EP1003920B1 - Method for producing a high-strength track element and track element thus obtained - Google Patents

Method for producing a high-strength track element and track element thus obtained Download PDF

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Publication number
EP1003920B1
EP1003920B1 EP98943853A EP98943853A EP1003920B1 EP 1003920 B1 EP1003920 B1 EP 1003920B1 EP 98943853 A EP98943853 A EP 98943853A EP 98943853 A EP98943853 A EP 98943853A EP 1003920 B1 EP1003920 B1 EP 1003920B1
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EP
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Prior art keywords
steel
temperature
cooled
basic structure
process according
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EP98943853A
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German (de)
French (fr)
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EP1003920A1 (en
Inventor
Gerhard Ratz
Walter Kunitz
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Voestalpine Turnout Technology Germany GmbH
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Voestalpine BWG GmbH
Butzbacher Weichenbau GmbH
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Classifications

    • E—FIXED CONSTRUCTIONS
    • E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
    • E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
    • E01B7/00—Switches; Crossings
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C22C38/18—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
    • 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
    • C21D2211/002—Bainite

Definitions

  • the invention relates to a method for producing a high-strength track part made of steel, in particular soft parts such as the centerpiece, tongue or wing rail.
  • the invention further relates to a switch component which is made of steel.
  • Rails and switches in particular should have a high resistance to wear, crushing and fatigue damage. Break resistance and suitability for welding should also be provided. These requirements have given rise to the use of rails with a minimum tensile strength of 1100 N / mm 2 .
  • a track part or a method for producing such is known in which a vacuum-treated steel with 0.53 to 0.52% C, 0.1 to 0.25 Si, 0.65 to 1 , 1% Mn, 0.8 to 1.3% Cr, 0.05 to 0.11% Mo, 0.05% to 0.11% V, ⁇ 0.02% P, optionally up to 0.025% Al, optionally up to 0.5% Nb, remainder iron and usual melting-related impurities, the ratio of Mn: Cr being about 0.80 ⁇ Mn: Cr ⁇ 0.85 and the ratio of Mo: V being about 1, and wherein Track part in the form of a switch section is a rolled rail section as the starting material, which has a martensitic structure, at least in the rail head, through tempering. This results in strengths of over 1500 N / mm 2 in the rail head.
  • the present invention is based on the problem of further developing a method for producing a track part of the type mentioned at the outset or a switch component itself in such a way that high strength and yield strength are obtained with an increase in the service life, so that it can be used in particular in high-stress switches.
  • the problem is solved in that steel undergoes a chemical directional analysis with 0.3 to 0.6% C, 0.8 to 1.5% Si, 0.7 to 1.0% Mn, 0.9 to 1.4 % Cr, 0.6 to 1.0% Mo, remainder iron and usual fusion-related combinations after cooling from the rolling heat and formation of a bainitic basic structure with a tensile strength of approximately 1100 N / mm 2 is first subjected to a pretreatment step by the steel with the bainitic basic structure is heated to a temperature T 4 with 400 ° C. ⁇ T 4 ⁇ 550 ° C.
  • the steel has a tensile strength of at least 1200 N / mm 2 after the pretreatment, and then to a temperature T 1 750 ° C ⁇ T 1 ⁇ 920 ° C heated, then accelerated to a temperature T 2 with 450 ° C ⁇ T 2 ⁇ 250 ° C in a polymer-water mixture, in a molten salt or in a powder, again to a temperature T. 3 > T 2 with 400 ° C ⁇ T 3 ⁇ 560 ° C t and kept at temperature T 3 for a time t 1 with 60 min ⁇ t 1 ⁇ 150 min and then cooled to room temperature.
  • the steel is heated to a temperature T 1 of in particular approximately 860 ° C. after a specific cooling from the rolling heat and formation of the basic bainitic structure with a tensile strength of approximately 1100 N / mm 2 , in order to subsequently accelerate the steel to the Cool the temperature T 2 and expose it to a cooling medium so that the core of the steel has cooled to the temperature T 2 .
  • the steel with a bainitic basic structure with usual Rail steels such as 900 A and S 1100 connected by flash butt welding can be, the connected, track parts following a common Can be subjected to heat treatment.
  • the volume of a steel bainitic basic structure is tempered, with targeted heat treatment allowing tensile strengths of up to 1700 N / mm 2 , yield strengths (technical yield strengths with 0.2% permanent elongation) to 1400 N / mm 2 , elongation at break A 5 (%) result in more than 10 and constrictions of more than 25%.
  • a switch component made of steel, manufactured according to the previously described method, is characterized in that the track part made of steel is subjected to a chemical directional analysis with 0.3 to 0.6% C, 0.8 to 1.5% Si, 0.7 to 1 , 0% Mn, 0.9 to 1.4 % Cr, 0.6 to 1.0% Mo, remainder iron as well as usual fusion-related impurities, a bainitic basic structure, a tensile strength of more than 1600 N / mm 2 and one technical yield strength of more than 1250 N / mm 2 has an elongation at break> 10% and a constriction> 25%.
  • the steel has a chemical directional analysis of 0.4 to 0.5% C, approximately 1% Si, approximately 0.8% Mn, approximately 1.0% Cr and 0.6 to 1.0% Mo , where the strength is up to 1700 N / mm 2 and the yield strength is up to 1400 N / mm 2 .
  • the steel is heat-treated in such a way that the elongation at break is> 10% and the constriction is> 25%.
  • a steel with a chemical directional analysis of 0.45% C, 1% Si, 0.8% Mn, 1% Cr, 0.8% Mo, remainder iron as well as usual fusion-related impurities is formed into a track part by rolling in order to be controlled Cooling from the rolling heat to achieve a structure with a bainitic basic structure and a strength of approximately 1100 N / mm 2 .
  • the switch component cooled to room temperature is then heated in a heat treatment furnace to a temperature of approximately 500 ° C. in order to achieve a strength of 1300 to 1400 N / mm 2 by subsequent controlled cooling.
  • the switch component is then heated to approx. 860 ° C. After reaching this temperature in the core of the switch component, the polymer-water mixture cools down to about 350 ° C.
  • a corresponding switch component is sodarm with a UIC 900 A rail or UIC S 1100 connected by flash butt welding and in a track been installed. Regular checks showed a high wear resistance, which, compared to conventional switch components, increase the stability of showed in about 50%.

