EP3821040A1 - Partie de voie en acier hypereutectoïde - Google Patents

Partie de voie en acier hypereutectoïde

Info

Publication number
EP3821040A1
EP3821040A1 EP19752261.8A EP19752261A EP3821040A1 EP 3821040 A1 EP3821040 A1 EP 3821040A1 EP 19752261 A EP19752261 A EP 19752261A EP 3821040 A1 EP3821040 A1 EP 3821040A1
Authority
EP
European Patent Office
Prior art keywords
rail
track part
hypereutectoid steel
amount
part according
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.)
Granted
Application number
EP19752261.8A
Other languages
German (de)
English (en)
Other versions
EP3821040B1 (fr
Inventor
Jürgen GORIUPP
Mario Kuss
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.)
Voestalpine Rail Technology GmbH
Original Assignee
Voestalpine Rail Technology GmbH
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 Voestalpine Rail Technology GmbH filed Critical Voestalpine Rail Technology GmbH
Publication of EP3821040A1 publication Critical patent/EP3821040A1/fr
Application granted granted Critical
Publication of EP3821040B1 publication Critical patent/EP3821040B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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
    • C22C38/02—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
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/08—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling structural sections, i.e. work of special cross-section, e.g. angle steel
    • B21B1/085—Rail sections
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D1/62—Quenching devices
    • C21D1/63—Quenching devices for bath quenching
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties 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 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
    • C21D9/04—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
    • 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
    • C22C38/24—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
    • C22C38/40—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
    • C21D2211/003—Cementite
    • 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
    • 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

