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EP1538231B1 - Mikrolegierter bainitischer Stahl mit hoher Ermüdungsfestigkeit - Google Patents

Mikrolegierter bainitischer Stahl mit hoher Ermüdungsfestigkeit Download PDF

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Publication number
EP1538231B1
EP1538231B1 EP04016413A EP04016413A EP1538231B1 EP 1538231 B1 EP1538231 B1 EP 1538231B1 EP 04016413 A EP04016413 A EP 04016413A EP 04016413 A EP04016413 A EP 04016413A EP 1538231 B1 EP1538231 B1 EP 1538231B1
Authority
EP
European Patent Office
Prior art keywords
amount
temperature
comprised
fatigue
wheel
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.)
Expired - Lifetime
Application number
EP04016413A
Other languages
English (en)
French (fr)
Other versions
EP1538231A1 (de
Inventor
Stefano Cantini
Andrea Ghidini
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.)
Lucchini Rs SpA
Original Assignee
Lucchini RS SpA
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 Lucchini RS SpA filed Critical Lucchini RS SpA
Priority to PL04016413T priority Critical patent/PL1538231T3/pl
Publication of EP1538231A1 publication Critical patent/EP1538231A1/de
Application granted granted Critical
Publication of EP1538231B1 publication Critical patent/EP1538231B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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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
    • C22C38/18—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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/34—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tyres; for rims
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/78—Combined heat-treatments not provided for above
    • 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 present invention refers to a microalloy bainitic steel with high resistance to fatigue and to fretting fatigue.
  • the present invention refers to a microalloy bainitic steel with high resistance to fatigue and to fretting fatigue being particularly suitable to be used for the manufacturing of rail wheels, i.e. wheels for railway, tramway and/or metro fields.
  • the wheel is one of the most important components making the rolling stock.
  • the wheel is submitted to complex phenomena such as ratchetting, fretting fatigue wear friction, etc. intervening on the wheel/rail interface.
  • complex phenomena such as ratchetting, fretting fatigue wear friction, etc. intervening on the wheel/rail interface.
  • great stresses occur due to the severe load conditions. These stresses give rise both to the first stages of fretting fatigue failures and to wearing.
  • Fatigue failures are very dangerous as they can cause the detachment of small portions of wheel, with serious consequences both on suspensions, on the axle-box bearings of the vehicle and on the railway infrastructure.
  • fretting fatigue failures can be spallings due to ratchetting phenomena or to heat loads or spallings due to shellings or deep shellings.
  • spallings are induced by cold ratchetting. It is known that the wheel/rail contact develops in cyclic elastic-plastic conditions with localized ratchetting and the sum of ratchetting deriving from various cycles may give rise to local failures for damage accumulation.
  • spallings are due to the detachment of small portions of wheels with cratering forming on the rolling surface in conditions of high axle loads or in the presence of macrodefects at depths comprised between 6 and 30 mm under the rolling surface.
  • EP-A-1 241 277 on which is based the preamble of claim 1, discloses a steel alloy, particularly for railway wheels, comprising carbon, silicon, manganese as alloying elements imparting hardness, and chromium, nickel, molybdenum, as alloying elements improving the tempering properties, but no elements with microalloying properties.
  • Both FR-A-2 166 585 and EP-A-0 884 396 disclose the manufacturing of a steel alloy comprising carbon, silicon, manganese as alloying elements imparting hardness, and chromium, nickel, molybdenum, as alloying elements improving the tempering properties, the former document additionally disclosing the use of V in the composition.
  • EP 0612852 discloses a process for manufacturing high-strength bainitic steel rails with excellent rolling contact fatigue resistance, the steel comprising carbon, silicon, manganese and chromium, and optionally at least one element selected from three groups of elements, namely Ni, Mo, Cu; Nb, V, Ti; B.
  • the object of the present invention is to remove the above-mentioned drawbacks.