Abstract

The invention relates to a high-strength steel track element, and process of making the steel track element by rolling and heat treating. The steel comprises: 0.3-0.6% C, 0.8-1.5% Si, 0.7-1.0% Mn, 0.9-1.4% Cr, 0.6-1.0% Mo, balance iron and smelting-related impurities. The steel has a bainitic basic structure, a tensile strength of at least 1600 N/mm2 and a technical yield strength of at least 1250 N/mm2.

Description

Die Erfindung bezieht sich auf ein Verfahren zur Herstellung eines hochfesten Gleisteils aus Stahl, insbesondere Weichenteils wie Herzstück, Zungen- oder Flügelschiene. Ferner bezieht sich die Erfindung auf ein Weichenbauteil, das aus Stahl hergestellt ist.The invention relates to a method for producing a high-strength track part made of steel, in particular soft parts such as the centerpiece, tongue or wing rail. The invention further relates to a switch component which is made of steel.

Durch die Geschwindigkeitszunahme von Zügen bedingt nehmen die Anforderungen an den Gleisoberbau zu. Dabei sollen insbesondere Schienen und Weichen einen hohen Widerstand gegen Verschleiß, Verquetschungen und Ermüdungsschäden aufweisen. Auch soll eine Bruchsicherheit und eine Eignung zum Schweißen gegeben sein. Diese Forderungen haben den Einsatz von Schienen mit Mindestzugfestigkeiten von 1100 N/mm2 begründet.Due to the speed increase of trains, the demands on the track superstructure are increasing. Rails and switches in particular should have a high resistance to wear, crushing and fatigue damage. Break resistance and suitability for welding should also be provided. These requirements have given rise to the use of rails with a minimum tensile strength of 1100 N / mm 2 .

