WO2014056726A1 - Alliage d'acier pour roulement résistant à la fragilisation par l'hydrogène - Google Patents

Alliage d'acier pour roulement résistant à la fragilisation par l'hydrogène Download PDF

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Publication number
WO2014056726A1
WO2014056726A1 PCT/EP2013/070033 EP2013070033W WO2014056726A1 WO 2014056726 A1 WO2014056726 A1 WO 2014056726A1 EP 2013070033 W EP2013070033 W EP 2013070033W WO 2014056726 A1 WO2014056726 A1 WO 2014056726A1
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WO
WIPO (PCT)
Prior art keywords
steel alloy
bearing steel
vanadium
alloy
bearing
Prior art date
Application number
PCT/EP2013/070033
Other languages
English (en)
Inventor
Aidan KERRIGAN
Mohamed Sherif
Blanka SZOST
Original Assignee
Aktiebolaget Skf
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 filed Critical Aktiebolaget Skf
Publication of WO2014056726A1 publication Critical patent/WO2014056726A1/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
    • 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
    • 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
    • C22C38/20—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
    • F16C33/30—Parts of ball or roller bearings
    • F16C33/58—Raceways; Race rings
    • F16C33/62—Selection of substances
    • 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
    • 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
    • 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

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 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
  • 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 100CrMnMoSi8-4-6 has the following composition: 0.97 wt% carbon, 0.50 wt% silicon, 0.90 wt% manganese, 0.50 wt% molybdenum, 1 .90 wt% chromium, up to 0.05 wt% aluminium, up to 0.30 wt% copper, up to 0.25 wt% nickel, up to 0.025 wt% phosphorus and up to 0.015 wt% sulphur, the balance being iron (and any unavoidable impurities).
  • This steel exhibits high hardness and is suitable for use in a bearing component.
  • 100CrMnMoSi8-4-6 exhibits moderate-to-low resistance to hydrogen embrittlement.
  • the present invention provides a bearing steel alloy comprising from 0.8 to 1 .2 wt% carbon
  • vanadium optionally one or more of from 0 to 0.25 wt% nickel
  • the steel alloy according to the present invention comprises from 0.8 to 1 .2 wt% carbon.
  • the steel alloy composition comprises from 0.9 to 1 .1 wt% carbon, more preferably from 0.95 to 1 .05 wt% carbon.
  • the alloy comprises about 0.97 wt% carbon.
  • the presence of carbon in the specified amount may serve to increase the hardness of the steel alloy in the hardened condition.
  • 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 according to the present invention comprises from 0.3 to 0.9 wt% silicon.
  • the steel alloy comprises from 0.45 to 0.8 wt% silicon, more preferably from 0.5 to 0.8 wt% silicon.
  • the alloy comprises about 0.5 wt% silicon. Silicon may also act to increase strength and hardness.
  • the steel alloy according to the present invention comprises from 0.7 to 1 .3 wt% manganese.
  • the alloy comprises from 0.75 to 1 .2 wt% manganese, more preferably from 0.8 to 1 .1 wt% manganese.
  • the alloy comprises about 0.9 wt% manganese.
  • the manganese, in combination with the other alloying elements, may increase hardness and hardenability, and may contribute to the steel's strength. Manganese may also have a beneficial effect on surface quality. Manganese contents above the recited ranges will cause the excessive formation of retained austenite which is undesirable for hardness and dimensional stability.
  • the steel alloy according to the present invention comprises from 0.3 to 0.8 wt% molybdenum.
  • the alloy comprises from 0.4 to 0.7 wt% molybdenum, more preferably from 0.5 to 0.6 wt% molybdenum.
  • the alloy comprises about 0.5 wt% molybdenum.
  • molybdenum in the specified amounts may improve 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.
  • the steel alloy according to the present invention comprises from 2 to 2.6 wt% chromium.
  • the alloy comprises from 2.1 to 2.5 wt% chromium, more preferably from 2.2 to 2.4 wt% chromium.
  • the alloy comprises about 2.25 wt% chromium.
  • the presence of chromium in the specified amount may provide an improved corrosion resistance property to the steel alloy.
  • the chromium leads to a hard oxide on the metal surface to inhibit corrosion. Chromium may also have a beneficial effect on hardenability.
  • the steel alloy according to the present invention comprises from 0.15 to 0.55 wt% vanadium.
  • the alloy comprises from 0.16 to 0.3 wt% vanadium, more preferably from 0.17 to 0.23 wt% vanadium.
  • the alloy comprises about 0.2 wt% vanadium.
  • vanadium in the specified amounts has been found to form carbides, such as, for example, V C3.
  • Such carbides which are preferably nanometre-scaled, may act as hydrogen traps.
  • the presence of such carbides may provide the steel alloy with increased resistance to hydrogen embrittlement.
  • the presence of such carbides may also provide the steel alloy with increased strength and hardness.
  • the presence of vanadium in the range of about 0.15 to about 0.55 wt% makes carbide formation (for example V 4 C 3 ) thermodynamically possible at about 600°C, and is also beneficial for retarding grain growth during austenitisation.
  • the steel alloy according to the present invention may comprise up to 0.25 wt% nickel.
  • the alloy comprises from 0.005 to 0.05 wt% nickel, more preferably from 0.007 to 0.02 wt% nickel.
  • the alloy comprises about 0.01 wt% nickel.
  • Nickel, in concentrations close to the cited upper limit may act to increase hardenability and impact toughness.
  • the steel alloy according to the present invention may comprise up to 0.3 wt% copper.
  • the alloy comprises from 0.01 to 0.28 wt% copper, still more preferably from 0.1 to 0.27 wt% copper.
  • the alloy comprises about 0.25 wt% copper.
  • the copper may act to provide improved corrosion resistance.
  • the steel alloy according to the present invention may comprise up to 0.05 wt% aluminium.
  • the steel alloy comprises from 0.001 to 0.01 wt% aluminium, more preferably from 0.002 to 0.005 wt% aluminium.
  • the steel alloy comprises about 0.003 wt% aluminium.
