EP1538231A1 - A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue - Google Patents

A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue Download PDF

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Publication number
EP1538231A1
EP1538231A1 EP04016413A EP04016413A EP1538231A1 EP 1538231 A1 EP1538231 A1 EP 1538231A1 EP 04016413 A EP04016413 A EP 04016413A EP 04016413 A EP04016413 A EP 04016413A EP 1538231 A1 EP1538231 A1 EP 1538231A1
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EP
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Prior art keywords
weight
quantities
comprised
temperature
fatigue
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Application number
EP04016413A
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German (de)
French (fr)
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EP1538231B1 (en
Inventor
Stefano Cantini
Andrea Ghidini
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Lucchini Rs SpA
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LUCCHINI SIDERMECCANICA SpA
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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 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.
  • 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.
  • trace elements in well defined ratios among them and compared with the other steel elements helps the steel hardening and protects its toughness.
  • These trace elements with microalloying properties are Nb, Zr, Al and Ti in quantities not higher than 0.06% by weight and B, Ca and N in quantities not higher than 0.007% by weight.
  • the object of the present invention is a microalloy bainitic steel with high resistance to fatigue and to fretting fatigue containing:
  • the steel 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 weight 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.
  • the rail wheels thus obtained had the following average mechanical features: ROLLING SURFACE 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

Abstract

A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue comprising:
  • C in quantities comprised between 0.15 and 0.35% by weight;
  • Si and Mn in quantities comprised between 0.50 and 1.50% by weight for each element;
  • Cr, Ni and Mo in quantities comprised between 0.10 and 1.00% by weight for each element and,
  • small quantities of trace elements with microalloying properties.

Description

    Field of the invention
  • The present invention refers to a microalloy bainitic steel with high resistance to fatigue and to fretting fatigue.
  • More particularly, 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 wheels for railway, tramway and/or metro fields.
    • Description of the prior art
  • It is known that the wheel is one of the most important components making the rolling stock. During the running of the vehicle, the wheel is submitted to complex phenomena such as ratchetting, fretting fatigue wear friction, etc. intervening on the wheel/rail interface. In fact, during the wheel/rail contact on a thin layer of material placed immediately under the contact area, 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.
  • According to the working conditions, fretting fatigue failures can be spallings due to ratchetting phenomena or to heat loads or spallings due to shellings or deep shellings.
  • In the first case, 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.
  • In the second case, 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.
  • Steels with high resistance levels are known on the market, they successfully remove the drawbacks due to wearing phenomena, but the problems connected to fretting fatigue failures which constitute an ever higher percentage of the damage phenomena of wheels and rails are still present.
    • Summary of the invention
  • The object of the present invention is to remove the above-mentioned drawbacks.
  • More particularly, 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.
  • According to the present invention these and other objects, that will be clear from the following description, are obtained by a steel comprising:
    • C in quantities comprised between 0.15 and 0.35% by weight for each element;
    • Si and Mn in quantities comprised between 0.50 and 1.50% by weight for each element;
    • Cr, Ni and Mo in quantities comprised between 0.10 and 1.00% by weight for each element, and
    • small quantities of trace elements with microalloying properties.
  • The presence of these trace elements in well defined ratios among them and compared with the other steel elements helps the steel hardening and protects its toughness. These trace elements with microalloying properties are Nb, Zr, Al and Ti in quantities not higher than 0.06% by weight and B, Ca and N in quantities not higher than 0.007% by weight.
  • Therefore, the object of the present invention is a microalloy bainitic steel with high resistance to fatigue and to fretting fatigue containing:
    • C in quantities comprised between 0.15 and 0.35% by weight;
    • Si and Mn in quantities comprised between 0.50 and 1.50% by weight for each element;
    • Cr, Ni and Mo in quantities comprised between 0.10 and 1.00% by weight for each element;
    • 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;
    • The remaining part up to 100 being Fe without impurities.
  • The steel 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 weight
    Nitrogen 0.003 - 0.007% by weight
  • The remaining part up to 100 being iron without impurities.
  • After the mechanical machining of the steel of the present invention for the manufacturing of wheels for the railway, tramway and/or metro fields, 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.
  • A clear demonstration of said feature balancing is due to the fact that the ductile/brittle transition temperature, defined by the F.A.T.T. value corresponding to 50% is placed at - 40°C even though the tensile stress values are very high.
  • In order to better understand the present invention and put it into practice the following illustrative and non limitative example is given.
    • Example
  • 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.
  • With the steels thus obtained some rail wheels have been manufactured according to the prior arts each of them having a rolling diameter of 915 mm.
  • 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.
  • The rail wheels thus obtained had the following average mechanical features:
    ROLLING SURFACE
    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