Definitions

  • the invention relates to a track part, in particular a rail for rail vehicles, made of a hypereutectoid steel
  • the invention further relates to a method for producing such a track part.
  • RCF surface damage examples are e.g. head checks
  • Hypereutectoid steels are known for producing rails, for example from EP 2388352 A1.
  • the iron-carbon diagram shows an eutectoid at a carbon content (C content) of 0.77% by weight of carbon and at a temperature of 723 °C, at which point a fixed direct phase transition from the austenite phase to the perlite phase occurs on cooling.
  • Perlite is preferred over other steel modifications for rails in terms of wear resistance and elongation at break, as it is best for wear due to the lamellar structure.
  • the pearlitic structure comprises a ferrite phase, wherein the ferrite content in the perlite phase can be regarded as a tough and ductile phase and as a fixed variable, because the C-content of the rail steel varies only in very narrow limits, and the pearlitic structure further comprises a cementite phase, wherein the ferrite and the cemetite phases are arranged in lamellar
  • secondary cementite precipitates are significantly influenced by a combination of alloying and heat treatment technology.
  • the knowledge of the precipitation temperature of the secondary cementite is of crucial importance and one should not fall below the precipitation temperature before the subsequent heat treatment.
  • the cooling rate during the heat treatment process should be as high as possible to suppress the precipitation of secondary cementite.
  • Essential for the quality of a rail is thus a high wear resistance, for which essentially the hardness (for example indicated as Brinell hardness) of the rail is
  • the desirable hardness inevitably goes hand in hand with a reduction in toughness, which is detrimental to the durability of the track part, especially in heavy load, where the rail is subjected to particularly high bending stresses when driving over a rail vehicle.
  • the invention therefore aims to improve a track part, in particular a rail, which is to consist of a low-alloy steel for reasons of cost and ease of welding, to the effect that due to a high hardness of the material even at elevated wheel loads, the wear resistance in the rail head is increased so far that a use time of longer than 30 years can be ensured.
  • the track part should be well weldable and have similar other material properties as proven steels used in the rail construction, such as e.g. a similar electrical conductivity and a similar coefficient of thermal expansion.
  • the invention aims to provide a simple
  • the manufacturing method for a track part according to the invention which is characterized by a short process time (avoidance of incandescent phases) , high reproducibility and high cost-effectiveness.
  • the method shall be suitable for producing long rails of e.g. over 100 m in length, with specification-compliant material properties over the entire rail length to be ensured.
  • the invention according to a first aspect provides a track part, in particular a rail of the type mentioned above, which is characterized in that a hypereutectoid steel with the following directional
  • o of Cr and the steel, at least in the head portion of the rail, has a pearlitic structure that is substantially free of secondary cementite networks.
  • the rail according to the invention has proven to be extremely suitable, since a hardness in the range of 460 HB and higher could be achieved and the rail according to the invention at the same time has a sufficient elongation at break for the heavy load range.
  • a secondary cementite network means a microstructure in which the former austenite grains are completely surrounded by a closed network of secondary cementite .
  • Secondary cementite precipitates reduce the carbon supply for the formation of pearlitic cementite lamellae needed for wear resistance. For these reasons, the suppression of secondary cementite in hypereutectoid rail steels is considered to be advantageous.
  • the concentration of manganese in the present steel is selected to shift the formation of embrittling secondary cementite to lower temperatures due to its austenite stabilizing effect, thereby enabling fine grain rolling at low rolling temperatures of hypereutectoid rail steels while suppressing secondary cementite precipitation.
  • the lower limit of 0.9 wt.-% manganese was chosen because the precipitation temperature of embrittling secondary cementite shifts to higher temperatures if one falls below this lower limit, which would result in that the
  • the upper limit of 1.35 wt.-% manganese was chosen to ensure castability of the steel.
  • the alloy composition of the present invention provides a lower limit of the carbon content of 0.98 wt% and an upper limit of 1.17 wt%.
  • the lower limit was chosen here in view of a sufficient strength, since carbon brings the required strength.
  • the upper limit was chosen in order to avoid the precipitation of secondary cementite networks, especially from a depth of approx. 5-10 mm below the rail head
  • the alloy composition of the invention provides for silicon a lower limit of 0.70 wt.-% and an upper limit of 1.10 wt . - %.
  • the lower limit was chosen to ensure the effectiveness of silicon to suppress embrittling secondary cementite precipitates. This extends the process window of the heat treatment so that a secondary cementite network can be avoided.
  • the upper limit is based on the background that, if this limit is exceeded, the required electrical
  • the alloy composition according to the invention provides for chromium a lower limit of 0.15 wt.-% and an upper limit of 0.70 wt.-%. It has been found that chromium, starting at a content of 0.15 wt.-%, has a marked effect on the cross- section hardening of the rail and suppresses the formation of secondary cementite, which in turn widens the process window of the heat treatment, so that the secondary
  • cementite structure cannot be formed as a network.
  • the upper limit of 0.70 wt.-% was chosen because the
  • weldability of the rail is made difficult or impossible with increasing chromium content.
