WO2016083283A1 - Composant de palier - Google Patents

Composant de palier Download PDF

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Publication number
WO2016083283A1
WO2016083283A1 PCT/EP2015/077314 EP2015077314W WO2016083283A1 WO 2016083283 A1 WO2016083283 A1 WO 2016083283A1 EP 2015077314 W EP2015077314 W EP 2015077314W WO 2016083283 A1 WO2016083283 A1 WO 2016083283A1
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WO
WIPO (PCT)
Prior art keywords
bearing component
ppm
steel
alloy
alloy comprises
Prior art date
Application number
PCT/EP2015/077314
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English (en)
Inventor
Mohamed Sherif
Original Assignee
Aktiebolaget Skf
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Filing date
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Application filed by Aktiebolaget Skf filed Critical Aktiebolaget Skf
Publication of WO2016083283A1 publication Critical patent/WO2016083283A1/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
    • 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
    • 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
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D2211/008—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
    • F16C2204/64—Medium carbon steel, i.e. carbon content from 0.4 to 0,8 wt%
    • 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
    • F16C2204/74—Ferrous alloys, e.g. steel alloys with manganese as the next major constituent

Definitions

  • the present invention relates generally to the field of metallurgy and to a bearing component made from a steel composition having relatively low carbon content.
  • the steel composition is through-hardenable.
  • Rolling element bearings comprise inner and outer raceways and a plurality of rolling elements (balls or rollers) disposed there-between.
  • rolling elements balls or rollers
  • An important characteristic of bearing steels is the hardenability, i.e. the depth up to which the alloy is hardened after putting it through a heat-treatment process.
  • a known bearing steel comprises 0.97 wt.% C, 0.32 wt.% Si, 0.31 wt.% Mn, 1 .43 wt.% Cr, the balance being Fe and any unavoidable impurities.
  • Another commercial through- hardenable steel comprises 0.65 wt.% C, 1 .50 wt.% Si, 1.40 wt.% Mn, 1 .10 wt.% Cr, 0.25 wt.% Mo, the balance being Fe and any unavoidable impurities.
  • the present invention aims to provide a bearing component made from a low carbon bearing steel that can be through-hardened by a simple heat-treatment.
  • the present invention provides a bearing component made from a steel alloy comprising: from 0.5 to 0.7 wt.% carbon,
  • the steel alloy preferably has a martensitic microstructure and may, for example, comprise tempered martensite.
  • the microstructure may optionally include carbides, nitrides and/or carbonitrides.
  • the microstructure may optionally include untransformed "retained" austenite.
  • the steel alloy composition comprises from 0.5 to 0.7 wt.% carbon, preferably from 0.55 to 0.65 wt.% carbon, more preferably approximately 0.6 wt.% carbon. In combination with the other alloying elements, this results in the desired martensitic microstructure.
  • the relatively low carbon content impacts positively on the hardenability of the steel, making it particularly suitable for bearing components with relatively large wall thicknesses.
  • the high hardenability of the steel during austenitisation reduces or eliminates the likelihood of forming the slack-quench phase "Troostite" upon quenching the bearing component. It is believed that Troostite may trigger premature bearing component failure during service, if present.
  • the relatively lower carbon content also means that the steel will possess good toughness and as such good defect-tolerance, and that it is particularly suitable for continuous casting and induction hardening and tempering processes.
  • the steel alloy composition comprises from 1.4 to 1.8 wt.% silicon, preferably from 1 .5 to 1 .7 wt.% silicon, more preferably approximately 1 .6 wt.% silicon. In combination with the other alloying elements, this results in the desired microstructure with a minimum amount of retained austenite. Silicon helps to suppress the precipitation of cementite and carbide formation. Also, silicon strengthens the structure and improves resistance to softening caused by tempering.
  • the maximum silicon content is 1 .8 wt.%.
  • Steels with high silicon content tend to retain more austenite in their hardened and tempered structures due to the carbide-suppressing characteristics of the element, which will lower the hardness and have a negative impact on dimensional stability. It follows that the steel concentration of silicon can be reduced to lower the retained austenite content.
  • the relatively high silicon content in the steel alloy used in the present invention has also been found to contribute to good tempering resistance.
  • the steel alloy composition comprises from 1.7 to 2.1 wt.% manganese, preferably from 1.8 to 2.0 wt.% manganese, more preferably approximately 1 .9 wt.% manganese.
