US20200017943A1 - Track part made of a hypereutectoid steel - Google Patents

Track part made of a hypereutectoid steel Download PDF

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US20200017943A1
US20200017943A1 US16/506,234 US201916506234A US2020017943A1 US 20200017943 A1 US20200017943 A1 US 20200017943A1 US 201916506234 A US201916506234 A US 201916506234A US 2020017943 A1 US2020017943 A1 US 2020017943A1
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rail
track part
hypereutectoid steel
amount
part according
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Jürgen GORIUPP
Mario KUSS
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Voestalpine Rail Technology GmbH
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Voestalpine Schienen GmbH
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Assigned to VOESTALPINE SCHIENEN GMBH reassignment VOESTALPINE SCHIENEN GMBH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: GORIUPP, JURGEN, KUSS, MARIO
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/18—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
    • C22C38/40—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
    • C22C38/06—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
    • 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

Definitions

  • the invention relates to a track part, in particular a rail for rail vehicles, made of a hypereutectoid steel comprising a rail foot, a rail web and a rail head portion.
  • the invention further relates to a method for producing such a track part.
  • 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 relationship to each other.
  • 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. Excessive levels of secondary cementite can adversely affect the breaking properties of steels, as the breaking behavior becomes increasingly intercrystalline.
  • 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 characteristic.
  • 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 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 analysis is used:
  • the steel at least in the head portion of the rail, has a pearlitic structure that is substantially free of secondary cementite networks.
  • this steel composition 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.
  • the feature that at least in the head portion of the rail a pearlitic structure is substantially free of secondary cementite networks means that at most 5% of the existing secondary cementite precipitates are in the form of secondary cementite networks.
  • 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 suppression of the same can not be guaranteed in the subsequent heat treatment.
  • 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 surface, even with a lower heat dissipation during forced cooling after rolling.
  • 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 conductivity of the rails would decrease in such a way that in some cases impairments in the signaling technology would be possible.
  • 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.
  • the directional analysis of the rail steel may be formed such that Al (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.
  • V (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
  • Ti titanium
  • Ti titanium
  • 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 preferred embodiment of the present invention.
  • 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 temperature of 450° C. to 600° C.
  • 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 particular rail.
  • a final rolling temperature i.e. a temperature of the steel at the end of the rolling mill, of 850° C.
  • secondary cementite precipitates at the perlite grain boundaries, especially in the formation of secondary cementite networks can lead to unacceptable embrittlement of the rail.
  • 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 deformation induced precipitations and precipitates in solution taking into account the forming speed of the reduction per pass, the temperature and the alloy composition, which allows to realize a small former austenite grain size of 8 ⁇ m to 35 ⁇ m, 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.
  • a bath of cooling medium not being pure water With non-pure water cooling media evaporation effects on the surface to be cooled of the rail can be avoided, which leads on the one hand to improved heat transfer from the hot steel to the cooling medium and, consequently, in the interest of avoiding secondary 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:
  • a rail with a tensile strength of 1580 MPa/mm 2 , an elongation at break (A 5 ) of 8.5% and a hardness (RS) of 475 HB (Brinell hardness) was obtained.
  • 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 , an elongation at break (A 5 ) of 9.2% and a hardness (RS) of 470 HB (Brinell hardness) was obtained.
  • 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 1515 MPa/mm 2 , an elongation at break (A 5 ) of 9.7% and a hardness (RS) of 463 HB (Brinell hardness) was obtained.
  • 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 1500 MPa/mm a , an elongation at break (A 5 ) of 9.6% and a hardness (RS) of 460 HB (Brinell hardness) was obtained.
  • 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 , an elongation at break (A 5 ) of 9.2% and a hardness (RS) of 478 HB (Brinell hardness) was obtained.
  • the rails produced according to Examples 1 to 5 have a purely pearlitic microstructure essentially free of secondary cementite networks according to FIG. 1
  • FIG. 1 depicts the pearlitic microstructure of the track part according to the invention
  • FIG. 2 is a chart showing the cementite lamella thickness of the track part of the present invention as compared to the cementite lamella thickness of a rail according to the state of the art
  • FIG. 3 depicts a classification of secondary cementite networks in the material microstructure of the inventive rail part
  • FIG. 4 is a chart showing the wear resistance of the track part of the present invention as compared to the wear resistance of a rail according to the state of the art.
  • 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 corresponding to the classification chart in FIG. 3 .
  • 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 .

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  • 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)
US16/506,234 2018-07-10 2019-07-09 Track part made of a hypereutectoid steel Abandoned US20200017943A1 (en)

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
ATA201/2018 2018-07-10

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US20200017943A1 true US20200017943A1 (en) 2020-01-16

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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)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2022004247A1 (fr) * 2020-06-29 2022-01-06 Ｊｆｅスチール株式会社 Rail présentant d'excellentes caractéristiques de résistance à la propagation de fissures par fatigue, et son procédé de production
CN115094338A (zh) * 2022-07-27 2022-09-23 内蒙古科技大学 一种过共析钢轨用钢及其制备方法

Citations (1)

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Publication number Priority date Publication date Assignee Title
US8469284B2 (en) * 2009-02-18 2013-06-25 Nippon Steel & Sumitomo Metal Corporation Pearlitic rail with excellent wear resistance and toughness

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BR9506522A (pt) * 1994-11-15 1997-09-02 Nippon Steel Corp Trilho de aço perlítico que tem excelente resisténcia ao desgaste e método de produção do mesmo
DE19906694C2 (de) 1999-02-18 2002-04-11 Lueraflex Gmbh G Lueckenotto Breitstreckwalze
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EP3821040A1 (fr) 2021-05-19
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