Aus der EP 0 620 865 B1 ist ein Gleisteil bzw. ein Verfahren zur Herstellung eines solchen bekannt, bei dem ein vakuumbehandelter Stahl mit 0,53 bis 0,52 % C, 0,1 bis 0,25 Si, 0,65 bis 1,1 % Mn, 0,8 bis 1,3 % Cr, 0,05 bis 0,11 % Mo, 0,05% bis 0,11 % V, ≤ 0,02 % P, wahlweise bis 0,025 % Al, wahlweise bis 0,5 % Nb, Rest Eisen sowie üblichen erschmelzungsbedingten Verunreinigungen verwendet wird, wobei das Verhältnis von Mn : Cr in etwa 0,80 < Mn : Cr < 0,85 und das Verhältnis von Mo : V in etwa 1 beträgt und wobei das Gleisteil in Form eines Weichenabschnitts ein gewalzter Schienenabschnitt als Ausgangsmaterial ist, der durch Vergütung ein martensitisches Gefüge zumindest im Schienenkopf aufweist. Hierdurch ergeben sich im Schienenkopf Festigkeiten über 1500 N/mm2.From EP 0 620 865 B1 a track part or a method for producing such is known in which a vacuum-treated steel with 0.53 to 0.52% C, 0.1 to 0.25 Si, 0.65 to 1 , 1% Mn, 0.8 to 1.3% Cr, 0.05 to 0.11% Mo, 0.05% to 0.11% V, ≤ 0.02% P, optionally up to 0.025% Al, optionally up to 0.5% Nb, remainder iron and usual melting-related impurities, the ratio of Mn: Cr being about 0.80 <Mn: Cr <0.85 and the ratio of Mo: V being about 1, and wherein Track part in the form of a switch section is a rolled rail section as the starting material, which has a martensitic structure, at least in the rail head, through tempering. This results in strengths of over 1500 N / mm 2 in the rail head.

Aus der Literaturstelle DE-Z: "Stahl und Eisen 115 (1995), No. 2", Seiten 93 - 98, wird ein Verfahren zur Herstellung einer naturharten bainitischen Schiene mit hoher Zugfestigkeit beschrieben. Dabei wird ein naturharter Stahl einer Wärmebehandlung derart unterzogen, dass zunächst eine Erwärmung auf über 750 °C erfolgt, um anschließend durch eine Luftabkühlung bis unterhalb von ca. 450°C ein gewünschtes bainitisches Gefüge auszubilden. Sodann kann ein Anlassen über einen Zeitraum von einer Stunde bei etwa 550 °C erfolgen, um schließlich die Schiene auf Raumtemperatur abzukühlen. Mit dem entsprechenden Verfahren können Schienenstellen einer Zugfestigkeit über 1400 N/mm2 erzielt werden.From the literature reference DE-Z: "Stahl und Eisen 115 (1995), No. 2", pages 93-98, a method for producing a naturally hard bainitic splint with high tensile strength is described. Here, a naturally hard steel is subjected to a heat treatment in such a way that it is first heated to above 750 ° C, in order to then form a desired bainitic structure by air cooling to below approx. 450 ° C. It can then be tempered at about 550 ° C for one hour to finally cool the rail to room temperature. With the corresponding method, rail points with a tensile strength above 1400 N / mm 2 can be achieved.

