EP3124636B1 - Rail et procédé pour le fabriquer - Google Patents

Rail et procédé pour le fabriquer Download PDF

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Publication number
EP3124636B1
EP3124636B1 EP15768893.8A EP15768893A EP3124636B1 EP 3124636 B1 EP3124636 B1 EP 3124636B1 EP 15768893 A EP15768893 A EP 15768893A EP 3124636 B1 EP3124636 B1 EP 3124636B1
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rail
rolling
cooling
hardness
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German (de)
English (en)
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EP3124636A1 (fr
EP3124636A4 (fr
EP3124636B2 (fr
Inventor
Tatsumi Kimura
Yukio Takashima
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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 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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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

Definitions

  • the present disclosure relates to a rail, particularly a rail having high hardness and small hardness variation, and also to a method for manufacturing the rail.
  • Freight cars used on freight transportation and mining railways tend to have heavier loading weights than passenger cars, which results in heavy loads acting on the axles of the freight cars and a severe contact environment between the freight car wheels and rails. Rails used under these conditions are expected to exhibit wear resistance and are conventionally made from steel having a pearlite structure.
  • PTL 8 proposes a method for manufacturing a high hardness rail having superior head internal fatigue resistance.
  • finish rolling is performed at a head surface temperature of 850°C to 1050°C to leave final finishing, and after a time interval between passes of at least 3 seconds and no greater than 1 minute, one pass or a plurality of passes of final finish rolling are performed at a head surface temperature of 800°C to 950°C and with a rolling reduction of 10% or less per pass.
  • PTL 9 describes a method for manufacturing a high toughness rail that exhibits a pearlite metal structure.
  • this method after rough rolling of a steel slab of low-alloy steel or carbon steel containing 0.60% to 1.00% of C into a rail shape, continuous finish rolling is performed for three or more rolling passes at a rail surface temperature of 850°C to 1000°C with a cross-section area reduction rolling reduction of 5% to 30% per pass and 10 seconds or less between rolling passes, and thereafter the rail is allowed to cool or is cooled from 700°C or higher to a temperature in a range of 500°C to 700°C at a rate of 2°C/s to 15°C/s.
  • PTL 10 discloses a method for manufacturing a pearlitic rail having superior wear resistance and ductility in which at least rough rolling and finish rolling are performed on a steel slab for rail rolling that contains, in mass%, 0.65% to 1.20% of C, 0.05% to 2.00% of Si, and 0.05% to 2.00% of Mn, the balance being Fe and incidental impurities.
  • Rails used in high axle load railways are expected to have superior wear resistance in order to improve rail durability and, in response, there have been various proposals for rails, such as described above, that focus on increasing hardness.
  • a rail is manufactured by hot rolling a steel raw material to a length of as long as 100 m or greater and, hardness of the rail exhibits variation in the rail length direction that is dependent on the method of manufacture. Consequently, the rail may experience uneven wear when laid and thus may be unable to sufficiently demonstrate its effects. Although it is extremely important, therefore, to reduce hardness variation in the longitudinal direction of rolling, PTL 1-10 make no mention of this hardness variation.
  • an objective of the present disclosure is to provide a rail that exhibits excellent wear resistance and reduced hardness variation in the rail length direction, and also a method for manufacturing the rail.
  • the inventors sampled test pieces from steel materials having pearlite structures corresponding to rails of differing hardness and conducted a rail wear test with respect to the test pieces in order to investigate a relationship between hardness and wear. The results of the investigation are shown in FIG. 1 .
  • Nishihara type wear test pieces 1 were sampled from two locations in a rail head 3 as illustrated in FIG. 3 .
  • a test piece sampled from a surface layer of the rail head 3 is denoted Nishihara type wear test piece 1a and a test piece sampled from an inner part of the rail head 3 is denoted Nishihara type wear test piece 1b.
  • the center, in a longitudinal direction, of the Nishihara type wear test piece 1b sampled from the inner part of the rail head 3 is located at a depth of from 24 mm to 26 mm (average value 25 mm) from an upper surface of the rail head 3.
  • the test was conducted in dry ambient conditions and the wear was measured after 1.8 ⁇ 10 5 rotations under conditions of a contact pressure of 1.2 GPa, a slip ratio of -10%, and a rotational speed of 750 rpm (tire test piece: 750 rpm). The wear was calculated from the difference in the mass of the test piece measured before and after the test.
