AU2016200056B2 - High-Strength and Highly Fatigue-Resistant Steel Rail and Production Method Thereof - Google Patents

High-Strength and Highly Fatigue-Resistant Steel Rail and Production Method Thereof Download PDF

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AU2016200056B2
AU2016200056B2 AU2016200056A AU2016200056A AU2016200056B2 AU 2016200056 B2 AU2016200056 B2 AU 2016200056B2 AU 2016200056 A AU2016200056 A AU 2016200056A AU 2016200056 A AU2016200056 A AU 2016200056A AU 2016200056 B2 AU2016200056 B2 AU 2016200056B2
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steel rail
cooling
rail
steel
strength
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Yong Deng
Hua Guo
Zhenyu Han
Jihai Jia
Chunjian Wang
Jun Yuan
Ming Zou
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Pangang Group Panzhihua Steel and Vanadium Co Ltd
Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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Pangang Group Panzhihua Steel and Vanadium Co Ltd
Pangang Group Panzhihua Iron and Steel Research Institute 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • 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
    • 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
    • C21D1/613—Gases; Liquefied or solidified normally gaseous material
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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 by deformation combined with, or followed by, heat treatment
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • 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
    • C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/009—Pearlite

Abstract

Abstract The present invention relates to a high-strength, highly wear-resistant, and highly contact-fatigue-resistant steel rail and a production method thereof, and belongs to the field of black steel manufacturing technology. The present invention provides a high-strength 5 and highly fatigue-resistant steel rail, comprising the following chemical components by weight percentage: C: 0.76%-0.86%; Si: 0.6%-1%; Mn: 0.7%-1.5%, Cr: 0.1%-0.5%, and 0.8%sMn%+Cr%s1.6%; V: 0.05%-0.3%, Ni: 0.1%-0.35%, and 0.15%sV%+Ni%s0.4%; Mo: 50.03%; P: 50.02%; S: 50.015%; Fe and inevitable impurities: the remaining content, wherein, the metallurgical structure of the steel rail is fine pearlite + A, where, A is 10 proeutectoid ferrite or proeutectoid cementite, and As2%. The tensile strength of the obtained steel rail is 1,260MPa-1,42OMPa. | 72811961 (GHMatters) P101957.AU GARYC Drawings 5 Figure 1 | 72811961 (GHMatters) P101957.AU GARYC

Description

ο (N S'
cn (N
in O O o (N H O (N 10
High-Strength and Highly Fatigue-Resistant Steel Rail and Production Method
Thereof
CROSS REFERENCE TO RELATED APPLICATIONS
This application claims priority to Chinese Application No. 201510006016.8, filed on January 7, 2015, entitled “High-Strength and Highly Fatigue-Resistant Steel Rail and Production Method Thereof, which is specifically and entirely incorporated by reference.
FIELD OF THE INVENTION
The present invention relates to a high-strength, highly wear-resistant, and highly contact-fatigue-resistant steel rail and a production method thereof, and belongs to the field of black steel manufacturing technology.
BACKGROUND OF THE INVENTION 15 With the rapid development of China’s heavy haul railways, the axle load on the freight railways in China has been increased continuously. For example, the axle load on most mixed passenger and freight transport railways is 21 tons or 23 tons, the axle load on special major freight railways, such as Daqin Railway and Shuohuang Railway, is 25 tons, and the axle load on the South Central Channel, which has just be built up and put into trial 20 run, is 30 tons. It is foreseeable that increasing the axle load of freight trains will be the most optimal and the most economical method among the methods for further improving the efficiency of railway freightage in China. In addition, as the axle load on freight railways is increased continuously, the need for high wear resistance performance and high contact fatigue resistance performance of freight railways becomes more urgent. Therefore, it is an 25 urgent task to develop new rail steel to adapt to the new railway transport pattern in China. Thus, in the present invention, a heavy-duty steel rail with high wear resistance and high contact fatigue resistance performance is developed, against the complex and heavy-haul railway transportation conditions in China.