Der vorliegenden Erfindung liegt das Problem zugrunde, ein Verfahren zur Herstellung eines Gleisteils der eingangs genannten Art bzw. ein Weichenbauteil selbst derart weiterzubilden, dass sich eine hohe Festigkeit und Streckgrenze bei Erhöhung der Lebensdauer ergibt, so dass insbesondere ein Einsatz in hochbeanspruchten Weichen erfolgen kann. Verfahrensmäßig wird das Problem dadurch gelöst, dass Stahl einer chemischen Richtanalyse mit 0,3 bis 0,6 % C, 0,8 bis 1,5 % Si, 0,7 bis 1,0 % Mn, 0,9 bis 1,4 % Cr, 0,6 bis 1,0 % Mo, Rest Eisen sowie üblichen verschmelzungsbedingten Verumeinigungen nach einer Abkühlung aus der Walzwärme und Ausbildung eines bainitischen Grundgefüges einer Zugfestigkeit von ungefähr 1100 N/mm2 zunächst einer Vorbehandlungsstufe unterzogen wird, indem der Stahl mit der bainitischen Grundstruktur auf eine Temperatur T4 mit 400 °C < T4 < 550 °C erwärmt und sodann gesteuert derart abgekühlt wird, dass der Stahl nach der Vorbehandlung eine Zugfestigkeit von zumindest 1200 N/mm2 aufweist, sodann auf eine Temperatur T1 mit 750 °C < T1 < 920 °C angewärmt, anschließend auf eine Temperatur T2 mit 450 °C < T2 < 250 °C in einem Polymer-Wassergemisch, in einer Salzschmelze oder in einem Pulver beschleunigt abgekühlt, erneut auf eine Temperatur T3 > T2 mit 400 °C < T3 < 560 °C erwärmt und bei der Temperatur T3 über eine Zeit t1 mit 60 min < t1 < 150 min gehalten und anschließend auf Raumtemperatur abgekühlt wird.The present invention is based on the problem of further developing a method for producing a track part of the type mentioned at the outset or a switch component itself in such a way that high strength and yield strength are obtained with an increase in the service life, so that it can be used in particular in high-stress switches. In terms of the method, the problem is solved in that steel undergoes a chemical directional analysis with 0.3 to 0.6% C, 0.8 to 1.5% Si, 0.7 to 1.0% Mn, 0.9 to 1.4 % Cr, 0.6 to 1.0% Mo, remainder iron and usual fusion-related combinations after cooling from the rolling heat and formation of a bainitic basic structure with a tensile strength of approximately 1100 N / mm 2 is first subjected to a pretreatment step by the steel with the bainitic basic structure is heated to a temperature T 4 with 400 ° C. <T 4 <550 ° C. and is then cooled in a controlled manner in such a way that the steel has a tensile strength of at least 1200 N / mm 2 after the pretreatment, and then to a temperature T 1 750 ° C <T 1 <920 ° C heated, then accelerated to a temperature T 2 with 450 ° C <T 2 <250 ° C in a polymer-water mixture, in a molten salt or in a powder, again to a temperature T. 3 > T 2 with 400 ° C <T 3 <560 ° C t and kept at temperature T 3 for a time t 1 with 60 min <t 1 <150 min and then cooled to room temperature.

Besonders gute Ergebnisse lassen sich dann erzielen, wenn der Stahl nach Erreichen der Temperatur T1 in seinem Kern über einen Zeitraum t2 mit 10 min < t2 < 30 min, insbesondere t2 in etwa 20 min gehalten wird.Particularly good results can be achieved if the steel is held in its core over a period t 2 with 10 min <t 2 <30 min, in particular t 2, in about 20 min after the temperature T 1 has been reached.

Insbesondere ist vorgesehen, dass der StahI nach einer gezielten Abkühlung aus der Walzwärme und Ausbildung des bainitischen Grundgefüges einer Zugfestigkeit von ungefähr 1100 N/mm2 auf eine Temperatur T1 von insbesondere in etwa 860 °C angewärmt wird, um anschließend den Stahl beschleunigt auf die Temperatur T2 abzukühlen und einem Kühlmedium auszusetzen, so dass der Stahl in seinem Kern auf die Temperatur T2 abgekühlt ist.In particular, it is provided that the steel is heated to a temperature T 1 of in particular approximately 860 ° C. after a specific cooling from the rolling heat and formation of the basic bainitic structure with a tensile strength of approximately 1100 N / mm 2 , in order to subsequently accelerate the steel to the Cool the temperature T 2 and expose it to a cooling medium so that the core of the steel has cooled to the temperature T 2 .