Claims (9)

  1. A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue comprising:
    C in quantities comprised between 0.15 and 0.35% by weight
    Si and Mn in quantities comprised between 0.50 and 1.50% by weight for each element;
    Cr, Ni and Mo in quantities comprised between 0.10 and 1.00% by weight for each element and,
    small quantities of trace elements with microalloying properties.
  2. The steel according to claim 1, characterized in that the trace elements with microalloying properties are Nb, Zr, Al and Ti in quantities not higher than 0.06% by weight and B, Ca and N in quantities not higher than 0.007% by weight.
  3. The steel according to claims 1 or 2 characterized in that it contains:
    C in quantities comprised between 0.15 and 0.35% by weight
    Si and Mn in quantities comprised between 0.50 and 1.50% by weight for each element;
    Cr, Ni and Mo in quantities comprised between 0.10 and 1.00% by weight for each element;
    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;
    the remaining part up to 100 being Fe without impurities.
  4. The steel according to any of the previous claims, characterized in that it contains: 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 weight Nitrogen 0.003 - 0.007% by weight
    The remaining part up to 100 being iron without impurities.
  5. A method for the manufacturing of wheels for the railway, tramway and/or metro fields with high resistance to fatigue and fretting fatigue, characterized in that it consists in manufacturing the wheel by mechanical machining of the steel of any of the previous claims and in submitting it to an austenitization and quenching in water and subsequently to two thermal tempering processes.
  6. The method according to claim 5, characterized in that the austenitization and quenching in water consists in a heating at a temperature comprised between 850°C and 950°C in a stay at such a 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.
  7. The method according to claim 5 or 6, characterized in that the first thermal tempering process consists in a heating at a variable temperature comprised between 500 and 700°C according to the required features, a stay at this temperature for about one hour for each 20 mm of thickness of the processed product and a spontaneous air cooling until room temperature is reached.
  8. The method according to any of the previous claims from 5 to 7, characterized in that the second thermal tempering treatment 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.
  9. The method according to claim 8, characterized in that the cooling of the wheel rolling is carried out at a different speed from the one used for the cooling of the web.
EP04016413A 2003-12-03 2004-07-13 A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue Not-in-force EP1538231B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL04016413T PL1538231T3 (en) 2003-12-03 2004-07-13 A microalloy bainitic steel with high resistance to fatigue and to fretting fatigue

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
IT002370A ITMI20032370A1 (en) 2003-12-03 2003-12-03 HIGH BAINITH MICROLEGATE STEEL FOR FATIGUE RESISTANCE
ITMI20032370 2003-12-03

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EP1538231A1 true EP1538231A1 (en) 2005-06-08
EP1538231B1 EP1538231B1 (en) 2010-08-25

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EP (1) EP1538231B1 (en)
AT (1) ATE478970T1 (en)
DE (1) DE602004028791D1 (en)
ES (1) ES2350204T3 (en)
IT (1) ITMI20032370A1 (en)
PL (1) PL1538231T3 (en)