In recent years, considering the present situation of steel rail production and railway 30 operation in China, relevant domestic and foreign steel rail manufacturers have applied for patents related with steel rail techniques in China, such as hyper-eutectoid steel rail production technique, low alloy steel rail production technique, etc.. Relevant patent applications include as indicated below. (1) Corus UK LIMITED applied for a patent for “Rail Steel with an Excellent Combination 35 of Wear Properties and Rolling Contact Fatigue Resistance” (Application Publication ο (Ν δ' (Ν Ό Ο Ο Ο (Ν Ό Ο (Ν ο
No. CN101946019A) in 2011, which related to a high-strength pearlitic steel rail with an excellent combination of wear properties and rolling contact fatigue resistance, comprising: C: 0.88-0.95%, Si: 0.75-0.92%, Mn: 0.80-0.95%, V: 0.05-0.14%, N: <0.008%, P: <0.030%, S: 0.008-0.030%, H: <2.5ppm, Cr: <0.10%, Al: <0.010%, 0: 5 <20ppm, and Fe and inevitable impurities: the remaining content. The patented steel rail has RCF resistance higher than 130,000 cycles underwater lubricated condition. (2) Baotou Steel Corporation (China) applied for a patent for “High-Strength Rare Earth Steel Rail Containing Crand V” (Application Publication No. CN102517501 A) in 2012, which related to a high-strength and highly wear-resistant rare earth steel rail and 10 belongs to the technical field of metallurgical products. The chemical components and their weight percentages in the steel rail are: C: 0.65-0.82%, Si: 0.50-0.80%, Mn: 0.70-1.20%, P: <0.025%, S: <0.025%, Cr: 0.20-0.40%, V: <0.10%, RE (addition): SO.03%, and Fe substrate and trace impurities: the remaining content. By adding Cr and V alloys and rare earth (rare earth cored wires are added after refining), the 15 elements complement each other and thereby the strength and wear resistance of the steel rail are improved, and overall properties, welding performance, and heat treatment performance of the steel rail are improved. Thus, the steel rail is applicable to important heavy-haul trunk railways and has extensive application prospects. (3) Baotou Steel Corporation (China) applied for a patent for “Steel Special for 20 High-Strength and Heat-Treated Steel Rail” (Application Publication No. CN103014486A) in 2013, which related to steel special for high-strength and heat-treated steel rail, and the chemical components of the steel by weight percentage include: C: 0.70-0.82%, Si: 0.13-0.60%, Mn: 0.65-1.25%, P orS: <0.025%, Al: <0.007%, and Fe and inevitable impurities: the remaining content. The 25 steel has reasonable composition proportion, the strength of the steel rail is improved through heat treatment, and the steel can meet the requirements for steel rails on the coal transport railways and curve steel rail in Indonesia. (4) Baotou Steel Corporation (China) applied for a patent for “Steel special for Low-Alloy and Medium-Strength Steel Rail” (Application Publication No. CN103014506A) in 30 2013, which related to steel special for low-alloy and medium-strength steel rail, and the chemical components of the steel by weight percentage include: C: 0.72-0.82%, Si: 0.35-1.00%, Mn: 0.80-1.25%, Cr: 0.40-0.70%, P: <0.020%, S: <0.020%, Al: <0.005%, and Fe and inevitable impurities: the remaining content. The steel has reasonable composition proportion and low alloying element content, the steel rail 35 has higher strength and higher hardness when compared with ordinary hot-rolled ο (N a
cn (N
O o o (N o (N r- steel rails, and the steel can meet the use requirements for steel rails on curve railways and heavy-haul railways. (5) Nippon Steel &amp; Sumitomo Metal Corporation (Japan) applied for a patent for “Steel Rail and Production Method Thereof (Application Publication No. CN102985574A) in 5 2013, which provided a steel rail comprising the following components by weight percentage: C: >0.85 and <1.20%, Si: 0.05-2.00%, Mn: 0.05-0.50%, Cr: 0.05-0.60%, P: <0.0150%, and Fe and inevitable impurities: the remaining content, wherein, 97% or more of a head surface portion, which is in a range from a surface of a head corner portion and a head top portion as a starting point to a depth of 10mm, has a pearlite 10 structure, wherein, the