  • wear resistance increases with increasing hardness.
  • wear resistance of a rail having a hardness of HB 400 or higher can be improved by 15% compared to an ordinary heat treated rail (HB 370).
  • HB 370 ordinary heat treated rail
  • the hardness exhibits a large amount of variation in the rail length direction, a difference in wear behavior arises for hard portions and soft portions.
  • the wear changes from 0.37 g to 0.3 g and accordingly exhibits variation of 20% or less.
  • the present disclosure enables minimization of hardness variation in a rail length direction and effectively improves rail durability (extends rail life), particularly in the case of a rail that is laid in a high axle load environment such as a heavy freight railway or a mining railway, and thus demonstrates a significant effect in industrial use.
  • Si is added to the rail material as a deoxidizing material and in order to raise the equilibrium transformation temperature (TE) and reinforce the pearlite structure (increase hardness by refining the lamellar structure).
  • TE equilibrium transformation temperature
  • these effects are small when Si content is less than 0.1%.
  • an increase in the Si content promotes decarburization and promotes formation of rail surface defects. Therefore, the upper limit for the Si content is 1.5%.
  • the Si content is preferably in a range of 0.5% to 1.3%.
  • Mn has an effect of lowering the actual pearlite transformation temperature and narrowing pearlite lamellar spacing, and is an effective element for achieving high hardness. However, these effects are small when Mn content is less than 0.01%. On the other hand, addition of greater than 1.5% of Mn to improve hardenability facilitates transformation to bainite or martensite. Therefore, the upper limit for the Mn content is 1.5%.
  • the Mn content is preferably in a range of 0.3% to 1.2%.
  • the upper limit for the P content is 0.035%.
  • a preferable range for the P content has an upper limit of 0.025%.
  • the lower limit for the P content is preferably 0.001%.
  • Cr raises the equilibrium transformation temperature (TE), contributes to refinement of pearlite lamellar spacing, and increases hardness and strength. In order to obtain such effects, it is necessary to add 0.2% or greater of Cr. On the other hand, adding greater than 2.0% of Cr increases occurrence of welding defects while also increasing hardenability and promoting martensite formation. Therefore, the upper limit for Cr content is 2.0%.
  • the Cr content is more preferably in a range of 0.26% to 1.00%.
  • one or more of 1.0% or less of Cu, 0.5% or less of Ni, 0.5% or less of Mo, and 0.15% or less of V may be added.
  • Ni is an effective element for improving toughness and ductility. Ni is also an effective element for inhibiting Cu cracking through combined addition with Cu. Therefore, in a situation in which Cu is added, Ni is preferably also added. However, these effects are not noticeable when Ni content is less than 0.01%. Therefore, in a situation in which Ni is added, the lower limit for the Ni content is preferably 0.01% or greater. On the other hand, adding greater than 0.5% of Ni increases hardenability and promotes formation of martensite. Therefore, the upper limit for the Ni content is preferably 0.5%. The Ni content is more preferably in a range of 0.05% to 0.50%.
  • Mo is an effective element for increasing strength, but this effect is small when Mo content is less than 0.01%. Therefore, the lower limit for the Mo content is preferably 0.01%. On the other hand, adding greater than 0.5% of Mo causes formation of martensite as a result of increased hardenability and dramatically decreases toughness and ductility. Therefore, the upper limit for the Mo content is preferably 0.5%.
  • the Mo content is more preferably in a range of 0.05% to 0.30%.
  • V 0.15% or less
  • V forms VC, VN, or the like as a fine precipitate in ferrite and is an element that contributes to achieving high hardness through precipitation strengthening of ferrite.
  • the solvation temperature of VC or VN is sufficiently lower than that of Ti or Nb such as to have little influence on recrystallization behavior of austenite during rolling and therefore has little influence on variation of properties in the rail length direction.
  • V also acts as a hydrogen trapping site and can be expected to exhibit an effect of inhibiting delayed fracture. Therefore, 0.001% or greater of V is preferably added.
  • the upper limit for V content is preferably 0.15%.
  • the V content is more preferably in a range of 0.005% to 0.12%.
  • the balance excluding the aforementioned components is Fe and incidental impurities.
  • N and 0.003% of O may be allowed as incidental impurities.
  • Al is effective as a deoxidizing material, Al forms cluster-shaped AlN, which significantly decreases rolling fatigue characteristics. Therefore, Al content is preferably 0.003% or less. Nb and Ti are also contained as incidental impurities as described below.
  • the steel raw material that is used is preferably continuous-cast steel obtained through continuous casting of molten steel that has been adjusted to the chemical composition described above through steelmaking processes such as a process in a blast furnace, molten iron pretreatment, a process in a converter, and RH degassing.