Des Weiteren ist vorgesehen, dass der Stahl mit bainitischem Grundgefüge mit üblichen Schienenstählen wie 900 A und S 1100 durch Abbrennstumpfschweißen verbunden werden kann, wobei die verbundenen, Gleisteile nachfolgend einer gemeinsamen Wärmebehandlung unterzogen werden können.Furthermore, it is envisaged that the steel with a bainitic basic structure with usual Rail steels such as 900 A and S 1100 connected by flash butt welding can be, the connected, track parts following a common Can be subjected to heat treatment.

Erfindungsgemäß erfolgt eine Volumenvergütung eines Stahl bainitischer Grundstruktur, wobei sich durch gezielte Wärmebehandlung Zugfestigkeiten bis ohne Weiteres 1700 N/mm2, Streckgrenzen (technische Streckgrenzen mit 0,2 % bleibender Dehnung) bis 1400 N/mm2, Bruchdehnung A5 (%) von mehr als 10 und Einschnürungen von mehr als 25 % ergeben. According to the invention, the volume of a steel bainitic basic structure is tempered, with targeted heat treatment allowing tensile strengths of up to 1700 N / mm 2 , yield strengths (technical yield strengths with 0.2% permanent elongation) to 1400 N / mm 2 , elongation at break A 5 (%) result in more than 10 and constrictions of more than 25%.

Ein Weichenbauteil aus Stahl, hergestellt nach zuvor geschildertem Verfahren, zeichnet sich dadurch aus, dass das Gleisteil aus Stahl einer chemischen Richtanalyse mit 0,3 bis 0,6 % C, 0,8 bis 1,5 % Si, 0,7 bis 1,0 % Mn, 0,9 bis 1,4 % Cr, 0,6 bis 1,0 % Mo, Rest Eisen sowie üblichen verschmelzungsbedingten Verunreinigungen hergestellt ist, ein bainitisches Grundgefüge, eine Zugfestigkeit von mehr als 1600 N/mm2 und einer technische Streckgrenze von mehr als 1250 N/mm2 eine Bruchdehnung > 10 % und eine Einschnürung > 25 % aufweist.A switch component made of steel, manufactured according to the previously described method, is characterized in that the track part made of steel is subjected to a chemical directional analysis with 0.3 to 0.6% C, 0.8 to 1.5% Si, 0.7 to 1 , 0% Mn, 0.9 to 1.4 % Cr, 0.6 to 1.0% Mo, remainder iron as well as usual fusion-related impurities, a bainitic basic structure, a tensile strength of more than 1600 N / mm 2 and one technical yield strength of more than 1250 N / mm 2 has an elongation at break> 10% and a constriction> 25%.

Insbesondere weist der Stahl eine chemische Richtanalyse von 0,4 bis 0,5 % C, in etwa 1 % Si, in etwa 0,8 % Mn, in etwa 1,0 % Cr und 0,6 bis 1,0 % Mo auf, wobei die Festigkeit bis 1700 N/mm2 und die Streckgrenze bis 1400 N/mm2 beträgt. Dabei ist der Stahl derart wärmebehandelt, dass die Bruchdehnung > 10 % und die Einschnürung> 25 % beträgt.In particular, the steel has a chemical directional analysis of 0.4 to 0.5% C, approximately 1% Si, approximately 0.8% Mn, approximately 1.0% Cr and 0.6 to 1.0% Mo , where the strength is up to 1700 N / mm 2 and the yield strength is up to 1400 N / mm 2 . The steel is heat-treated in such a way that the elongation at break is> 10% and the constriction is> 25%.