  • the invention is based on a particular selection of the quantitative ranges of the individual alloy constituents, the individual alloying constituents having partially opposite effects.
  • a higher carbon content is desirable for achieving high strengths, but as the carbon content increases, the disadvantage of the increasing austenite-to-perlite- transition temperature has to be considered.
  • high silicon contents are responsible for the suppression of embrittling secondary cementite precipitates, they also increases the austenite-to-perlite-transition temperature.
  • secondary cementite precipitates at relatively high temperatures due to the relatively high carbon and silicon content, so that secondary cementite precipitates can occur in an enhanced form also prior to the heat treatment process.
  • the use of high carbon content in combination with silicon is actually counterproductive.
  • high silicon concentrations also have a diffusion- inhibiting effect on carbon and thus minimize secondary cementite. To take advantage of this positive effect, the negative effect of the shift in the transformation
  • the directional analysis of the rail steel may be formed such that A1 (aluminum) is additionally used in amounts of 0.01- 0.06 wt.-%. This leads to a minimization of the pearlite grain size, which is beneficial to the elongation at break.
  • vanadium may additionally be used in amounts of from 0.07 to 0.20 wt.-%, in particular from 0.10 to 0.20 wt.-%, as in a preferred embodiment of the present invention. It has been found that already starting from a vanadium content of 0.07 wt.-%, an increase in strength and a grain refining effect may be achieved. The strength decreases again from the upper limit of 0.2 wt.-%, since too much C from the matrix is bound.
  • Nb niobium
  • Nb niobium
  • (titanium) may additionally be used in amounts of 0.015 - 0.05 wt . -% .
  • V is used in amounts of 0.07 to 0.20 wt.-%, in particular 0.10 to 0.2 wt.-%, together with Nb in amounts of 0.010 to 0.030 wt.-%.
  • Al is used in amounts of 0.01 - 0.06 wt.-% together with Nb in amounts of 0.01 - 0.03 wt.-%.
  • the grain refining effect can be increased by a nitrogen content set in the steel in the range of 40 to 120 ppm, which corresponds to a preferred embodiment of the present invention.
  • a steel quality is achieved which enables the production of a track part in which the steel, at least in the head portion of the rail, has a tensile strength greater than 1500 MPa, an elongation at break of greater than 8% and a Brinell hardness (according to EN ISO 6506-1) of greater than 460 HB, as corresponds to a
  • the inventive method for producing a track part according to the invention is characterized in that a hypereutectoid steel having a composition according to any one of claims 1 to 9 is taken from a furnace at a temperature of 1000 - 1300°C, then rolled at a final rolling temperature of 850 - 950°C and is then subjected to forced cooling to a
  • the furnace is preferably a walking beam furnace.
  • the steel with the composition according to the invention is removed from the furnace and rolled to the desired shape of the track part, in
  • the conditions in the rolling mill are selected by means of the accumulated degree of transformation within continuous rolling passes on the finishing scale such that a recrystallization- controlled rolling process is achieved by means of
  • austenite grain size 8 pm to 35 pm, at least in the head portion of the rail. According to the invention this is followed by a rapid cooling to below 600°C, in which temperature range no secondary cementite is precipitated any more, creating a very wear-resistant fine-pearlitic microstructure with sufficient elongation at break for the heavy-duty application.
  • the forced cooling takes place at least in the head portion of the rail, in order to ensure at least there the pearlitic structure.
  • the cooling rate is chosen so high that a substantial suppression of secondary cementite precipitation takes place, but no formation of undesirable secondary phases such as wear-promoting bainite or martensite occurs.
  • the process according to the invention is preferably further developed in that the forced cooling takes place in a bath of cooling medium not being pure water.
  • cooling medium not being pure water.
  • cementite precipitates to a more rapid cooling, and on the other hand, suppresses the emergence of soft staining the surface of the rail.
  • a particularly effective cooling succeeds in the interest of avoiding secondary cementite precipitates, when the forced cooling takes place in a polymer bath with a temperature of 10 - 70°C, as provided according to a preferred embodiment of the present invention.
  • the method is carried out such that, to avoid secondary cementite precipitates, the forced cooling is performed at a rate of at least 4°C/sec, preferably at least 8°C/sec, more preferably at least 12°C/sec. In this way, the area of the formation of secondary cementite precipitates is quickly passed through in the iron-carbon diagram, so that the embrittlement of the rail steel can be effectively avoided.
  • a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
  • Example 2 A rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
  • a rail with a tensile strength of 1550 MPa/mm 2 A rail with a tensile strength of 1550 MPa/mm 2 , an
  • a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
  • a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
  • a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
  • a rail with a tensile strength of 1570 MPa/mm 2 A rail with a tensile strength of 1570 MPa/mm 2 , an
  • the rails produced according to Examples 1 to 5 have a purely pearlitic microstructure essentially free of
  • the rail material microstructure at least in the standard tensile test position of the rail (10 mm below the running edge) , has a pearlitic structure below 3%-nital-etching substantially free of secondary cementite networks
  • the cementite lamella thickness is significantly increased in the case of the rail according to the invention compared with a rail from the prior art (rail R400HT according to EN 13674-1), as can be seen from Fig. 2.
  • the degree of secondary cementite itself can be assessed with the aid of a classification chart for assessing the secondary cementite precipitates on the microstructure, as shown in Fig. 3.