Vickers hardness of the pearlite structure is Hv320-500, and a CMn/FMn value which is a value obtained by dividing CMn [at. %] that is a Mn concentration of a cementite phase in the pearlite structure by FMn [at. %] that is a Mn concentration of a ferrite is >1.0 and <5.0. (6) Voest-Alpine Stahl AG (Austria) applied for a patent for “Method for Heat Treatment of 15 Rails” (Application Publication No. CN1085258A) in 1993, which related to a method for the thermal treatment of steel rail, in particular of the rail head, in which cooling is carried out in a cooling medium that contains a synthetic cooling agent additive, starting at temperatures above 720°C. In order to prevent the rail web from hardening while maintaining optimum cooling speeds for the rail head, immersion in the cooling 20 medium is continued until a surface temperature between 450°C and 550°C is obtained after drawing the submerged areas of the rails without temperature equalization over the whole cross section. (7) Nippon Steel Corporation (Japan) applied for a patent for “Pearlite-Based High-Carbon Steel Rail with Excellent Ductility and Method for Manufacturing the 25 Same” (Application Publication No. CN102803536A) in 2012, which related to a pearlite-based high-carbon steel rail with excellent ductility, comprising the following components by mass percentage: C: more than 0.85 to 1.40%, Si: 0.10 to 2.00%, Mn: 0.10 to 2.00%, Ti: 0.001 to 0.01%, V: 0.005 to 0.20%, N: less than 0.0040%, and Fe and inevitable impurities: the remaining content; the contents of Ti and V meet the 30 following formula (1), and the rail head part is a pearlite structure: 5 < [V (% by mass)]/[Ti (% by mass)] s 20. (8) BNSF Railway Co., Ltd. (USA) applied for a patent for “High-Strength and Damage-Resistant Steel Rail and Method for Manufacturing the Same” (Application Publication No. CN1063916A) in 1991. The patent puts forth a high-strength and 35 damage-resistant steel rail, comprising the following components by weight ο (N a
(N
Ooo (No (N 10 15 percentage: C: (0.60-0.85)%, Si: (0.1-1.0)%. Mn: (0.5-1.5)%. P: <0.035%, S: <0.040%, Al: <0.05%, and Fe and inevitable impurities: the remaining content. The hardness of the corner part 2 and head side part 3 of rail is HB341-HB405, and the hardness of the head top part is not more than 90% of the hardness of the corner part and head side part of rail. With that invention, injuries of the top part of rail head resulted from excessive contact pressure incurred by scuffs on the head part can be inhibited, and the service life of the steel rail can be prolonged. (9) Nippon Kokan Co., Ltd. (Japan) applied for a patent for “Wear-Resistant Steel Rail Capable for Preventing Propagation of Unstable Fracture” (Application Publication No. CN86106894A) in 1986, in which the steel rail comprises the following components by weight percentage: C: 0.50-0.85%, Si: 0.10-1.0%, Mn: 0.50-1.50%, P: <0.035%, S: <0.035%, Al: <0.050%, and Fe and inevitable impurities: the remaining content. The structure of the rail web is high-ductility tempered bainite structure or mixed structure of bainite and martensite. The steel rail may further comprises one or more of the following elements by weight percentage: Cr: 0.05-1.50%, Mo: 0.05-0.20%, V: 0.03-0.10%, Ni: 0.10-1.00%, and Nb: 0.005-0.050%.
SUMMARY OF THE INVENTION
The technical problem to be solved in the present invention is to provide a high-strength, 20 highly wear-resistant, and highly contact-fatigue-resistant steel rail and a production method thereof.
The technical solution of the present invention is as indicated below. A high-strength and highly fatigue-resistant steel rail, consisting of the following chemical components by weight percentage: C: 0.76%-0.86%; Si: 0.60%-1.00%; Mn: 25 0.70%-1.50%, Cr: 0.10%-0.50%, and 0.80%<Mn%+Cr%<1.60%; V: 0.05%-0.30%, Ni: 0.10%-0.35%, and 0.15%<V%+Ni%<0.40%; Ti: 0.05%-0.30%, Nb: 0.005%-0.10%; Mo: <0.03%: P: ^0.020%: S: <0.015%; Fe and inevitable impurities: the remaining content, wherein, the metallurgical structure of the steel rail is fine pearlite + A, where, A is proeutectoid ferrite or proeutectoid cementite, and A<2%. 30 Preferably, A is proeutectoid ferrite or proeutectoid cementite, and A<1 %.