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CN100374606C (en) * 2005-07-30 2008-03-12 马鞍山钢铁股份有限公司 Medium carbon low alloy steel for light high speed train wheel
WO2008154680A1 (en) * 2007-06-19 2008-12-24 Qr Limited Treatment of railway wheels
DE112008001181B4 (en) * 2007-05-16 2012-01-12 Benteler Deutschland Gmbh Use of a steel alloy for axle tubes and axle tube
CN104975229A (en) * 2015-06-15 2015-10-14 柳州金特新型耐磨材料股份有限公司 Gear sleeve
EP3460089A4 (en) * 2016-07-06 2019-07-24 Magang (Group) Holding Co., Ltd. Low cost lean production bainitic steel wheel for rail transit, and manufacturing method therefor
EP3483298A4 (en) * 2016-07-06 2019-07-24 Magang (Group) Holding Co., Ltd. High toughness bainitic steel wheel for rail transit, and manufacturing method therefor
WO2019229693A1 (en) * 2018-05-30 2019-12-05 Rail 1520 Ip Ltd Alloyed cast stell and article made therefrom
CN113186446A (en) * 2021-04-02 2021-07-30 甘肃酒钢集团宏兴钢铁股份有限公司 Process for controlling pearlite morphology and carbon-nitrogen compound precipitation of microalloyed medium plate

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CN104325838B (en) * 2014-10-22 2016-08-24 雷帮荣 A kind of high ferro wheel and hot extrusion integral forming method thereof

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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
GB1417330A (en) * 1972-03-02 1975-12-10 Italsider Spa Method for manufacturing steel monobloc wheels
US5518685A (en) * 1994-02-03 1996-05-21 Mitsubishi Steel Mfg. Co., Ltd. Steel for carburized gear
US5533770A (en) * 1992-10-10 1996-07-09 Man Gutehoffnungshutte Aktiengesellschaft High-strength solid wheels and tires for railroad traction vehicles and cars
EP0884396A1 (en) * 1997-05-23 1998-12-16 Valdunes Method for manufacturing a railway wheel and railway wheel so obtained
EP1241277A2 (en) * 2001-03-05 2002-09-18 AMSTED Industries Incorporated Railway wheel alloy

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2166585A5 (en) * 1971-12-30 1973-08-17 Creusot Loire Steel alloy - for use in pressurised hydrogen or during hydrogen production
GB1417330A (en) * 1972-03-02 1975-12-10 Italsider Spa Method for manufacturing steel monobloc wheels
US5533770A (en) * 1992-10-10 1996-07-09 Man Gutehoffnungshutte Aktiengesellschaft High-strength solid wheels and tires for railroad traction vehicles and cars
US5518685A (en) * 1994-02-03 1996-05-21 Mitsubishi Steel Mfg. Co., Ltd. Steel for carburized gear
EP0884396A1 (en) * 1997-05-23 1998-12-16 Valdunes Method for manufacturing a railway wheel and railway wheel so obtained
EP1241277A2 (en) * 2001-03-05 2002-09-18 AMSTED Industries Incorporated Railway wheel alloy

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100374606C (en) * 2005-07-30 2008-03-12 马鞍山钢铁股份有限公司 Medium carbon low alloy steel for light high speed train wheel
DE112008001181B4 (en) * 2007-05-16 2012-01-12 Benteler Deutschland Gmbh Use of a steel alloy for axle tubes and axle tube
WO2008154680A1 (en) * 2007-06-19 2008-12-24 Qr Limited Treatment of railway wheels
CN101821414B (en) * 2007-06-19 2013-07-17 昆士兰铁路有限公司 Treatment of railway wheels
AU2008265498B2 (en) * 2007-06-19 2013-10-31 Asciano Services Pty Ltd Treatment of railway wheels
CN104975229A (en) * 2015-06-15 2015-10-14 柳州金特新型耐磨材料股份有限公司 Gear sleeve
EP3460089A4 (en) * 2016-07-06 2019-07-24 Magang (Group) Holding Co., Ltd. Low cost lean production bainitic steel wheel for rail transit, and manufacturing method therefor
EP3483298A4 (en) * 2016-07-06 2019-07-24 Magang (Group) Holding Co., Ltd. High toughness bainitic steel wheel for rail transit, and manufacturing method therefor
WO2019229693A1 (en) * 2018-05-30 2019-12-05 Rail 1520 Ip Ltd Alloyed cast stell and article made therefrom
CN113186446A (en) * 2021-04-02 2021-07-30 甘肃酒钢集团宏兴钢铁股份有限公司 Process for controlling pearlite morphology and carbon-nitrogen compound precipitation of microalloyed medium plate

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ITMI20032370A1 (en) 2005-06-04
ATE478970T1 (en) 2010-09-15

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