WO2014053385A1 - Alliage d'acier - Google Patents

Alliage d'acier Download PDF

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Publication number
WO2014053385A1
WO2014053385A1 PCT/EP2013/070037 EP2013070037W WO2014053385A1 WO 2014053385 A1 WO2014053385 A1 WO 2014053385A1 EP 2013070037 W EP2013070037 W EP 2013070037W WO 2014053385 A1 WO2014053385 A1 WO 2014053385A1
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WO
WIPO (PCT)
Prior art keywords
steel alloy
vanadium
alloy
carbon
composition
Prior art date
Application number
PCT/EP2013/070037
Other languages
English (en)
Inventor
Harshad Kumar Dharamshi Hansraj Bhadeshia
Pedro Eduardo Jose RIVERA-DIAZ-DEL-CASTILLO
Blanka SZOST
Erik VEGTER
Original Assignee
Aktiebolaget Skf
Cambridge Enterprise Limited, The Old Schools
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 Aktiebolaget Skf, Cambridge Enterprise Limited, The Old Schools filed Critical Aktiebolaget Skf
Publication of WO2014053385A1 publication Critical patent/WO2014053385A1/fr

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Classifications

    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • 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
    • C21D9/42—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for armour plate
    • 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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/121—Use of special materials
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/008—Martensite
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/60—Ferrous alloys, e.g. steel alloys
    • F16C2204/66—High carbon steel, i.e. carbon content above 0.8 wt%, e.g. through-hardenable steel
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
    • F16C2240/48—Particle sizes