The tensile strength of the steel rail is 1,260MPa-1,420MPa, the hardness of the rail head tread is 390HB-432HB, the hardness of the part at 10mm below the surface of rail head is 380HB-420HB, and the hardness of the part at 24mm below the surface of rail head is 370HB-401HB. 35 The present invention further provides a method for producing the high-strength and highly ο (Ν S' (Ν Ο Ο Ο (Ν Ό Ο (Ν 35 fatigue-resistant steel rail, comprising the procedures in turn: converter smelting - LF refining - RH vacuum treatment - continuous casting - rolling - cooling - straightening, wherein, the finish rolling temperature in the rolling procedure is controlled to be 930°C~1,000°C; the initial cooling temperature in the cooling procedure is controlled to be 5 780°C~880°C, the final cooling temperature is controlled to be 300°C~400°C, and the cooling rate is controlled to be 4.0°C~10.0°C/s.
Preferably, the cooling method is at least one selected from the group consisting of air blast cooling, water mist cooling and water cooling.
The present invention has the following beneficial effects. Compared with the inventions 10 reported in the prior art, in the present invention, the second-phase structure (e.g., proeutectoid ferrite and proeutectoid cementite) is less, and the full rail profile is pearlite structure; especially, there is no martensite or bainite structure in tempered state in the rail web; thus, the risk of occurrence of horizontal cracks in the rail web in the service life of the steel rail is avoided. In addition, the present invention has the following advantages. 15 (1) The production process of the steel rail is compact and the operation is easier to control; a secondary heating procedure is eliminated, when compared with an offline heat treatment process; thus, energy and production time are saved. (2) Through the process described above, the cooiing of the rail head is more uniform, and the depth of hardened layer in the rail head is greater. 20
BRIEF DESCRIPTION OF THE DRAWINGS
Figure 1 is a structural representation of hardness testing positions on the steel rail tread, where, L=10mm, and B=24mm. At the hardness testing position AO on the rail tread, when the steel rail tread is tested, the surface layer of the rail tread must be ground off by 25 0.50mm, before Brinell hardness test can be carried out for the surface; A1, B1 and C1 are hardness testing points at 10mm distance from the surface of rail head, A2, B2 and C2 are hardness testing points at 24mm distance from the surface of rail head.
Figure 2 is a partially enlarged view of part A in Figure 1.
Figure 3 shows the typical metallurgical structure of the sample obtained in example 1, and 30 the metallurgical structure is pearlite + 0.8% trace proeutectoid ferrite.
DETAILED DESCRIPTION OF EMBODIMENTS
The present invention provides a high-strength and highly fatigue-resistant steel rail, comprising the following chemical components by weight percentage: C: 0.76%~0.86%; Si: 0.60%~1.00%; Mn: 0.70%~1.50%, Cr: 0.10%~0.50%, and 0.80%<Mn%+Cr%<1.60%; V: ο (Ν m (Ν Ό Ο Ο Ο (Ν Ό Ο (Ν ο 0.05%~0.30%, Νϊ: 0.10%~0.35%, and 0.15%<V%+Ni%<0.40%; Mo: <0.03%; Ρ: <0.020%; S: <0.015%: Fe and inevitable impurities: the remaining content, wherein, the metallurgical structure of the steel rail is fine pearlite + A, where, A is proeutectoid ferrite or proeutectoid cementite (also referred to as secondary cementite), and A<2%. 5 Proeutectoid ferrite: it means ferrite precipitating from austenite lower than the eutectoid composition as the austenite is cooled down from a high temperature before eutectoid transformation (eutectoid transition) takes place.
Proeutectoid cementite: it is also referred to as secondary cementite, which refers to FesC precipitating from austenite A. The secondary cementite precipitates from austenite along 10 the grain boundaries as the carbon content changes during temperature drop. It appears in hypereutectoid steel in most cases and is usually in mesh form. In view that the secondary cementite meshes have adverse effects to the performance of the steel, they can be broken by normalization to improve performance.