  • the object of the present invention is to provide a steel suitable for the manufacturing of wheels for the railway, tramway and/or metro fields having a high resistance to fretting fatigue failures.
  • a further object of the present invention is to provide a steel suitable for the manufacturing of wheels for the railway, tramway and/or metro fields having high mechanical resistance and toughness features combined with high resistance features to wearing and fretting fatigue.
  • microalloying elements in well defined ratios among them and compared with the other steel elements helps the steel hardening and protects its toughness.
  • These elements with microalloying properties are Nb, Zr, Al and Ti in quantities not higher than 0.06% by weight for each element and B, Ca and N in quantities not higher than 0.007% by weight, for each element.
  • a steel according to an embodiment of the present invention preferably comprises: Carbon 0.15 - 0.35% by weight Silicon 0.60 - 1.20% by weight Manganese 0.60 - 1.50% by weight Chromium 0.10 - 1.00% by weight Nickel 0.10 - 1.00% by weight Molybdenum 0.10 - 0.90% by weight Vanadium 0.01 - 0.15% by weight Niobium 0.01 - 0.05% by weight Zirconium 0.005 - 0.06% by weight Aluminium 0.005 - 0.06% by weight Titanium 0.005 - 0.06% by weight Boron 0.0005 - 0.005% by weight Calcium 0.0002 - 0.005% by weigh Nitrogen 0.003 - 0.007% by weight
  • the remaining part up to 100 being iron without impurities.
  • the product is submitted to austenitization and quenching in water.
  • This process consists in the heating at a temperature comprised between 850 and 950° C, a stay at this temperature for one hour for about each 40 mm of thickness of the processed product and in a quick cooling in water until room temperature is reached.
  • the product is then submitted to two thermal tempering processes in order to attenuate internal stresses caused by the abrupt cooling.
  • the first thermal tempering process is carried out by heating at a variable temperature comprised between 500 and 700°C according to the required features for a stay time at this temperature of about one hour for each 20 mm of thickness of the processed product, followed by a spontaneous air cooling until room temperature is reached.
  • the second thermal tempering process is carried out by heating at a temperature lower than 20°C compared to the one of the first thermal tempering process for a stay time at this temperature of about one hour for each 20 mm of thickness of the processed product followed by a spontaneous air cooling for at least 25 minutes and in any case being such to cool the rail wheel rolling until room temperature is reached.
  • the cooling of the rail wheel rolling can be carried out at a different speed from the one used for the cooling of the web in order to give different properties to each part of the wheel.
  • the steel of the present invention is characterized by an excellent balancing between tensile and toughness features. Toughness values are very high at any temperature level.
  • Some castings have been manufactured according to the following objective analysis: Carbon 0.27 - 0.32% by weight Silicon 0.60 - 0.80% by weight Manganese 0.90 - 1.10% by weight Chromium 0.20 - 0.50% by weight Nickel 0.20 - 0.50% by weight Molybdenum 0.20 - 0.50% by weight Vanadium 0.020 - 0.050% by weight Niobium 0.020 - 0.040% by weight Zirconium 0.015 - 0.045% by weight Aluminium 0.015 -0.055% by weight Titanium 0.010 - 0.040% by weight Boron 0.0010 - 0.040% by weight Calcium 0.002 - 0.003% by weight Nitrogen 0.003 - 0.004% by weight
  • the remaining part up to 100 being iron without impurities.
  • Each wheel has been submitted to austenitization and quenching by heating at a temperature of about 900°C for a stay time at this temperature of about 3 hours and a quick cooling in water until room temperature was reached.
  • Each wheel was then submitted to two subsequent thermal tempering processes the first of which was carried out by heating at a temperature of about 520°C - 600°C for a stay time at this temperature of about six hours and a spontaneous air cooling until room temperature was reached; the second one was carried out by heating at a temperature of 20°C lower than the one of the first process for a stay time at such temperature of about six hours and a spontaneous air cooling for 60 minutes until room temperature was reached.
  • PROPERTIES STANDARD UNIT VALUE Monotonic yield UNI EN10002 Mpa 1,090 Tensile stress UNI EN10002 Mpa 1,210 Elongation at break UNI EN10002 % 16 Reduction coeff. UNI EN 10002 % 55 WEB PROPERTIES STANDARD UNIT VALUE Monotonic yield UNI EN10002 Mpa 1,090 Tensile stress UNI EN10002 Mpa 1,210 Elongation at break UNI EN10002 % 16 Reduction coeff. UNI EN10002 % 55