Definitions

  • the present invention relates generally to the field of metallurgy and to an improved steel alloy and a method of heat-treating an alloy.
  • the steel alloy exhibits resistance to hydrogen embrittlement and good mechanical properties, such as a high hardness.
  • the steel alloy may be used in a number of applications, including, for example, bearings. Background
  • Rolling element bearings are devices that permit constrained relative motion between two parts.
  • Rolling element bearings comprise inner and outer raceways and a plurality of rolling elements (balls or rollers) disposed therebetween.
  • rolling elements balls or rollers
  • the hydrogen concentration should typically not exceed 1 ppm. Even if the hydrogen content is very low in the as-produced steel, its amount is likely to increase during service, for example due to oil decomposition or electric current breaking through the layer of oil, resulting in the decomposition of oil molecules into products including free hydrogen, making its ingress into the bulk possible.
  • Hydrogen embrittlement is likely to occur when the steel contains mobile hydrogen. For this reason it has been proposed to immobilise hydrogen in the alloy microstructure.
  • the steel known as 100Cr6 has the following composition: 0.974 wt% carbon, 0.282 wt% silicon, 0.276 wt% manganese, 0.056 wt% molybdenum, 1.384 wt% chromium, 0.184 wt% nickel, 0.042 wt% aluminium, 0.21 wt% copper, 0.01 wt% phosphorus and 0.017 wt% sulphur, the balance being iron (and any unavoidable impurities).
  • This steel exhibits high hardness and is suitable for use in a bearing component.
  • 100Cr6 exhibits moderate-to-low resistance to hydrogen embrittlement.
  • the present invention provides a steel alloy having a composition comprising: from 0.6 to 1 .2 wt% carbon
  • vanadium optionally one or more of from 0 to 1 . .0 wt% silicon
  • the steel alloy according to the present invention comprises from 0.6 to 1 .2 wt% carbon.
  • the steel alloy composition comprises from 0.8 to 1 .2 wt % carbon, more preferably from 0.9 to 1.1 wt% carbon, even more preferably from 0.95 to 1.05 wt% carbon.
  • the alloy comprises about 0.99 wt% carbon.
  • the presence of carbon in the specified amount may serve to increase the hardness of the steel alloy.
  • the presence of carbon together with vanadium may enable the formation of carbides comprising carbon and vanadium. As discussed below, the presence of such carbides may increase the alloy's resistance to hydrogen embrittlement.
  • the steel alloy comprises from 0.1 to 0.8 wt% manganese, more typically from 0.1 to 0.6 wt% manganese.
  • the alloy comprises from 0.2 to 0.5 wt% manganese, more preferably from 0.2 to 0.4 wt% manganese. In one example, the alloy comprises about 0.28 wt% manganese.
  • the manganese, in combination with the other alloying elements, may increases hardness and may contribute to the steel's strength. Manganese may also have a beneficial effect on surface quality.
  • the steel alloy comprises from 0.5 to 2.5 wt% chromium.
  • the alloy comprises from 1.0 to 2.0 wt% chromium, more preferably from 1.2 to 1.6 wt% chromium.
  • the alloy comprises about 1 .42 wt% chromium.
  • the presence of chromium in the specified amount may provide an improved corrosion resistance property to the steel alloy.
  • the chromium may lead to a hard oxide on the metal surface to inhibit corrosion. Chromium may also have a beneficial effect on hardenability.
  • the steel alloy comprises from 2.5 to 3.5 wt% vanadium.
  • the alloy comprises from 2.5 to 3 wt% vanadium, more preferably from 2.6 to 2.9 wt% vanadium, still more preferably from 2.7 to 2.8 wt% vanadium.
  • the alloy comprises about 2.75 wt% vanadium.
  • vanadium in the specified amounts can provide the steel alloy with increased resistance to hydrogen embrittlement.
  • Vanadium may also act to increase the hardness of the alloy and preferably also the yield strength and/or tensile strength.
  • Vanadium can form carbides, such as, for example, V 4 C 3 . Such carbides, which are preferably nanometre-scaled, may act as hydrogen traps.
  • carbides are believed to provide the steel alloy with increased resistance to hydrogen embrittlement.
  • vanadium in the range of 2.5 to 3.5 wt% may make carbide formation (for example V 4 C 3 ) thermodynamically possible at about 600°C, and may also be beneficial for delaying grain growth during austenitisation.
  • Vanadium levels lower that 2.5 wt% can result in the high temperature formation of cementite.
  • vanadium levels of 2.5 wt% or higher can avoid the formation of cementite at high temperature. This is advantageous since cementite may then be formed at a lower tempering temperature resulting in improved mechanical properties (primarily high hardness).
  • Vanadium levels lower than 2.5 wt% may result in the formation of detrimental carbides such as, for example, M 6 C and M 2 3C 6 .
  • Vanadium levels higher than 3.5 wt% may result in the formation of other undesirable phases.