  • the steel raw material is hot rolled to form a rail shape by ordinary caliber rolling or universal rolling.
  • ordinary caliber rolling or universal rolling The following explains the reasons for limitations placed on conditions during the heating and rolling described above and also conditions during subsequent cooling.
  • Heating of the produced steel raw material is required to 1200°C or higher. This is performed with the main objective of sufficiently reducing deformation resistance so as to enable use of a lighter rolling load and also with the objective of homogenization.
  • the heating temperature is required to be 1200°C or higher.
  • the heating temperature is 1300°C or lower from a viewpoint of suppressing scale loss and decarburization.
  • the difference in the time interval between passes for a leading end and a trailing end of a rolled material is fundamentally small. Therefore, inhomogeneity of the austenite structure arising from the above-described difference in the time interval between passes can be resolved. It is therefore necessary for the aforementioned difference in the time interval between passes to be 15 s or less. In other words, a difference in the time interval between passes of 15 s or less can suppress hardness variation in the rail length direction.
  • the difference in the time interval between passes is preferably 12 s or less.
  • the above stipulations are conditions to be applied to rolling performed at 1000°C or lower in the hot rolling.
  • Reverse rolling may be used for rolling performed in a temperature region exceeding 1000°C, a representative example of which is rough rolling. In other words, so long as rolling at 1000°C or lower is performed continuously in a single direction, a preceding stage of rolling in a temperature region exceeding 1000°C may be performed freely.
  • two to seven passes of rolling are performed at 1000°C or lower. The reason for this is that single pass rolling requires a large rolling load and makes shaping difficult, whereas more than seven passes tends to cause a fairly inhomogeneous austenite state and increase hardness variation.
  • the cumulative area reduction rate of rolling performed at 1000°C or lower is required to be 40% or greater. The reason for this is that it is necessary to perform 40% or greater of area reduction processing at 1000°C or lower in order to promote recrystallization refinement of austenite. If the area reduction rate for rolling at 1000°C or lower is less than 40%, recrystallization refinement of austenite is insufficient and coarse austenite may partially remain, which results in increased hardness variation in the rail length direction (rolling direction).
  • a finisher delivery temperature of 900°C or higher is preferable.
  • the finisher delivery temperature is preferably 900°C or higher in order to prevent a decrease in hardness such as described above.
  • Cooling is performed consecutively after the hot rolling under the following conditions.
  • the cooling rate is in a range of 1°C/s to 10°C/s.
  • a cooling rate of greater than 10°C/s does not allow sufficient time for pearlite transformation, causes formation of bainite and martensite, and thus reduces toughness, ductility, and fatigue resistance.
  • a cooling rate of less than 1°C/s does not allow sufficient hardness to be obtained.
  • the cooling rate is preferably in a range of 2°C/s to 8°C/s.
  • the cooling rate exhibits variation of +1°C/s or less in the rolling longitudinal direction. Restricting cooling rate variation to ⁇ 1°C/s or less reduces variation in pearlite lamellar spacing, enables hardness variation of ⁇ HB 10 or less to be achieved, and reduces wear resistance variation and fatigue resistance variation in the rail longitudinal direction.
  • a pearlitic steel rail that has a surface hardness of preferably HB 400 or greater and that exhibits surface hardness variation of ⁇ HB 15 points or less in the rail length direction.
  • a homogeneous and high-hardness pearlitic steel rail that exhibits little hardness variation in the rolling length direction can be obtained.
  • the cooling start temperature and the cooling stop temperature are results for surface temperature of a rail corner measured by a thermoviewer.
  • the rail cooling rate is an average value of cooling rates measured from cooling start and end temperatures and cooling times measured at 5 m intervals in the length direction. With regards to cooling rate variation in the length direction, it was determined whether the difference between a largest value and a smallest value in variation of the cooling rates was greater than ⁇ 1°C/s or was less than or equal to ⁇ 1°C/s.
  • the hardness of rails according to the present disclosure exhibited extremely small variation of ⁇ HB 15 or less in the rail length direction, whereas the hardness of rails that deviated from the scope of the present disclosure in terms of either or both of chemical composition and rolling conditions exhibited variation of greater than ⁇ HB 15.