Weitere Einzelheiten, Vorteile und Merkmale der Erfindung ergehen sich nicht nur aus den Ansprüchen, den diesen zu entnehmenden Merkmalen - für sich und/oder in Kombination -, sondern auch ans der nachfolgenden Beschreibung von Ausführungsbeispielen.Further details, advantages and features of the invention are not only apparent the claims, the features to be extracted from them - for themselves and / or in Combination - but also to the following description of exemplary embodiments.

Die Erfindung wird nachstehend anhand eines Beispiels näher erläutert.The invention is explained in more detail below using an example.

Ein Stahl mit einer chemischen Richtanalyse von 0,45 % C, 1 % Si, 0,8 % Mn, 1 % Cr, 0,8 % Mo, Rest Eisen sowie üblichen verschmelzungsbedingten Verunreinigungen wird durch Walzen zu einem Gleisteil geformt, um durch gezieltes Abkühlen aus der Walzwärme ein Gefüge mit bainitischer Grundstruktur und einer Festigkeit von in etwa 1100 N/mm2 zu erzielen. Sodann wird das auf Raumtemperatur abgekühlte Weichenbauteil in einem Wärmebehandlungsofen auf eine Temperatur von in etwa 500 °C erwärmt, um durch anschließendes erneutes gesteuertes Abkühlen eine Festigkeit von 1300 bis 1400 N/mm2 zu erreichen. Sodann wird das Weichenbauteil auf ca. 860 °C angewärmt. Nach Erreichen dieser Temperatur im Kern des Weichenbauteils erfolgt eine beschleunigte Abkühlung in einem Polymer-Wassergemisch auf in etwa 350 °C. Nach Erreichen dieser Temperatur im Kern des Weichenbauteils erfolgt wiederum ein. Erwärmen auf in etwa 450 °C, wobei das Weichenbauteil bei dieser Temperatur über einen Zeitraum von in etwa 2 h gehalten wird. Durch diese Wärmebehandlung ergibt sich ein feinnadliges bainitisches Gefüge mit nachfolgenden Eigenschaften: Zugfestigkeit ca. 1680 N/mm2, technische Streckgrenze ca. 1350 N/mm2, Bruchdehnung > 10 %, Einschnürung > 25 %. A steel with a chemical directional analysis of 0.45% C, 1% Si, 0.8% Mn, 1% Cr, 0.8% Mo, remainder iron as well as usual fusion-related impurities is formed into a track part by rolling in order to be controlled Cooling from the rolling heat to achieve a structure with a bainitic basic structure and a strength of approximately 1100 N / mm 2 . The switch component cooled to room temperature is then heated in a heat treatment furnace to a temperature of approximately 500 ° C. in order to achieve a strength of 1300 to 1400 N / mm 2 by subsequent controlled cooling. The switch component is then heated to approx. 860 ° C. After reaching this temperature in the core of the switch component, the polymer-water mixture cools down to about 350 ° C. After this temperature in the core of the switch component has been reached, Heating to approximately 450 ° C., the switch component being held at this temperature for a period of approximately 2 hours. This heat treatment results in a fine-needle bainitic structure with the following properties: tensile strenght approx. 1680 N / mm 2 , technical yield strength approx. 1350 N / mm 2 , Elongation at break > 10%, Constriction > 25%.

Ein entsprechendes Weichenbauteil ist sodarm mit einer Schiene der Güte UIC 900 A bzw. UIC S 1100 durch Abbrennstumpfschweißen verbunden und in einem Gleis eingebaut worden. Regelmäßige Überprüfungen ergaben eine hohe Verschleißfestigkeit, die im Vergleich zu üblichen Weichenbauteilen eine Erhöhung der Standfestigkeit von in etwa 50 % zeigten.A corresponding switch component is sodarm with a UIC 900 A rail or UIC S 1100 connected by flash butt welding and in a track been installed. Regular checks showed a high wear resistance, which, compared to conventional switch components, increase the stability of showed in about 50%.