Preferably, 0.05%~0.30% Ti and 0.005%~0.10% Nb may be added, depending on the 15 requirement for strengthening. Hereinafter, the design and control ranges of the elements will be described. C is a positive element for improving wear resistance of steel rail. However, if the carbon content is too high, a large amount of proeutectoid cementite (also referred to as secondary cementite) may appear; if the carbon content is too low, a large amount of 20 proeutectoid ferrite may precipitate; both cases have adverse effects to the contact fatigue resistance of the steel rail. Hence, in the present invention, the carbon content is controlled to be within a range of 0.76%~0.86%, so that proeutectoid ferrite and proeutectoid cementite can be controlled to be 2.0% or lower.
Si is a major element for solution strengthening, and can improve the strength and wear 25 resistance of steel rail. In addition, in eutectoid steel rails. Si is an element that promotes the precipitation of ferrite, and has a function of inhibiting the precipitation of cementite. However, if the Si content is too high, the plasticity and toughness of the steel rail will be decreased: consequently, the contact fatigue resistance of the steel rail will be decreased. Hence, in the present invention, the Si content is controlled to be within a range of 30 0.60%~1.00%.
Mn and Cr are strong-hardenability alloying elements, an optimal effect can be attained if both elements are added at the same time. In addition, Mn and Cr are major elements for improving wear resistance of steel rail. However, if the Mn content and Cr content are too high, harmful bainite and martensite structures may appear in the steel rail. Therefore, the 35 total addition amount of Mn and Cr must be controlled strictly. Hence, in the present
ο (N
m (N
Ό O O o (N o (N r- invention, to ensure the structure of the steei raii is peariite structure, the Mn content is controiied to be within a range of 0.70%~1.50%, the Cr content is controlled to be within a range of 0.10%~0.50%, and 0.80%<Mn %+Cr%<1.60%.
Mo is an eiement that can strongiy increase hardenabiiity; especiaiiy, when Mn and Cr are 5 used in combination, even a smaii amount of Mo can resuit in mixed bainite and martensite structure in the raii web, which is quite harmfui to the performance of the raii web. For exampie, in the Mn, Cr and Mo aiioy system described in the patent document CN86106894A, typicai bainite structure appears in the raii web. In the present invention, microaiioy eiements Mn and Cr are mainiy utiiized to ensure hardenabiiity performance. 10 Hence, in the present invention, the Mo content is controiied to be iower than 0.03%. V and Ni are eiements that can improve the strength-toughness of steei raii without compromising the piasticity of steei raii. However, excessive V and Ni have iittie contribution to further improvement of toughness but have adverse effects, and resuit in significantiy increased production cost at the same time. Hence, in the present invention, 15 the V content is controiied to be within a range of 0.05%~0.30%, the Ni content is controiied to be within a range of 0.10%~0.35%, and 0.15%SV%+Ni%<0.40%.
Both P and S are eiements that can not be eiiminated compieteiy. P segregates at the grain boundaries in the steei raii structure, which is very harmfui to the toughness of the steel rail; S mainly produces MnS inclusion in the steel, which is harmful to the contact fatigue 20 resistance of the steel rail. Hence, in the present invention, according to the actual production control ability of the manufacturer, the P content is controlled to be lower than 0.020%, and the S content is controlled to be lower than 0.015%.
In addition, to improve the strength and wear resistance of the rail steel, prevent the welding heat affected zone from softening, and improve the strength and hardness of 25 welded joints, Ti and Nb elements can be added for grain refining. However, if the Ti content and Nb content are too high, a second phase such as TiC or NbC will precipitate in the steel rail at a high temperature. In the precipitation process of the above second phase, the content of cementite lamellas in the peariite structure of the steel rail will be reduced, because the content of carbon dissolved in the steel rail is decreased actually. 30 Consequently, the strength and hardness of the steel will be decreased instead. Hence, in the present invention, only a very small amount of Ti and Nb can be added. The Ti content is controlled to be within a range of 0.05%~0.30%, and the Nb content is controlled to be within a range of 0.005%~0.10%.
