2012-08-22 山东钢铁股份有限公司 一种高强度耐磨钢板的制备方法
CN102605234A (zh) * 2011-01-25 2012-07-25 宝山钢铁股份有限公司 一种400hb级耐磨钢板及其制造方法
AU2012233197B8 (en) * 2011-03-29 2015-07-30 Jfe Steel Corporation Abrasion resistant steel plate or steel sheet excellent in resistance to stress corrosion cracking and method for manufacturing the same
CN102560272B (zh) * 2011-11-25 2014-01-22 宝山钢铁股份有限公司 一种超高强度耐磨钢板及其制造方法
CN102534423B (zh) * 2012-02-29 2016-01-20 宝山钢铁股份有限公司 高强度钢板及其制造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1140205A (zh) 1995-03-28 1997-01-15 王宇辉 一种中碳中合金耐磨钢
CN1865481A (zh) 2005-05-19 2006-11-22 宝钢集团上海梅山有限公司 一种贝氏体耐磨钢板制备工艺
CN101258257A (zh) * 2005-09-09 2008-09-03 新日本制铁株式会社 使用中的硬度变化小的高韧性耐磨耗钢及其制造方法
JP2012031510A (ja) * 2010-06-30 2012-02-16 Jfe Steel Corp 溶接部靭性および耐遅れ破壊特性に優れた耐磨耗鋼板
CN102876969A (zh) * 2012-07-31 2013-01-16 宝山钢铁股份有限公司 一种超高强度高韧性耐磨钢板及其制造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2881487A4

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015200015A (ja) * 2014-03-31 2015-11-12 Ｊｆｅスチール株式会社 高温環境における耐摩耗性に優れた厚鋼板
CN103949984A (zh) * 2014-04-10 2014-07-30 大丰市飞腾铸造机械有限公司 一种耐磨抗冲击型落砂管的制造工艺及其焊接方法

Also Published As

Publication number Publication date
JP6254160B2 (ja) 2017-12-27
KR102128026B1 (ko) 2020-06-29
JP2015524881A (ja) 2015-08-27
AU2013299254A1 (en) 2015-02-19
AU2013299254B2 (en) 2018-03-29
ZA201500275B (en) 2015-12-23
EP2881487B1 (en) 2019-08-07
US9816165B2 (en) 2017-11-14
CN102876969B (zh) 2015-03-04
NZ630918A (en) 2016-07-29
EP2881487A4 (en) 2016-04-20
CN102876969A (zh) 2013-01-16
US20150191806A1 (en) 2015-07-09
KR20150036787A (ko) 2015-04-07
EP2881487A1 (en) 2015-06-10

Similar Documents

Publication Publication Date Title
WO2014019353A1 (zh) 一种超高强度高韧性耐磨钢板及其制造方法
CN102747280B (zh) 一种高强度高韧性耐磨钢板及其制造方法
KR102076053B1 (ko) 고성능 저합금 내마모성 강판 및 이의 제조 방법
KR102040680B1 (ko) 고인성 저합금 내마모성 강판 및 이의 제조 방법
CN102747282B (zh) 一种高硬度高韧性耐磨钢板及其制造方法
CN101775539B (zh) 一种高韧性耐磨钢板及其制造方法
WO2014154106A1 (zh) 一种低合金高硬度耐磨钢板及其制造方法
CN102605234A (zh) 一种400hb级耐磨钢板及其制造方法
CN111748728A (zh) 一种易焊接高强高韧耐磨钢板及其制造方法
CN115287531B (zh) 770MPa直缝焊接钢管用钢及其制造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 13826542

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 14418417

Country of ref document: US

ENP Entry into the national phase

Ref document number: 2015524603

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2013299254

Country of ref document: AU

Date of ref document: 20130131

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 2013826542

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 20157005295

Country of ref document: KR

Kind code of ref document: A