  • the steel alloy may optionally comprise up to 0.5 wt% copper, for example from 0.1 to 0.5 wt% copper.
  • the alloy comprises from 0.2 to 0.5 wt% copper, still more preferably from 0.2 to 0.4 wt% copper.
  • the alloy comprises about 0.25 wt% copper.
  • the copper may act to provide improved corrosion resistance.
  • the steel alloy may optionally comprise up to 1.0 wt.% silicon, more typically up to 0.5 wt% silicon, for example from 0.1 to 0.5 wt% silicon.
  • the alloy comprises from 0.1 to 0.4 wt% silicon, more preferably from 0.2 to 0.3 wt% silicon.
  • Silicon may be added during the steel making process as a deoxidizer. Silicon may also act to increase strength and hardness.
  • the steel alloy may optionally comprise up to 2 wt% molybdenum, for example from 0.01 to 2 wt% molybdenum.
  • the alloy comprises from 0.01 to 0.3 wt% molybdenum, more preferably from 0.01 to 0.2 wt% molybdenum, even more preferably from 0.05 to 0.1 wt% molybdenum.
  • the alloy comprises about 0.093 wt% molybdenum.
  • molybdenum in the specified amounts may improve the hydrogen-trapping capacity of the steel alloy, possibly owing to more favourable coherency strains. This may provide the steel alloy with increased resistance to hydrogen embrittlement.
  • Molybdenum may also act to increase the hardenability of the alloy.
  • Molybdenum may improve grain boundary cohesion.
  • the steel alloy may optionally comprise up to 3.5 wt% nickel, typically up to 1 wt% nickel, more typically up to 0.1 wt% nickel.
  • the alloy comprises from 0.005 to 0.05 wt% nickel, more preferably from 0.007 to 0.02 wt% nickel. In one example, the alloy comprises about 0.01 wt% nickel. Nickel may act to increase hardenability and impact strength.
  • the steel alloy may optionally comprise up to 0.1 wt% aluminium.
  • the steel alloy comprises from 0.001 to 0.01 wt% aluminium, more preferably from 0.002 to 0.005 wt% aluminium. In one example, the steel alloy comprises about 0.003 wt% aluminium.
  • Aluminium may be used as a deoxidizer. Aluminium may also act to control grain size in the alloy.
  • the steel alloy may optionally comprise up to 0.1 wt% of one or more of titanium, niobium, tantalum, tungsten, boron, nitrogen, calcium and cobalt.
  • oxygen oxygen
  • phosphorus phosphorus
  • sulphur sulphur
  • the content thereof should generally not exceed 0.05 wt%.
  • the phosphorus content will be about 0.004 wt%.
  • sulphur is present, the content should generally not exceed 0.05 wt%.
  • the sulphur content will be about 0.003 wt%.
  • oxygen is present, the content should generally not exceed 0.1 wt%.
  • the oxygen content does not exceed 15 ppm.
  • the steel alloy may contain unavoidable impurities, although, in total, these are unlikely to exceed 0.5 wt.% of the composition.
  • the alloy contains unavoidable impurities in an amount of not more than 0.3 wt.% of the composition, more preferably not more than 0.1 wt.% of the composition.
  • the phosphorus, sulphur and oxygen contents are preferably kept to a minimum.
  • a most preferred steel alloy according to the present invention comprises: about 0.994 wt% carbon
  • the alloys according to the present invention may consist essentially of the recited elements. It will therefore be appreciated that in addition to those elements which are mandatory other non-specified elements may be present in the composition provided that the essential characteristics of the composition are not materially affected by their presence.
  • the alloy typically has a microstructure comprising martensite, optionally cementite, and carbides comprising vanadium and carbon. If the alloy undergoes a tempering heat- treatment, then cementite is present in the final microstructure.
  • the carbides may consist of vanadium and carbon, for example V 4 C 3 , or may include one or more additional alloying elements.
  • carbide as used herein is meant to encompass also, for example, carbo-nitrides and carbo-oxy-nitrides and also mixed metal carbides, carbo-nitrides and carbo-oxy-nitrides.
  • the microstructure typically comprises at least 70 vol. % martensite, more typically at least 75 vol. %.
  • the microstructure comprises from 1 to 5 vol. % carbides (comprising vanadium and carbon) and from 5 to 20 vol. % cementite, the remainder being martensite.
  • the microstructure comprises about 2 vol. % carbides (comprising vanadium and carbon), about 10 vol. % cementite, and the remainder being martensite.
  • the carbide precipitates comprising vanadium and carbon may act as hydrogen traps.
  • the presence of cementite precipitates may impart strength.
  • the cementite precipitates are typically nanometre-sized, preferably having a mean diameter of from 10 to 500 nm.
  • the carbide precipitates comprising vanadium and carbon are advantageously nanometre- sized and, preferably, have a mean diameter of from 1 to 50 nm, more preferably from 1 to 30 nm, even more preferably from 5 to 25 nm. Most preferably, the carbides have a mean diameter of about 10 nm. Carbides having such sizes are particularly effective as hydrogen traps.
