US3704183A - Method for producing a low-cost hypereutectoid bearing steel - Google Patents

Method for producing a low-cost hypereutectoid bearing steel Download PDF

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Publication number
US3704183A
US3704183A US146911A US3704183DA US3704183A US 3704183 A US3704183 A US 3704183A US 146911 A US146911 A US 146911A US 3704183D A US3704183D A US 3704183DA US 3704183 A US3704183 A US 3704183A
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United States
Prior art keywords
steel
cost
hypereutectoid
low
bearing
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Expired - Lifetime
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US146911A
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English (en)
Inventor
Charles P Weigel
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Timken Co
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Timken Co
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Publication date
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/08—Casting in, on, or around objects which form part of the product for building-up linings or coverings, e.g. of anti-frictional metal
    • B22D19/085—Casting in, on, or around objects which form part of the product for building-up linings or coverings, e.g. of anti-frictional metal of anti-frictional metal
    • 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

Definitions

  • a steel of this type usually in the form of wire, rod, bar, forgings, rings or tubing, is annealed at a maximum temperature of 1400 F. for thirteen hours to produce an annealed microstructure comprising spheroidized carbides in a matrix of ferrite. After forming into bearing races or balls, the formed product is quenched from 1550 F. and thereafter tempered to produce a steel having a Rockwell C hardness of about 60 or greater and excellent fatigue strength.
  • AISI 52100 steel has been used extensively, and almost exclusively, for ball bearing applications.
  • Such a steel contains as essential alloying additions, .98-1.10% carbon, .25-.45% manganese and 1.30-1.60% chromium.
  • the relatively high amount of chromium is added to assist in hardenability; however this materially increases the cost of the product.
  • tubular shapes, bars, forgings and rings (for forming bearing races) and wire or rod (for forming balls) are initially annealed at about 1450 F., maximum temperature, and furnace cooled at a controlled rate for twenty-two hours, followed by air cooling.
  • spheroidized carbides are formed in a matrix of ferrite to produce a product having good machinability, cold heading and/or cold forming properties.
  • the balls and races are quenched in oil from about 1550 F. and then tempered to achieve a Rockwell C hardness of 60 or greater. Of course, the steel must also have good fatigue strength.
  • the present invention resides in the discovery that a high carbon bearing steel can be prepared which contain substantially less total alloy content than conventional bearing steels, without sacrificing the hardenability, fatigue strength and processing characteristics of higher alloy bearing steels. At the same time, the annealing time required to achieve adequate carbon diffusion to produce a spheroidized microstructure is materially reduced with the steel of the invention.
  • the bearing steel of the invention has the following broad and preferred compositions:
  • Nickel and silicon are relatively unimportant in achieving the desired characteristics of the alloy and can be classified as residual amounts. .20-.35% silicon is that amount found in most alloy steels. Similarly, a certain amount of sulfur is found in every steel; however, it is desired to deliberately include .008-.04% sulfur to improve machinability and fatigue strength. As was mentioned above, carbon, manganese, chromium and molybdenum are the essential additions, the chromium and molybdenum acting to increase hardenability. In the preferred analysis given above, percent by Weight of carbon is however it should be understood that this can vary plus or minus five points, in accordance with usual metallurgical practices.
  • the steel of the foregoing composition is melted, formed into tubing, forgings, rings, bars, rod, wire or other shapes, and then annealed at a maximum temperature of 1400 F. for thirteen hours in order to achieve a spheroidized microstructure comprising spheroidized carbides in a matrix of ferrite.
  • the steel is passed through eleven zones of a roller hearth furance at a constant speed, the time in each zone being about oneeleventh of the total time of thirteen hours.
  • the temperatures of the respective zones are shown in the following Table I:
  • the annealed product is then cold headed or cold formed into balls and machined or formed into races which are thereafter heated to a temperature of 1550 F., followed by quenching in oil. In this condition, the product has a Rockwell C hardness of about 63-66.
  • the final step in the process is to temper the product at 300 F. for about 1 to 2 hours to achieve a Rockwell C hardness of 60 or greater.
  • the resulting product has a density of 0.283 pound per cubic inch, a specific gravity of 7.83, a modulus of elasticity of 29 l0 pounds per square inch and a modulus of rigidity of 12x10 pounds per square inch.
  • the product has excellent fatigue strength, comparable to that of the higher alloy AISI 52100 bearing steel and much better than AISI 5160 which is sometimes used as a low-cost substitute for hearing steels. This is shown in the accompanying drawing wherein curve 10 is that for the steel of the invention; whereas curve 12 is that obtained from fatigue tests conducted on AISI 5160 steel.
  • the steel of the invention has an L fatigue life (i.e., a probability of 10% failures, or 90% survival) after about 10 million stress cycles; whereas AISI 5160 steel has an L fatigue life after only 6.5 million stress cycles. Note that the improvement in fatigue life persists at 50% survival. Thus, the steel of the invention has an L fatigue life of 45 million stress cycles as compared with 25 million stress cycles for AISI 5160.