  • Manganese acts to increase the stability of austenite relative to ferrite. Manganese also acts to improve hardenability.
  • the steel alloy according to the present invention comprises at least 1 .7 wt.% manganese and no more than 2.1 wt.% manganese.
  • the steel composition comprises from 0.05 to 0.4 wt.% molybdenum, preferably from 0.05 to 0.3 wt.%
  • molybdenum more preferably from 0.1 to 0.3 wt.% molybdenum, still more preferably from 0.1 to 0.2 wt.% molybdenum, still more preferably approximately 0.15 wt.% molybdenum.
  • Molybdenum may act to avoid grain boundary embrittlement and has a strong positive impact on hardenability. However, molybdenum is expensive and hence it is desirable, if possible, to limit its content in the alloy. In combination with the other alloying elements, it is possible to limit the molybdenum content to a maximum of 0.4 wt.%, more preferably 0.2 wt.%.
  • the steel composition comprises from 1.1 to 1.5 wt.% chromium.
  • the content of chromium was found during thermodynamic calculations to greatly impact the type of carbide obtainable during hardening in that if the concentration is too low, the relatively undesirable cementite phase is stabilised.
  • the alloy therefore comprises at least 1 .1 wt.% chromium, preferably at least 1.2 wt.% chromium.
  • the chromium content must be restricted, for example, to ensure sufficient carbon in solid solution in the austenite phase during hardening. For the austenite to transform into a sufficiently hard structure at lower temperatures it must possess sufficient dissolved carbon and nitrogen.
  • the steel alloy therefore comprises a maximum of 1 .5 wt.% chromium.
  • the steel composition preferably comprises from 1.1 to 1.4 wt.% chromium, more preferably from 1 .2 to 1 .4 wt.% chromium, still more preferably approximately 1 .3 wt.% chromium.
  • the steel alloy may comprise up to 0.2 wt.% vanadium, for example 0.05 to 0.15 wt.% vanadium, preferably approximately 0.1 wt.% vanadium. Vanadium may form carbides, nitrides and/or carbonitrides.
  • one or more of the optional elements Ta and/or Nb may be added to the alloy to form carbides, nitrides and/or carbonitrides.
  • nitrogen is added such that the steel alloy comprises from 50 to 200 ppm nitrogen, preferably from 75 to 200 ppm nitrogen. In other embodiments, there is no deliberate addition of nitrogen. Nevertheless, the alloy necessarily still comprises at least 50 ppm nitrogen due to exposure to the atmosphere during melting. Nitrogen in an amount of 50 to 200 ppm, in conjunction with the other alloying elements, has been found to be beneficial in terms of achieving the desired microstructure and properties.
  • the steel alloy comprises no more than 0.05 wt.% aluminium. Aluminium may be present in the steel in very small amounts due to de-oxidation. However, its content must be controlled to ensure high cleanliness consistent with bearing application requirements.
  • the steel composition may also optionally include one or more of the following elements: from 0 to 0.2 wt.% vanadium (for example 0.05 to 0.2 wt.% vanadium)
  • nickel for example 0.02 to 0.2 wt.% nickel
  • aluminium from 0 to 0.05 wt.% aluminium (for example 0.025 wt.% aluminium)
  • niobium from 0 to 0.1 wt.% niobium (for example 0.05 to 0.1 wt.% niobium)
  • the steel alloy referred to herein may contain unavoidable impurities, although, in total, these are unlikely to exceed 0.3 wt.% of the composition.
  • the alloys may contain unavoidable impurities in an amount of not more than 0.1 wt.% of the composition, more preferably not more than 0.05 wt.% of the composition.
  • the steel composition may also include one or more impurity elements.
  • impurities includes, for example: from 0 to 0.025 wt.% phosphorous
  • the steel alloy composition preferably comprises little or no sulphur, for example from 0 to 0.015 wt.% sulphur.
  • the steel alloy composition preferably comprises little or no phosphorous, for example from 0 to 0.025 wt.% phosphorous.
  • the steel composition preferably comprises ⁇ 15 ppm oxygen. Oxygen may be present as an impurity.
  • the steel composition preferably comprises ⁇ 30 ppm titanium. Titanium may be present as an impurity.
  • the steel composition preferably comprises ⁇ 20 ppm boron. Boron may be present as an impurity at, for example, 1 -5 ppm.
  • the steel composition preferably comprises ⁇ 50 ppm calcium. Calcium may be present as an impurity but may also be added intentionally in very small amounts, for example 1 -10 ppm or 1 -3 ppm.
  • the steel alloy composition may consist essentially of the recited elements. It will therefore be appreciated that in addition to those elements that 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 bearing component comprises the steel alloy as herein described. Examples of bearing components include a rolling element (e.g. ball, cylinder, tapered or specially-profiled rolling element), an inner ring, and an outer ring.
  • the present invention also provides a bearing comprising a bearing component as herein described. The present invention will now be described further with reference to a suitable heat treatment for the steel alloy, provided by way of example.