  • the structure of the steel alloy described herein can be determined by conventional microstructural characterisation techniques such as, for example, optical microscopy, TEM, SEM, AP-FIM, TDA and X-ray diffraction, including combinations of two or more of these techniques.
  • the present invention provides an engine component or an armour component comprising a steel alloy as defined herein.
  • the material may also be used in marine and aerospace applications, for example gears and shafts.
  • the present invention provides a bearing component comprising a steel alloy as defined herein.
  • the bearing component may be at least one of a rolling element (for example ball or cylinder), an inner ring, and/or an outer ring.
  • the present invention provides a bearing comprising a bearing component as described herein.
  • the present invention provides a method of heat-treating a steel alloy comprising:
  • step (ii) optionally carrying out a tempering heat-treatment following the ageing step (iv).
  • the composition is at least partially austenitised, preferably completely austenitised. This is achieved by heating the alloy composition to a temperature of from 780 to 950°C, preferably from 820 to 900°C, more preferably from 840 to 880°C, and most preferably about 860°C.
  • the composition may be maintained in this temperature regime for up to 30 minutes, preferably from 5 to 20 minutes, even more preferably for about 15 minutes. However, longer heating times are also possible.
  • Step (ii) may result in the formation of vanadium carbides.
  • Step (ii) may result in only minimal formation of cementite.
  • Step (iii) Further heating of the at least partially austenitised composition in step (iii) is carried out at a temperature of from 1200 to 1400°C, preferably from 1300 to 1380°C, more preferably from 1340 to 1360°C, even more preferably at about 1350 °C.
  • Step (iii) may result in the dissolution of any coarse vanadium carbides formed on austenitisation.
  • the composition may be maintained in this elevated temperature regime for up to 10 minutes, preferably from 30 seconds to 5 minutes, even more preferably for about 1 minute.
  • the composition may optionally be quenched, preferably to a temperature lower than 200°C, more preferably to a temperature lower than 150 °C.
  • the quenching may occur using helium quenching gas, and may occur at a cooling rate of 10 °C/minute or more, preferably 25 °C/minute or more.
  • the alloy is aged at a temperature of from 540 to 660°C, preferably from 560 to 640°C, more preferably from 580 to 620°C, and most preferably about 600°C.
  • the alloy may be aged for up to 120 minutes, preferably from 30 to 90 minutes, even more preferably for about 60 minutes. However, longer heating times are also possible.
  • the composition may optionally undergo a quench, preferably to a temperature lower than 200°C, more preferably to a temperature lower than 150 °C.
  • the quenching may occur using helium quenching gas, and may occur at a cooling rate of 10 °C/minute or more, preferably 25 °C/minute or more.
  • the heat-treatment method according to the present invention may further comprise carrying out an optional spheroidising treatment prior to the austenetising step (ii). This may increase the machinability of the alloy composition.
  • a tempering heat-treatment (v) may be optionally carried out following the ageing step (iv).
  • the optional tempering heat-treatment (v) may be carried out at a temperature of from 150 °C to 300 °C, preferably from 190 °C to 260 °C, more preferably from 200 to 230 °C, even more preferably about 215 °C.
  • the optional tempering heat-treatment (v) may be carried out for at least 30 minutes, preferably from 40 minutes to 240 minutes, more preferably from 90 minutes to 150 minutes, even more preferably for about 120 minutes. Longer heating times may also be employed.
  • the optional heat-treatment (v) results in the formation of fine cementite particles, which can impart the steel with high hardness.
  • One or more of the heat-treating steps may be carried out via induction heating.
  • induction heating improves efficiency.
  • Figure 1 shows a possible heat treatment schedule according to the present invention.
  • a steel alloy composition as described herein is heated to approximately 860°C and maintained at that temperature for about 15 minutes in order to at least partially austenise the composition. Vanadium carbides are also formed during this step. The composition is then further heated to approximately 1350°C and held at that temperature for about one minute in order to dissolve any coarse vanadium carbides formed during the austenisation before being quenched. Aging is then carried out at a temperature of approximately 600 °C for about 60 minutes, after which the composition is again quenched. In the final step, the composition is tempered at a temperature of approximately 215 °C for about 120 minutes, resulting in the formation of fine cementite particles.