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)
  • Heat Treatment Of Articles (AREA)

Abstract

L'invention concerne une partie de voie, en particulier un rail destiné à des véhicules ferroviaires, en acier hypereutectoïde, comprenant un pied de rail, une bande de rail et une section de tête de rail, un acier hypereutectoïde doté de l'analyse directionnelle suivante étant utilisé : 0,98 à 1,17 % en poids de C, 0,90 à 1,35 % en poids de Mn, 0,70 à 1,10 % en poids de Si, 0,15 à 0,70 % en poids de Cr, et l'acier, au moins dans la section de tête du rail, présentant une structure perlitique qui est sensiblement exempte de réseaux de cémentite secondaires.
EP19752261.8A 2018-07-10 2019-07-03 Partie de voie en acier hypereutectoïde Active EP3821040B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
ATA201/2018A AT521405B1 (de) 2018-07-10 2018-07-10 Gleisteil aus einem hypereutektoiden Stahl
PCT/IB2019/055660 WO2020012297A1 (fr) 2018-07-10 2019-07-03 Partie de voie en acier hypereutectoïde

Publications (2)

Publication Number Publication Date
EP3821040A1 true EP3821040A1 (fr) 2021-05-19
EP3821040B1 EP3821040B1 (fr) 2023-08-30

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP19752261.8A Active EP3821040B1 (fr) 2018-07-10 2019-07-03 Partie de voie en acier hypereutectoïde

Country Status (13)

Country Link
US (1) US20200017943A1 (fr)
EP (1) EP3821040B1 (fr)
AR (1) AR115726A1 (fr)
AT (1) AT521405B1 (fr)
AU (1) AU2019204857A1 (fr)
BR (1) BR102019014230B1 (fr)
CA (1) CA3048723C (fr)
ES (1) ES2834057T3 (fr)
MA (1) MA53132A (fr)
PL (1) PL3821040T3 (fr)
UA (1) UA127116C2 (fr)
WO (1) WO2020012297A1 (fr)
ZA (1) ZA202006996B (fr)

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AU2021302317B2 (en) * 2020-06-29 2023-11-16 Jfe Steel Corporation Rail having excellent fatigue crack propagation resistance characteristics, and method for producing same
CN115094338B (zh) * 2022-07-27 2023-09-22 内蒙古科技大学 一种过共析钢轨用钢及其制备方法
WO2024134872A1 (fr) * 2022-12-23 2024-06-27 日本製鉄株式会社 Rail et procédé de fabrication de rail

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JP5776565B2 (ja) * 2012-01-23 2015-09-09 新日鐵住金株式会社 レール鋼及び車輪鋼の材質選択方法
US9534278B2 (en) * 2012-06-14 2017-01-03 Nippon Steel & Sumitomo Metal Corporation Rail
BR112018073094A2 (pt) * 2016-05-19 2019-03-06 Nippon Steel & Sumitomo Metal Corp trilho

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BR102019014230B1 (pt) 2023-10-31
CA3048723A1 (fr) 2020-01-10
AT521405A1 (de) 2020-01-15
AU2019204857A1 (en) 2020-01-30
ES2834057T1 (es) 2021-06-16
AR115726A1 (es) 2021-02-17
UA127116C2 (uk) 2023-05-03
WO2020012297A1 (fr) 2020-01-16
MA53132A (fr) 2021-05-19
PL3821040T3 (pl) 2024-02-12
ES2834057T3 (es) 2024-03-26
BR102019014230A2 (pt) 2020-02-27
US20200017943A1 (en) 2020-01-16
AT521405B1 (de) 2021-09-15

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