  • the steel microstructure may harden by transforming into martensite during subsequent cooling to room temperature. It follows that a subsequent tempering step may be applied resulting in a tough-tempered structure that is particularly suitable for induction hardening and tempering processes - at a great cost-saving - at least due to not needing to carry out the expensive spheroidise-annealing process.
  • the resulting tough core is beneficial from a performance standpoint.
  • the steel may be spheroidise-annealed from the as hot-worked state, to improve machinability.
  • the steel composition may be austenitised at a temperature in the range of from 850 to 905 e C, preferably 875 to 895 e C, for example approximately 885 e C.
  • the alloy composition favours the formation of austenite that has a specific concentration of the recited alloying elements and this is believed to favour the formation of certain crystal defects, such as twins and stacking faults, once the alloy is quenched/transformed.
  • the alloy may be tempered following quenching.
  • the microstructure of the final alloy typically comprises martensite as the main phase and optionally some retained austenite, metal carbides, nitrides and/or carbonitrides.
  • the microstructure in one embodiment comprises tempered martensite.
  • the microstructure may also include a small amount of unavoidable retained austenite.
  • the microstructure may also include a small fraction of bainitic-ferrite (bainite).
  • the alloy may also be snap-tempered after the first quench and cooling to room
  • the steel may be deep-frozen, or sub-zero treated, followed by a single temper and then air-cooling.
  • bainitic heat treatment may be adopted for large bearing components, where the wall thickness is relatively high.
  • bainitic-ferrite is the main phase in the resulting microstructure.
  • the steel articles may be quenched to temperatures just above the martensite start temperature (M s ), equilibrated at temperature, then quenched to transform into martensite.
  • M s martensite start temperature
  • a small amount of austenite may transform into bainite (bainitic-ferrite) prior to the final quench; with little or no adverse effects on mechanical properties.
  • the microstructure in such a case may be a mixed bainite and martensite.
  • as-quenched martensite is preferably always followed by tempering.
  • Figures 1 a) and b) are optical micrographs showing the microstructure of a steel alloy for use in a bearing component according to the present invention.
  • Figures 2 a) and b) represent calculated continuous cooling transformation (CCT) diagrams for: a) a steel alloy for use in a bearing component according to the present invention; and b) a commercial through-hardenable steel.
  • CCT continuous cooling transformation
  • Oxygen level should be less than 10 ppm, Ti level less than 30 ppm, and Ca level less than
  • the novel steel composition once austenitised at approximately 885 e C, quenched and tempered, has a martensitic microstructure and aims at strengthening the matrix, with significant increase in hardness, by means of facilitating the formation of nanoscale crystal defects, such as, for example, planar defects, such as twins and stacking faults.
  • the increase in hardness may be achieved without the need for expensive alloying elements, or special heat treatments.
  • An experimental steel melt was prepared by Vacuum Induction Melting (VIM) followed by casting the molten steel into a 100 kg ingot. After discarding the head and the bottom of the ingot, ca. 55 kg were then used.
  • VIM Vacuum Induction Melting
  • the chemical composition can be seen below: Steel, comprising in wt.%
  • the plates were then air-cooled to 650 ° C before being placed in a furnace that was heated to 650 ° C, where they were allowed to cool in the furnace.
  • Some of the plate material was then soft-annealed (spheroidising-annealing process) by heating to the temperature of 800 ° C, soaking at temperature, then the steel was slowly cooled to room temperature (furnace-cooled). This heat treatment process ensures a structure which is sufficiently soft for machinability.
  • soft-annealing process is also carried out to control the starting microstructure prior to hardening (austenitisation).
  • the resulting microstructure was tempered martensite with very little carbides that could be resolved under the visible light optical microscope, see Figures 1 a) and b).
  • Figures 2 a) and b) represent the calculated CCT diagrams of the steel composition of: Example 2 in a); and that of a commercial, through-hardenable steel in b), the composition of which is provided below.
  • the hardness measured at room temperature was 63.0 ⁇ 0.4 HRC for one specimen and 63.4 ⁇ 0.1 HRC for the second.
  • the load used during the measurement was 150 kgf.
  • the steel alloy microstructure also exhibits good tempering resistance and withstands service at high temperatures. Thanks to the steel's relatively low carbon concentration, it could be austenitised at somewhat high temperatures without negatively impacting its toughness.