The tensile strength of the obtained steel rail is 1,260MPa~1,420MPa, and the testing 35 positions are shown in Figure 1; the hardness of the rail head tread is 390HB~432HB, and ο Η Ο (Ν m (Ν Ό Ο Ο Ο (Ν Ό Ο (Ν the testing positions are shown in Figure 2; the hardness of the part at 10mm below the surface of rail head is 380HB~420HB, and the testing positions are shown in Figure 2; the hardness of the part at 24mm below the surface of rail head is 370HB-401HB, and the testing positions are shown in Figure 2. 5 The present invention further provides a method for producing the above high-strength and highly fatigue-resistant steel rail, comprising the procedures In trun: converter smelting - LF refining - RH vacuum treatment - continuous casting - rolling - cooling - straightening - test - surface inspection, wherein, the finish rolling temperature in the rolling procedure is controlled to be 930°C~1,000°C; the initial cooling temperature In the cooling procedure is 10 controlled to be 780°C~880°C, the final cooling temperature is controlled to be 300°C~400°C, and the cooling rate Is controlled to be 4.0°C~10.0°C/s.
The steel rail Is treated by in-line heat treatment. Usually, the finish rolling temperature of the steel rail Is 930°C~1,000°C. Forced cooling (including a combination of one or more selected from the group consisting of air blast cooling, water mist cooling, and water 15 cooling) is required in the high-temperature stage in order to inhibit the precipitation of proeutectoid ferrite or proeutectoid cementite in the steel rail, and the initial cooling temperature of the steel rail is controlled to be between 780°C~880°C. Moreover, in view of the high initial cooling temperature, high cooling efficiency is required, so that the core part of rail head can be quenched fully. Usually, the cooling is controlled at 4.0°C/s~10.0°C/s 20 cooling rate, till the temperature at the center of the rail head surface drops to 300°C~400°C. Finally, the hardness of the part at 24mm below the rail head surface reaches 370HB or more, while the hardness of the rail head surface increased to 390HB.
Example 25 The production procedures include: rail steel smelting in a converter - refining in a LF furnace and molten steel heating - RH composition control and homogenization - bloom continuous casting under six-strand protection - bloom heating - 7-stand universal rolling -feeding the rolled steel with ends into heat treatment equipment for forced cooling -discharging from the heat-treatment equipment at 300°C~400°C final cooling temperature -30 cooling on walking beam cooler - combined vertical and horizontal straightening - non-destructive test, cross sectional dimension and straightness inspection - combined cutting and drilling, and cutting to specified length - surface inspection - warehousing.
The temperature of the rolled part is 930°C~1,000°C when the rolled part is discharged from the UF finish rolling section. To ensure the initial cooling temperature Is 780°C~880°C, the 35 running speed of the roller way must be Increased, and relevant pause procedures must be ο ο (Ν δ' (Ν οοο (Ν ΌΟ (Ν 10 cancelled, so that the rolled part enters into the heat treatment equipments at a desired temperature. The range of adjustment is 4.0°C/s~10.0°C/s, according to the composition of the steel rail in smelting and the cooling rate of the steel rail controlled by temperature. Hereinafter, some examples will be described with reference to the above embodiment. The chemical composition of the rail steel in smelting in Examples 1-10 is shown in Table 1, wherein the remaining is Fe and inevitable impurities: the process conditions controlled in Examples 1-10 as shown in Table 2; the properties and metallurgical structure of the finished product in Examples 1-10 are shown in Table 3. In the examples and comparative examples of the present invention, the properties of the steel rail, including tensile strength, specific elongation, and hardness of tread, etc., are respectively tested as perGB/T228.1 “Metallic Materials - Tensile Testing - Part 1: Method of Test at Room Temperature”, and GB/T 231.1 “Metallic Materials - Brinell Hardness Test - Part 1: Test Method”. 15 20