  • Aluminium may be used as a deoxidizer. Aluminium, with other alloying elements, particularly nitrogen, may also act to control grain size in the alloy.
  • oxygen oxygen
  • phosphorus phosphorus
  • sulphur sulphur
  • the content thereof should generally not exceed 0.025 wt%. Typically the phosphorus content will be about 0.004 wt%.
  • sulphur is present, the content should generally not exceed 0.015 wt%. Typically the sulphur content will be about 0.003 wt%.
  • oxygen is present, the content should generally not exceed 0.015 wt%.
  • the oxygen content does not exceed 10 ppm. More preferably, the oxygen content does not exceed 5 ppm.
  • the steel alloy according to the present invention may contain unavoidable impurities, although, in total, these are unlikely to exceed 0.5 wt.% of the composition.
  • the alloy according to the present invention 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.
  • the steel alloy according to the present invention has a ratio Mo/V by weight, based on the total weight of the alloy, of from 0.6 to 4, preferably from 0.8 to 3.5. This ratio may ensure a high hydrogen trap concentration without the formation of coarse carbides at higher ratios.
  • a most preferred steel alloy according to the present invention comprises: about 0.97 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 bainite (bainitic ferrite), retained austenite, and carbides some of which comprise mainly vanadium and carbon. The typical retained austenite content is up to 5 vol% (optionally present).
  • the bainite will typically be lower bainite with content up to 95 vol%.
  • aluminium nitrides are present in very small volume fraction.
  • the carbides may consist of vanadium and carbon, for example V C3, or may include one or more additional alloying elements.
  • carbide as used herein is meant to encompass also, for example, carbo-nitrides and also mixed metal carbides, carbo-nitrides.
  • the microstructure comprises from 1 to 10 vol. % carbides (some of which comprising mainly vanadium and carbon), the remainder being bainitic ferrite and retained austenite. Most preferably, the microstructure comprises about 5 vol. % carbides (some of which comprising mainly vanadium and carbon), the remainder being bainitic ferrite and retained austenite.
  • carbide precipitates comprising vanadium and carbon may act as hydrogen traps.
  • the carbide precipitates comprising vanadium and carbon have a plate shape with average aspect ratio of 4.5 to 6.5 and 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 may be particularly effective as hydrogen traps.
  • the microstructure of the alloy is substantially free of retained austenite for better dimensional stability, strength and hardness.
  • 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.
  • a rolling element for example ball or cylinder
  • inner ring for example ball or cylinder
  • outer ring for example ball or cylinder
  • Other example application can be for the manufacture of linear motion components such as screws and nuts.
  • the present invention provides a bearing comprising a bearing component as described herein.
  • Figure 1 shows the calculated TTT diagrams for 100CrMnMoSi8-4-6 (dashed line) and an alloy according to the present invention comprising about 0.97 wt% carbon, about 0.5 wt % silicon, about 0.9 wt% manganese, about 0.5 wt % molybdenum, about 2.25 wt% chromium, about 0.2 wt% vanadium, about 0.01 wt% nickel, about 0.25 wt% copper, about 0.003 wt% aluminium, about 0.004 wt% phosphorus, about 0.003 wt% sulphur and the balance iron, together with unavoidable impurities (solid line).
  • the TTT diagrams were calculated using the MUCG83 algorithm (http://www.msm.cam.ac.uk/map/steel/prgrams/mucg83.html).
  • the diagrams suggest that the transformation behaviour and the hardenability of the bearing steels of the present invention are similar to those of 100CrMnMoSi8-4-6.
  • a suitable heat treatment for the inventive alloy is as follows:
  • the bearing steel Prior to hardening, the bearing steel may be hot-worked (forged and/or hot-rolled), heat-treated and softened by means of applying a suitable spheroidise-annealing heat treatment.
  • the martensite-start temperature (M s ) is expected to be lowered as the austenite grains become finer which enables the bainite transformation to take place at even lower temperatures permitting the formation of harder structures. Moreover, the finer hardened structure yields better strength, toughness and hardness. All improve the resistance to rolling contact fatigue.
  • Typical temperatures for bainite transformation are within the range 150°C to 310°C for holding times between 30 min and 48 h.
  • the bainite transformation stage comprises:
  • the present invention describes a bainitic transformation schedule as follows (ordered 1 through 4):
  • Example temperature is 200°C ;
  • a second step may be employed which comprises heating the novel steel components, from the first bath temperature, typically by transferring the charge to a second salt bath kept at a temperature below the bainite-start temperature (B s ) and holding isothermally until the bainitic transformation has ceased;
  • the bainite transformed bearing components are then air-cooled and subsequently cleaned;
  • bearing components may then be frozen to sub-zero temperatures followed by tempering to further reduce the content of retained austenite.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente invention concerne un alliage d'acier pour roulement comprenant : de 0,8 à 1,2 % en poids de carbone, de 0,3 à 0,9 % en poids de silicium, de 0,7 à 1,3 % en poids de manganèse, de 0,3 à 0,8 % en poids de molybdène, de 2 à 2,6 % en poids de chrome, de 0,15 à 0,55 % en poids de vanadium, éventuellement au moins un parmi : de 0 à 0,25 % en poids de nickel, de 0 à 0,3 % en poids de cuivre, de 0 à 0,05 % en poids d'aluminium, de 0 à 0,015 % en poids d'azote, de 0 à 0,025 % en poids de phosphore, de 0 à 0,015 % en poids de soufre, de 0 à 0,015 % en poids d'oxygène, et le complément étant du fer, et des impuretés inévitables.
PCT/EP2013/070033 2012-10-10 2013-09-26 Alliage d'acier pour roulement résistant à la fragilisation par l'hydrogène WO2014056726A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP2012070020 2012-10-10
EPPCT/EP2012/070020 2012-10-10