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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)
  • Rolling Contact Bearings (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

Cette invention concerne un composant de palier fait d'un alliage d'acier comprenant : de 0,5 à 0,7 % en poids de carbone, de 1,4 à 1,8 % en poids de silicium, de 1,7 à 2,1 % en poids de manganèse, de 0,05 à 0,4 % en poids de molybdène, de 1,1 à 1,5 % en poids de chrome, de 50 à 200 ppm d'azote, de 0 à 0,2 % en poids de vanadium, de 0 à 0,25 % en poids de nickel, de 0 à 0,3 % en poids de cuivre, de 0 à 0,2 % en poids de cobalt, de 0 à 0,05 % en poids d'aluminium, de 0 à 0,1 % en poids de niobium, de 0 à 0,2 % en poids de tantale, de 0 à 0,025 % en poids de phosphore, de 0 à 0,015 % en poids de soufre, de 0 à 0,075 % en poids d'étain, de 0 à 0,075 % en poids d'antimoine, de 0 à 0,04 % en poids d'arsenic, de 0 à 0,002 % en poids de plomb, jusqu'à 15 ppm d'oxygène, jusqu'à 50 ppm de calcium, jusqu'à 20 ppm de bore, jusqu'à 30 ppm de titane, le reste étant du fer et les inévitables impuretés, l'alliage d'acier présentant une microstructure martensitique et comprenant éventuellement un ou plusieurs éléments parmi l'austénite résiduelle, des carbures, des nitrures et/ou des carbonitrures.
PCT/EP2015/077314 2014-11-27 2015-11-23 Composant de palier WO2016083283A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
GB1421047.0 2014-11-27
GBGB1421047.0A GB201421047D0 (en) 2014-11-27 2014-11-27 Bearing steel

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112662944A (zh) * 2020-12-03 2021-04-16 宝钢特钢韶关有限公司 轴承钢及其制备方法
CN113357265A (zh) * 2020-03-04 2021-09-07 马勒国际有限公司 烧结轴承套材料、滑动轴承、内燃机和电动机
WO2023101642A3 (fr) * 2021-11-04 2023-08-31 Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ Composition d'acier faiblement allié à haute résistance et procédé de production associé

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Publication number Priority date Publication date Assignee Title
US9869009B2 (en) * 2013-11-15 2018-01-16 Gregory Vartanov High strength low alloy steel and method of manufacturing

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JP2007270293A (ja) * 2006-03-31 2007-10-18 Nippon Steel Corp 耐遅れ破壊特性に優れた高強度支圧接合部品及びその製造方法並びに高強度支圧接合部品用鋼
JP2009242937A (ja) * 2008-03-10 2009-10-22 Jfe Steel Corp 転動疲労特性に優れた軸受鋼およびその製造方法
US20110052442A1 (en) * 2008-03-25 2011-03-03 Aktiebolaget Skf Bearing component

Patent Citations (3)

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JP2007270293A (ja) * 2006-03-31 2007-10-18 Nippon Steel Corp 耐遅れ破壊特性に優れた高強度支圧接合部品及びその製造方法並びに高強度支圧接合部品用鋼
JP2009242937A (ja) * 2008-03-10 2009-10-22 Jfe Steel Corp 転動疲労特性に優れた軸受鋼およびその製造方法
US20110052442A1 (en) * 2008-03-25 2011-03-03 Aktiebolaget Skf Bearing component

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CN113357265A (zh) * 2020-03-04 2021-09-07 马勒国际有限公司 烧结轴承套材料、滑动轴承、内燃机和电动机
CN113357265B (zh) * 2020-03-04 2023-10-24 马勒国际有限公司 烧结轴承套材料、滑动轴承、内燃机和电动机
CN112662944A (zh) * 2020-12-03 2021-04-16 宝钢特钢韶关有限公司 轴承钢及其制备方法
WO2023101642A3 (fr) * 2021-11-04 2023-08-31 Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ Composition d'acier faiblement allié à haute résistance et procédé de production associé

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