Claims (2)

  1. Rail comprenant
    une composition chimique constituée, en % en masse, de :
    0,60 % à 1,0 % de C ;
    0,1 % à 1,5 % de Si ;
    0,01 % à 1,5 % de Mn ;
    0,035 % ou moins de P ;
    0,030 % ou moins de S ;
    0,1 % à 2,0 % de Cr,
    et éventuellement l'un ou plus de
    0,006 % ou moins de N ;
    0,003 % ou moins de O ;
    0,003 % ou moins d'Al ;
    0,003 % ou moins de Nb ;
    0,003 % ou moins de Ti ;
    1,0 % ou moins de Cu ;
    0,5 % ou moins de Ni ;
    0,5 % ou moins de Mo ; et
    0,15 % ou moins de V,
    le reste étant du Fe et des impuretés inévitables,
    la dureté de surface de la tête du rail étant égale ou supérieure à 400 HB et la dureté de surface d'une tête du rail présentant une variation de ± 10 points HB ou moins dans un sens de la longueur du rail.
  2. Procédé de fabrication d'un rail consistant à :
    chauffer, à une température entre 1200 °C et 1300 °C, une matière première d'acier ayant une composition chimique constituée, en % en masse, de :
    0,60 % à 1,0 % de C ;
    0,1 % à 1,5 % de Si ;
    0,01 % à 1,5 % de Mn ;
    0,035 % ou moins de P ;
    0,030 % ou moins de S ;
    0,1 % à 2,0 % de Cr,
    et éventuellement l'un ou plus de
    0,006 % ou moins de N ;
    0,003 % ou moins de O ;
    0,003 % ou moins d'Al ;
    0,003 % ou moins de Nb ;
    0,003 % ou moins de Ti ;
    1,0 % ou moins de Cu ;
    0,5 % ou moins de Ni ;
    0,5 % ou moins de Mo ; et
    0,15 % ou moins de V,
    le reste étant du Fe et des impuretés inévitables,
    laminer à chaud la matière première d'acier après le chauffage, le laminage à chaud étant effectué en continu dans une seule direction de sorte que le laminage dans un sens de la longueur du rail dans une zone de température ne dépassant pas 1000 °C est effectué en 2 à 7 passes avec une différence d'intervalle de temps entre passes de 15 s ou moins dans le sens de la longueur du rail, un taux de réduction de surface cumulé égal ou supérieur à 40 % pour une partie formant une tête de rail, et une température en sortie de finissage égale à supérieure à 900 °C ; et
    refroidir la tête de rail après le laminage à chaud depuis une température de début de refroidissement de 800 °C ou plus jusqu'à une température d'arrêt de refroidissement de 400 °C à 600 °C à une vitesse de refroidissement de 1 °C/s à 10 °C/s, la vitesse de refroidissement lors du refroidissement présentant une variation de ± 1 °C/s ou moins dans le sens du rail.
EP15768893.8A 2014-03-24 2015-03-24 Rail et procédé pour le fabriquer Active EP3124636B2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2014060786 2014-03-24
PCT/JP2015/001659 WO2015146150A1 (fr) 2014-03-24 2015-03-24 Rail et procédé pour le fabriquer