Abstract

La présente invention se rapporte à un alliage d'acier qui comprend : une quantité de carbone comprise entre 0,6 et 1,2 % en poids ; une quantité de manganèse comprise entre 0,1 et 0,8 % en poids ; une quantité de chrome comprise entre 0,5 et 2,5 % en poids ; une quantité de vanadium comprise entre 2,5 et 3,5 % en poids ; facultativement, une quantité de silicium comprise entre 0 et 1,0 % en poids et/ou une quantité de molybdène comprise entre 0 et 2 % en poids et/ou une quantité de cuivre comprise entre 0 et 0,5 % en poids et/ou une quantité de nickel comprise entre 0 et 3,5 % en poids et/ou une quantité d'aluminium comprise entre 0 et 0,1 % en poids et/ou une quantité de phosphore comprise entre 0 et 0,05 % en poids et/ou une quantité de soufre comprise entre 0 et 0,05 % en poids et/ou une quantité de titane comprise entre 0 et 0,1 % en poids et/ou une quantité de niobium comprise entre 0 et 0,1 % en poids et/ou une quantité de tantale comprise entre 0 et 0,1 % en poids et/ou une quantité de tungstène comprise entre 0 et 0,1 % en poids et/ou une quantité de bore comprise entre 0 et 0,1 % en poids et/ou une quantité d'azote comprise entre 0 et 0,1 % en poids et/ou une quantité d'oxygène comprise entre 0 et 0,1 % en poids et/ou une quantité de calcium comprise entre 0 et 0,1 % en poids et/ou une quantité de cobalt comprise entre 0 et 0,1 % en poids, le reste étant du fer et des impuretés inévitables.
PCT/EP2013/070037 2012-10-03 2013-09-26 Alliage d'acier WO2014053385A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EPPCT/EP2012/069531 2012-10-03
EP2012069531 2012-10-03

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10060014B2 (en) 2014-11-21 2018-08-28 Hyundai Motor Company Bearing steel having improved fatigue durability and method of manufacturing the same

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Publication number Priority date Publication date Assignee Title
DE930267C (de) * 1941-07-09 1955-07-14 Oberhuetten Vereinigte Obersch Stahl fuer Dauerarbeitswerkzeuge, die bei Kaltarbeit auf Stoss, Schlag und Schneidenbeansprucht werden
JPH05148585A (ja) * 1991-11-26 1993-06-15 Japan Steel Works Ltd:The 高耐摩耗性冷延用作動ロール
GB2292389A (en) * 1994-08-08 1996-02-21 Nsk Ltd Rolling bearing
JPH10158780A (ja) * 1996-11-28 1998-06-16 Daido Steel Co Ltd プラズマ浸炭用冷間工具鋼
GB2345296A (en) * 1998-11-19 2000-07-05 Nsk Ltd Rolling member and production
EP1355071A1 (fr) * 2002-04-15 2003-10-22 Nsk Ltd Roulement pour transmission à variation continue
US20050051240A1 (en) * 2003-03-04 2005-03-10 Komatsu Ltd. Rolling element and method of producing the same
WO2005098057A1 (fr) * 2004-04-01 2005-10-20 Ntn Corporation Piece de roulement et roulement a billes
EP1715072A1 (fr) * 2004-01-20 2006-10-25 NSK Steering Systems Co. Ltd Roulement
JP2007100126A (ja) * 2005-09-30 2007-04-19 Ntn Corp 転動部材および転がり軸受

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE930267C (de) * 1941-07-09 1955-07-14 Oberhuetten Vereinigte Obersch Stahl fuer Dauerarbeitswerkzeuge, die bei Kaltarbeit auf Stoss, Schlag und Schneidenbeansprucht werden
JPH05148585A (ja) * 1991-11-26 1993-06-15 Japan Steel Works Ltd:The 高耐摩耗性冷延用作動ロール
GB2292389A (en) * 1994-08-08 1996-02-21 Nsk Ltd Rolling bearing
JPH10158780A (ja) * 1996-11-28 1998-06-16 Daido Steel Co Ltd プラズマ浸炭用冷間工具鋼
GB2345296A (en) * 1998-11-19 2000-07-05 Nsk Ltd Rolling member and production
EP1355071A1 (fr) * 2002-04-15 2003-10-22 Nsk Ltd Roulement pour transmission à variation continue
US20050051240A1 (en) * 2003-03-04 2005-03-10 Komatsu Ltd. Rolling element and method of producing the same
EP1715072A1 (fr) * 2004-01-20 2006-10-25 NSK Steering Systems Co. Ltd Roulement
WO2005098057A1 (fr) * 2004-04-01 2005-10-20 Ntn Corporation Piece de roulement et roulement a billes
JP2007100126A (ja) * 2005-09-30 2007-04-19 Ntn Corp 転動部材および転がり軸受

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10060014B2 (en) 2014-11-21 2018-08-28 Hyundai Motor Company Bearing steel having improved fatigue durability and method of manufacturing the same

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