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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)

Claims (7)

  1. Mikrolegierter bainitischer Stahl für Laufräder mit hoher Ermüdungsfestigkeit und hoher Kontaktermüdungsfestigkeit mit C, Si, Mn, Cr, Ni und Mo.
    dadurch gekennzeichnet enthält die Legierung:
    zwischen 0,15 und 0,35 % C;
    zwischen 0,6 und 1,20 % Si;
    zwischen 0,6 und 1.50 % Mn;
    zwischen 0,10 und 1,00 % Cr;
    zwischen 0,10 und 1,00 % Ni;
    zwischen 0,10 und 0,90 % Mo.
    Außerdem beinhaltet sie die folgenden Mikrolegierungselemente in den nachstehenden Gewichtsanteilen:
    zwischen 0,01 und 0,15 % V;
    jeweils höchstens 0,06 % Nb, Zr, Al und Ti;
    jeweils höchstens 0,007 % B, Ca und N,
    die restlichen Anteile auf 100 % bestehen aus reinem Eisen.
  2. Eine Methode zur Herstellung eines Laufrads mit hoher Ermüdungsfestigkeit und hoher Kontaktermüdungsfestigkeit mit einer Mikrolegierter bainitischer Stahl nach Anspruch 1, umfasst die folgenden Arbeitsschritte:
    mechanische Verarbeitung der oben genannten Stahllegierung;
    Austenitisierung;
    anschließendes Abschrecken in Wasser und
    abschließend zweimaliges Anlassen durch Wärmebehandlung.
  3. Eine Methode nach Anspruch 2, die sich dadurch auszeichnet, dass die genannten Vorgänge der Austenitisierung und des Abschreckens folgende Schritte beinhalten:
    Erhitzen des Rads auf eine Temperatur zwischen 850 C und 950 C;
    Durchwärmung des Rads bei dieser Temperatur für eine Stunde pro 40 mm Stärke des bearbeiteten Erzeugnisses;
    rasche Abkühlung in Wasser bis zur Erreichung der Raumtemperatur.
  4. Eine Methode nach Anspruch 2 oder 3, die sich dadurch auszeichnet, dass der genannte erste Anlassvorgang folgende Schritte beinhaltet:
    das Aufheizen auf eine Temperatur zwischen 500 und 700 C;
    die Durchwärmung des Rads bei dieser Temperatur für eine Stunde pro 20 mm Stärke des bearbeiteten Erzeugnisses
    und die anschließende Luftkühlung bis zur Erreichung der Raumtemperatur.
  5. Eine Methode nach Anspruch 2 oder 3 oder 4, die sich dadurch auszeichnet, dass der genannte zweite Anlassprozess folgende Schritte beinhaltet:
    Erhitzen des Erzeugnisses auf eine Temperatur, die 20 C unter der des ersten Anlassvorgangs liegt;
    Durchwärmung des Rads bei dieser Temperatur für eine Stunde pro 20 mm Stärke des bearbeiteten Erzeugnisses;
    sowie die anschließende Kühlung des Erzeugnisses für mindestens 25 Minuten und in jedem Fall so lange, bis das Wälzlager Raumtemperatur erreicht hat.
  6. Eine Methode nach Anspruch 5, die sich dadurch auszeichnet, dass das Kühlen des Wälzlagers bei einer unterschiedlichen Geschwindigkeit als jener durchgeführt wird, die für das Kühlen der Laufschiene verwendet wird.
  7. Ein Laufrad, das mit einer Mikrolegierter bainitischer Stahl laut Anforderung 1 hergestellt wird.
EP04016413A 2003-12-03 2004-07-13 Mikrolegierter bainitischer Stahl mit hoher Ermüdungsfestigkeit Expired - Lifetime EP1538231B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL04016413T PL1538231T3 (pl) 2003-12-03 2004-07-13 Mikroskopowa stal bainityczna o wysokiej wytrzymałości na zmęczenie i zmęczenie cierno korozyjne