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WO2014056726A1 true WO2014056726A1 (fr) 2014-04-17

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107034422A (zh) * 2015-12-14 2017-08-11 斯凯孚公司 耐疲劳轴承钢
WO2023165645A1 (fr) * 2022-03-03 2023-09-07 Schaeffler Technologies AG & Co. KG Procédé de fabrication de pièces de palier à roulement présentant un degré de ténacité élevé

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SU579337A1 (ru) * 1976-05-13 1977-11-05 Центральный Научно-Исследовательский Институт Технологии Машиностроения Сталь
SU583194A1 (ru) * 1976-07-12 1977-12-05 Центральный Ордена Трудового Красного Знамени Научно-Исследовательский Институт Технологии Машиностроения Сталь
EP0458646A1 (fr) * 1990-05-23 1991-11-27 Aichi Steel Works, Ltd. Acier pour paliers
JPH06293939A (ja) * 1993-04-07 1994-10-21 Kobe Steel Ltd 高温転動疲労性に優れた軸受部品
US20010015244A1 (en) * 1999-12-14 2001-08-23 Akihiro Kiuchi Rolling bearing and method manufacturing the same
EP1614761A1 (fr) * 2003-04-16 2006-01-11 JFE Steel Corporation Matiere en acier possedant une excellente longevite a la fatigue due au roulement et son procede de production
EP1826286A2 (fr) * 2006-02-28 2007-08-29 JFE Steel Corporation Pièce d'acier comportant une longue durée de roulement et son procédé de fabrication

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SU579337A1 (ru) * 1976-05-13 1977-11-05 Центральный Научно-Исследовательский Институт Технологии Машиностроения Сталь
SU583194A1 (ru) * 1976-07-12 1977-12-05 Центральный Ордена Трудового Красного Знамени Научно-Исследовательский Институт Технологии Машиностроения Сталь
EP0458646A1 (fr) * 1990-05-23 1991-11-27 Aichi Steel Works, Ltd. Acier pour paliers
JPH06293939A (ja) * 1993-04-07 1994-10-21 Kobe Steel Ltd 高温転動疲労性に優れた軸受部品
US20010015244A1 (en) * 1999-12-14 2001-08-23 Akihiro Kiuchi Rolling bearing and method manufacturing the same
EP1614761A1 (fr) * 2003-04-16 2006-01-11 JFE Steel Corporation Matiere en acier possedant une excellente longevite a la fatigue due au roulement et son procede de production
EP1826286A2 (fr) * 2006-02-28 2007-08-29 JFE Steel Corporation Pièce d'acier comportant une longue durée de roulement et son procédé de fabrication

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107034422A (zh) * 2015-12-14 2017-08-11 斯凯孚公司 耐疲劳轴承钢
US20170335440A1 (en) * 2015-12-14 2017-11-23 Aktiebolaget Skf Fatigue-resistant bearing steel
WO2023165645A1 (fr) * 2022-03-03 2023-09-07 Schaeffler Technologies AG & Co. KG Procédé de fabrication de pièces de palier à roulement présentant un degré de ténacité élevé

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