Zu erwähnen ist, dass es sich bei dem erneuten Anwärmen auf ca. 860 °C und der sodann beschriebenen Verfahrensschritte um bevorzugte Maßnahmen handelt.It should be mentioned that when it is warmed up again to approx. 860 ° C and the then described method steps are preferred measures.

Claims (8)

  1. A process for manufacture of a high-strength track section of steel, in particular of a switch section such as a frog, tongue rail or wing rail,
    wherein
    steel with a chemical orientation analysis of 0.3 to 0,6 % C, 0,8 to 1,5 % Si, 0,7 to 1,0 % Mn, 0,9 to 1,4 % Cr, 0,6 to 1,0 % Mo, remainder iron and usual smelting-related impurities, is after cooling from the rolling heat and formation of a bainitic basic structure with a tensile strength of approx. 1100 N/mm2, first subjected to a pretreatment stage in that the steel with the bainitic basic structure is heated to a temperature T4 of 400°C <T4 < 550°C and then cooled in controlled form in such a way that the steel has after the pretreatment a tensile strength of at least 1200 N/mm2, then heated to a temperature T1 with 750°C < T1 < 920°C, then cooled in accelerated form to a temperature T2 with 450°C < T2 < 250°C in a polymer/water mixture, in molten salt or in a powder, then heated up again to a temperature T3 > T2 with 400°C < T3 < 560°C, kept at the temperature T3 for a time t1 of 60 mins. < t1 < 150 mins., and then cooled to room temperature.
  2. Process according to Claim 1,
    wherein
    the steel with bainitic basic structure can be cooled from the temperature T1 to the temperature T2 preferably in an aluminum sump.
  3. Process according to Claim 1 or Claim 2,
    wherein
    the steel after reaching the temperature T1 at its core is kept there over a period t2 with 10 mins. < t2 < 30 mins., in particular t2 in approx. 20 mins.
  4. Process according to at least one of the preceding claims,
    wherein
    the steel is heated to a temperature T1 of in particular around 860°C, and wherein the steel is then cooled in accelerated form to the temperature T2 and subjected to a cooling medium such that the steel is cooled at its core to the temperature T2.
  5. Process according to at least one of the preceding claims,
    wherein
    the steel is cooled in controlled form in the pretreatment stage in such a way that the steel has after the pretreatment a tensile strength of between 1300 N/mm2 and 1400 N/mm2.
  6. Process according to at least one of the preceding claims,
    wherein
    the steel with bainitic basic structure is connected to standard rail steels such as 900 A and S 1100 by flash-butt welding, with the joined track sections then being subjected to a joint heat treatment.
  7. Switch section of steel manufactured according to a process according to at least Claim 1,
    wherein
    the track section is made of steel with a chemical orientation analysis of 0,3 to 0,6 % C, 0,8 to 1,5 % Si, 0,7 to 1,0 % Mn, 0,9 to 1,4 % Cr, 0,6 to 1,0% Mo, remainder iron and usual smelting-related impurities, and has a bainitic basic structure, a tensile strength of more than 1600 N/mm2, a technical yield strength of more than 1250 N/mm2, a breaking elongation > 10% and a constriction > 25%.
  8. Switch section according to Claim 6,
    wherein
    the track section is manufactured from steel with a chemical orientation analysis of 0,4 to 0,5 % C, around 1 % Si, around 0,8 % Mn, around 1,0 % Cr, and 0,6 to 1,0 % Mo, remainder iron and usual smelting-related impurities, and has a tensile strength of up to 1700 N/mm2 and a technical yield strength of up to 1400 N/mm2.
EP98943853A 1997-08-14 1998-08-06 Method for producing a high-strength track element and track element thus obtained Expired - Lifetime EP1003920B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19735285A DE19735285C2 (en) 1997-08-14 1997-08-14 Process for the production of a track part
DE19735285 1997-08-14
PCT/EP1998/004894 WO1999009222A1 (en) 1997-08-14 1998-08-06 Method for producing a high-strength track element and track element thus obtained

Publications (2)