Publications (4)

Publication Number Publication Date
EP3124636A1 EP3124636A1 (fr) 2017-02-01
EP3124636A4 EP3124636A4 (fr) 2017-02-01
EP3124636B1 true EP3124636B1 (fr) 2019-03-06
EP3124636B2 EP3124636B2 (fr) 2023-05-17

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WO2015182743A1 (fr) * 2014-05-29 2015-12-03 新日鐵住金株式会社 Rail et son procédé de fabrication
CN106636891A (zh) * 2016-11-17 2017-05-10 马鞍山市银鼎机械制造有限公司 抗震铁路钢轨用球磨铸铁制备方法
CN107326302B (zh) * 2017-05-26 2018-10-19 北京交通大学 一种耐蚀贝氏体钢、钢轨及制备方法
WO2019102258A1 (fr) * 2017-11-27 2019-05-31 Arcelormittal Procédé pour la fabrication d'un rail et rail correspondant
EP3778961B1 (fr) * 2018-03-30 2022-03-09 JFE Steel Corporation Rail, et procédé de fabrication de celui-ci
BR112020019343A2 (pt) 2018-03-30 2021-01-05 Jfe Steel Corporation Trilho
JP6822575B2 (ja) * 2018-03-30 2021-01-27 Ｊｆｅスチール株式会社 レールおよびその製造方法
JP6852761B2 (ja) * 2018-10-26 2021-03-31 Ｊｆｅスチール株式会社 レールおよびその製造方法
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CN112575137B (zh) * 2020-10-26 2022-03-25 邯郸钢铁集团有限责任公司 一种高速轨钢转炉冶炼直接出钢的方法
MX2023005664A (es) * 2020-11-17 2023-05-26 Arcelormittal Aceros para rieles y un metodo de fabricacion de un riel del mismo.
CN114058824B (zh) * 2021-11-26 2023-12-08 武汉钢铁有限公司 一种提高热处理钢轨踏面硬度均匀性的生产方法及所得钢轨

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US4886558A (en) 1987-05-28 1989-12-12 Nkk Corporation Method for heat-treating steel rail head
JP2773867B2 (ja) 1987-10-19 1998-07-09 新日本製鐵株式会社 高温レールの冷却法
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EP3124636A1 (fr) 2017-02-01
CN106103772A (zh) 2016-11-09
WO2015146150A1 (fr) 2015-10-01
JPWO2015146150A1 (ja) 2017-04-13
US20170101692A1 (en) 2017-04-13
AU2015237464B2 (en) 2018-02-01
EP3124636A4 (fr) 2017-02-01
BR112016022007B1 (pt) 2021-05-11
CA2936780A1 (fr) 2015-10-01
CN106103772B (zh) 2018-05-22
AU2015237464A1 (en) 2016-08-11
JP6150008B2 (ja) 2017-06-21
CA2936780C (fr) 2018-10-02
EP3124636B2 (fr) 2023-05-17

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