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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)
  • Heat Treatment Of Articles (AREA)
  • Rolling Contact Bearings (AREA)
US146911A 1971-05-26 1971-05-26 Method for producing a low-cost hypereutectoid bearing steel Expired - Lifetime US3704183A (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US14691171A 1971-05-26 1971-05-26

Publications (1)

Publication Number Publication Date
US3704183A true US3704183A (en) 1972-11-28

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Family Applications (1)

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US146911A Expired - Lifetime US3704183A (en) 1971-05-26 1971-05-26 Method for producing a low-cost hypereutectoid bearing steel

Country Status (8)

Country Link
US (1) US3704183A (enExample)
AU (1) AU469222B2 (enExample)
CA (1) CA954728A (enExample)
DE (1) DE2225517B2 (enExample)
FR (1) FR2139069B1 (enExample)
GB (1) GB1354828A (enExample)
IT (1) IT955833B (enExample)
SE (1) SE411557B (enExample)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2342818A1 (fr) * 1976-03-05 1977-09-30 Ceskoslovenska Akademie Ved Fabrication de pieces d'acier annulaire par coulee de lingots centrifuges, debites en couronnes
US4581079A (en) * 1985-03-27 1986-04-08 Amax Inc. Bearing steel
EP0571667A1 (en) * 1992-05-27 1993-12-01 Ab Skf Steel for ball and roller bearings
EP0657551A1 (fr) * 1993-12-13 1995-06-14 Ascometal Procédé de recuit de produits sidérurgiques en acier au carbone riches en chrome et en manganèse

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1046286A (ja) 1996-07-26 1998-02-17 Nippon Seiko Kk 転がり軸受

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2342818A1 (fr) * 1976-03-05 1977-09-30 Ceskoslovenska Akademie Ved Fabrication de pieces d'acier annulaire par coulee de lingots centrifuges, debites en couronnes
US4581079A (en) * 1985-03-27 1986-04-08 Amax Inc. Bearing steel
EP0571667A1 (en) * 1992-05-27 1993-12-01 Ab Skf Steel for ball and roller bearings
EP0657551A1 (fr) * 1993-12-13 1995-06-14 Ascometal Procédé de recuit de produits sidérurgiques en acier au carbone riches en chrome et en manganèse
FR2713661A1 (fr) * 1993-12-13 1995-06-16 Ascometal Sa Procédé de recuit de produits sidérurgiques en acier au carbone riches en chrome et en manganèse.

Also Published As

Publication number Publication date
FR2139069A1 (enExample) 1973-01-05
FR2139069B1 (enExample) 1973-07-13
IT955833B (it) 1973-09-29
DE2225517A1 (de) 1972-12-14
AU4244072A (en) 1973-11-22
GB1354828A (en) 1974-06-05
DE2225517B2 (de) 1977-05-18
SE411557B (sv) 1980-01-14
AU469222B2 (en) 1976-02-05
CA954728A (en) 1974-09-17

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