Comparative Examples 1-4 The chemical compositions of the steel rails in smelting in the comparative examples 1-4 are shown in Table 4, wherein the remaining is Fe and inevitable impurities. The production procedures involved in comparative examples are the same as those in the examples, and the process conditions involved in comparative examples 1-4 are the same as those in Example 1. Comparative Examples 5-7 The process conditions involved in comparative examples 5-7 are shown in Table 5. The chemical compositions of the steel rails in smelting in the comparative examples 5-7 are respectively the same as those involved in Example 5-7. Table 1. Composition in Smelting in Examples 1-10
Example Chemical Composition in Smelting /wt% C Si Mn Cr V Ni Mo Ti Nb P S 1 0.76 0.65 1.12 0.32 0.11 0.12 0.02 0.11 0.005 0.019 0.013 2 0.77 0.90 1.36 0.14 0.15 0.16 0.02 0.06 0.01 0.013 0.011 3 0.78 0.71 0.96 0.21 0.06 0.18 0.01 0.08 0.005 0.017 0.010 4 0.80 0.66 0.95 0.25 0.14 0.11 0.02 0.07 0.02 0.018 0.014 5 0.82 0.75 1.06 0.30 0.16 0.17 0.01 0.06 0.008 0.018 0.010 6 0.84 0.84 0.95 0.31 0.20 0.19 0.01 0.05 0.03 0.011 0.008 7 0.86 0.80 1.05 0.25 0.08 0.10 0.02 0.06 0.01 0.018 0.010 8 0.77 0.90 1.36 0.14 0.15 0.16 0.02 0 0 0.012 0.009 9 0.76 0.65 1.12 0.32 0.11 0.12 0.02 0 0.005 0.019 0.013 10 0.80 0.66 0.95 0.25 0.14 0.11 0.02 0.07 0 0.018 0.014 25 Table 2. Cooling Rates and Process Conditions in Examples 1-10 10
r-ο (N
m (N
Ό O Oo (N Ό O (N
Example Cooling rate /°C/s Finish Rolling Temperature / °C Initial cooling temperature / °C Final cooling temperature / °C 1 7.5 971 831 368 2 8.0 978 838 373 3 6.5 948 808 360 4 7.2 960 820 365 5 5.0 942 802 354 6 9.2 995 855 380 7 8.5 990 850 378 8 7.9 975 835 371 9 7.5 972 830 365 10 7.2 961 819 364 Table 3. Performance Indexes In Examples 1-10
ExampI e Tensil e strengt h /MPa Specific elongati on /% Hardne ss of tread AO/HB Hardness at 10mm below surface /HB Hardness at 24mm below surface /HB Metallurgica 1 structure A1 B1 Cl A2 B2 C2 1 1283 12.2 393 385 383 38 5 373 375 37 3 P+O.8%0 2 1355 13.0 406 398 395 39 5 385 388 38 8 P 3 1298 12.3 395 385 388 38 5 375 375 37 3 P 4 1345 11.5 404 395 393 39 3 385 385 38 3 P 5 1340 11.0 401 393 393 39 0 383 380 38 0 P 6 1395 12.3 420 409 412 40 9 393 395 39 5 P+0.1wt%F eC 7 1386 13.1 417 406 404 40 4 390 388 39 0 P+0.3wt%F eC 8 1355 11.0 406 398 395 39 5 385 388 38 8 P 9 1270 11.7 390 383 383 38 3 373 373 37 3 P+0.3wt%a 10 1325 11.3 398 390 390 39 0 380 383 38 3 P In the Table 3, P represents pearlite, aepresents proeutectoid ferrite, and FeC represents proeutectold cementite (also referred to as secondary cementite). 11
ο (N S' S m (N
IT)OOo (NO (N
Table 4. Composition in Smelting in Comparative Examples 1-4 Comparative example Chemical Composition in Smelting /wt% C Si Mn Cr V Ni Mo Ti Nb P S 1 0.77 0.9 1.36 0.30 0.15 0.16 0.02 0.06 0.01 0.012 0.013 2 0.78 0.71 0.70 0.05 0.06 0.18 0.01 0.08 0.005 0.016 0.01 3 0.84 0.84 0.95 0.31 0.20 0.25 0.01 0.05 0.03 0.011 0.008 4 0.86 0.8 1.05 0.25 0.05 0.05 0.02 0.06 0.01 0.018 0.01