Publication Number Publication Date
EP1003920A1 EP1003920A1 (en) 2000-05-31
EP1003920B1 true EP1003920B1 (en) 2001-12-05

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EP98943853A Expired - Lifetime EP1003920B1 (en) 1997-08-14 1998-08-06 Method for producing a high-strength track element and track element thus obtained

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US (1) US6315844B1 (en)
EP (1) EP1003920B1 (en)
AT (1) ATE210197T1 (en)
AU (1) AU736649B2 (en)
DE (2) DE19735285C2 (en)
DK (1) DK1003920T3 (en)
ES (1) ES2169547T3 (en)
NO (1) NO20000707D0 (en)
PL (1) PL189758B1 (en)
PT (1) PT1003920E (en)
WO (1) WO1999009222A1 (en)

Cited By (1)

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Publication number Priority date Publication date Assignee Title
DE102011014877A1 (en) 2011-03-23 2012-09-27 Db Netz Ag Method of re-forging a track part and track parts re-covered according to this method

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DE10313957A1 (en) * 2002-06-27 2004-01-22 Bwg Gmbh & Co. Kg Method for coating a surface of a track component and track component
DE102004048751B3 (en) * 2004-08-11 2005-12-29 Schreck-Mieves Gmbh Tongue rail structure, e.g. for urban tramways, has a cheek rail as a machined base block of wear-resistant heat treatable steel welded to a base plate with a sliding seat for a tongue rail
KR20140119153A (en) * 2012-01-25 2014-10-08 타타 스틸 유케이 리미티드 Steel for producing parts for railway, railway crossings and switches and method for producing said parts
CN103898310B (en) * 2014-04-04 2016-08-10 攀钢集团攀枝花钢铁研究院有限公司 A kind of post weld heat treatment method of bainite rail welding point

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DE1239110B (en) * 1965-10-02 1967-04-20 Kloeckner Werke Ag Use of a highly wear-resistant rail steel alloy
JPH0730401B2 (en) * 1986-11-17 1995-04-05 日本鋼管株式会社 Method for producing high strength rail with excellent toughness
DE4200545A1 (en) * 1992-01-11 1993-07-15 Butzbacher Weichenbau Gmbh TRACK PARTS AND METHOD FOR THE PRODUCTION THEREOF
AU663023B2 (en) * 1993-02-26 1995-09-21 Nippon Steel Corporation Process for manufacturing high-strength bainitic steel rails with excellent rolling-contact fatigue resistance
GB2297094B (en) 1995-01-20 1998-09-23 British Steel Plc Improvements in and relating to Carbide-Free Bainitic Steels
DE19621018C1 (en) * 1996-05-24 1997-10-16 Butzbacher Weichenbau Gmbh Rail track component e.g. frog with layered structure
AT407057B (en) * 1996-12-19 2000-12-27 Voest Alpine Schienen Gmbh PROFILED ROLLING MATERIAL AND METHOD FOR THE PRODUCTION THEREOF

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102011014877A1 (en) 2011-03-23 2012-09-27 Db Netz Ag Method of re-forging a track part and track parts re-covered according to this method
WO2012126550A1 (en) 2011-03-23 2012-09-27 Db Netz Ag Method for forming a rail track component by forging and rail track components forged by means of said method

Also Published As

Publication number Publication date
DE59802362D1 (en) 2002-01-17
PT1003920E (en) 2002-05-31
PL338544A1 (en) 2000-11-06
DE19735285A1 (en) 1999-02-18
NO20000707L (en) 2000-02-11
DE19735285C2 (en) 2001-08-23
EP1003920A1 (en) 2000-05-31
AU9159598A (en) 1999-03-08
WO1999009222A1 (en) 1999-02-25
NO20000707D0 (en) 2000-02-11
US6315844B1 (en) 2001-11-13
PL189758B1 (en) 2005-09-30
ES2169547T3 (en) 2002-07-01
DK1003920T3 (en) 2002-04-02
AU736649B2 (en) 2001-08-02
ATE210197T1 (en) 2001-12-15

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