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
IT002370A ITMI20032370A1 (it) 2003-12-03 2003-12-03 Acciaio microlegato bainitico ad elevata resistenza a fatica
ITMI20032370 2003-12-03

Publications (2)

Publication Number Publication Date
EP1538231A1 EP1538231A1 (de) 2005-06-08
EP1538231B1 true EP1538231B1 (de) 2010-08-25

Family

ID=34452266

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04016413A Expired - Lifetime EP1538231B1 (de) 2003-12-03 2004-07-13 Mikrolegierter bainitischer Stahl mit hoher Ermüdungsfestigkeit

Country Status (6)

Country Link
EP (1) EP1538231B1 (de)
AT (1) ATE478970T1 (de)
DE (1) DE602004028791D1 (de)
ES (1) ES2350204T3 (de)
IT (1) ITMI20032370A1 (de)
PL (1) PL1538231T3 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104325838A (zh) * 2014-10-22 2015-02-04 雷帮荣 一种高铁车轮及其热挤压整体成型方法

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100374606C (zh) * 2005-07-30 2008-03-12 马鞍山钢铁股份有限公司 一种轻型高速列车车轮用中碳低合金钢
DE102007023309A1 (de) * 2007-05-16 2008-11-20 Benteler Stahl/Rohr Gmbh Verwendung einer Stahllegierung für Achsrohre sowie Achsrohr aus einer Stahllegierung
CN101821414B (zh) * 2007-06-19 2013-07-17 昆士兰铁路有限公司 铁路车轮的处理
CN104975229A (zh) * 2015-06-15 2015-10-14 柳州金特新型耐磨材料股份有限公司 一种齿套
CN106191666B (zh) * 2016-07-06 2018-01-02 马钢(集团)控股有限公司 一种低成本精节生产的轨道交通用贝氏体钢车轮及其制造方法
CN106048430B (zh) * 2016-07-06 2017-11-03 马钢(集团)控股有限公司 一种高韧性轨道交通用贝氏体钢车轮及其制造方法
EA201891069A1 (ru) * 2018-05-30 2019-12-30 РЕЙЛ 1520 АйПи ЛТД. Легированная литейная сталь и изделие из нее
CN113186446A (zh) * 2021-04-02 2021-07-30 甘肃酒钢集团宏兴钢铁股份有限公司 一种控制微合金化中厚板珠光体形态及碳氮化合物析出的工艺

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FR2166585A5 (en) * 1971-12-30 1973-08-17 Creusot Loire Steel alloy - for use in pressurised hydrogen or during hydrogen production
IT957295B (it) * 1972-03-02 1973-10-10 Italsider Spa Procedimento perfezionato per la realizzazione di ruote monoblocco in acciaio
DE4234192C2 (de) * 1992-10-10 1996-01-11 Gutehoffnungshuette Man Hoch belastbare Vollräder und Radreifen für Schienen-Triebfahrzeuge und Wagen
US5518685A (en) * 1994-02-03 1996-05-21 Mitsubishi Steel Mfg. Co., Ltd. Steel for carburized gear
FR2763601B1 (fr) * 1997-05-23 1999-06-25 Valdunes Procede de fabrication d'une roue de chemin de fer en acier et roue de chemin de fer obtenue
US6783610B2 (en) * 2001-03-05 2004-08-31 Amsted Industries Incorporated Railway wheel alloy

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104325838A (zh) * 2014-10-22 2015-02-04 雷帮荣 一种高铁车轮及其热挤压整体成型方法
CN104325838B (zh) * 2014-10-22 2016-08-24 雷帮荣 一种高铁车轮及其热挤压整体成型方法

Also Published As

Publication number Publication date
ITMI20032370A1 (it) 2005-06-04
ES2350204T3 (es) 2011-01-20
PL1538231T3 (pl) 2011-02-28
EP1538231A1 (de) 2005-06-08
ATE478970T1 (de) 2010-09-15
DE602004028791D1 (de) 2010-10-07

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