Table 5. Cooling Rates and Process Conditions in Comparative Examples 5-7 Comparative example Cooling rate /°C/s Finish Rolling Temperature l°C Initial cooling temperature / °C Final cooling temperature / °C 5 3 1100 970 465 6 12 1200 1070 605 7 8 900 770 298
Table 6. Performance Indexes in Comparative Examples 1-7
Comparati ve example Tensll e strengt h /MPa Specific elongati on /% Hardne ss of tread AO/HB Hardness at 10mm below surface /HB Hardness at 24mm below surface /HB Metallurgical structure A1 B1 Cl A2 B2 C2 1 1373 8.0 412 40 1 39 8 39 8 39 3 39 0 39 0 P+dot-like M 2 1252 10.4 383 37 3 37 0 37 3 36 1 36 3 36 3 P 3 1420 9.5 423 41 2 41 5 41 2 39 5 39 5 39 8 P+0.1wt%Fe C+ dot-like M 4 1355 10.5 406 39 5 39 5 39 3 38 3 38 3 38 0 P+0.3wt%Fe C 5 1260 11.1 385 37 8 37 8 37 5 36 6 36 6 36 8 P 6 1230 10.8 373 36 6 36 6 36 8 34 5 34 3 34 3 P+1.2wt%Fe C 7 1425 9.3 426 41 7 41 7 41 5 39 8 40 1 40 1 P+0.1wt%Fe C+ dot-like M
In the Table 6, P represents pearlite, aepresents proeutectoid ferrite, and FeC represents proeutectoid cementite (also referred to as secondary cementite), M represents martensite. 10
It can be seen from Table 1 to 6 that the second-phase structure (e.g., proeutectoid ferrite and proeutectoid cementite) is less and the steel rail in the present invention has high-strength, highly wear-resistant, and highly contact-fatigue-resistant performance. 12 ο (Ν S' CT) (Ν *Τ) Ο Ο Ο (Ν Ό Ο (Ν
In the claims which follow and in the preceding description of the invention, except where the context requires otherwise due to express language or necessary implication, the word "comprise" or variations such as "comprises" or "comprising" is used in an inclusive sense, i.e. to specify the presence of the stated features but not to preclude the presence or addition of further features in various embodiments of the invention. It is to be understood that, if any prior art publication is referred to herein, such reference does not constitute an admission that the publication forms a part of the common general knowledge in the art, in Australia or any other country.

Claims (5)

  1. Claims
    1. A steel rail, consisting of the following chemical components by weight percentage: C: 0.76%~0.86%; Si: 0.60%~1.00%; Mn: 0.70%~1.50%, Cr: 0.10%~0.50%, and 0.80%<Mn%+Cr%<1.60%; V: 0.05%~0.30%, Ni: 0.10%~0.35%, and 0.15%<V%+Ni%<0.40%; Ti: 0.05%~0.30%, Nb: 0.005%~0.10%; Mo: <0.03%; P: <0.020%; S: <0.015%; Fe and inevitable impurities: the remaining content, wherein, the metallurgical structure of the steel rail is fine pearlite+A, where, A is proeutectoid ferrite or proeutectoid cementite, and A<2%.
  2. 2. The steel rail according to claim 1, wherein, A is <1 %.
  3. 3. The steel rail according to claim 1 or 2, wherein, tensile strength of the steel rail is 1,260MPa~1,420MPa, hardness of the rail head tread is 390HB-432HB, hardness of the part at 10mm below the surface of rail head is 380HB-420HB, and hardness of the part at 24mm below the surface of rail head is 370HB-401HB.
  4. 4. A method for producing the steel rail according to any one of the claims 1 to 3, comprising the procedures in turn: converter smelting - LF refining - RH vacuum treatment - continuous casting - rolling - cooling - straightening, wherein, finish rolling temperature in the rolling procedure is controlled to be 930°C~1,000°C; initial cooling temperature in the cooling procedure is controlled to be 780°0880°C, final cooling temperature is controlled to be 300oC~400°C, and cooling rate is controlled to be 4.0°010.0°C/s.
  5. 5. The method for producing the steel rail according to claim 4, wherein, the cooling method is at least one selected from the group consisting of air blast cooling, water mist cooling, and water cooling.
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