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EP0894873A1 - Vanadium alloyed bearing steel - Google Patents

Vanadium alloyed bearing steel Download PDF

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Publication number
EP0894873A1
EP0894873A1 EP98850125A EP98850125A EP0894873A1 EP 0894873 A1 EP0894873 A1 EP 0894873A1 EP 98850125 A EP98850125 A EP 98850125A EP 98850125 A EP98850125 A EP 98850125A EP 0894873 A1 EP0894873 A1 EP 0894873A1
Authority
EP
European Patent Office
Prior art keywords
steel
vanadium
bearing steel
weight
carbon content
Prior art date
Legal status (The legal status 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 status listed.)
Withdrawn
Application number
EP98850125A
Other languages
German (de)
French (fr)
Inventor
Thore Lund
Staffan Larsson
Patrik Ölund
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Ovako Steel AB
Original Assignee
Ovako Steel AB
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 Ovako Steel AB filed Critical Ovako Steel AB
Publication of EP0894873A1 publication Critical patent/EP0894873A1/en
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/12Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention relates to an improved vanadium alloyed bearing steel.
  • the hardness after martensitic hardening of a soft annealed bearing steel e.g. AISE 52100 is highly dependent on the carbon content in solid solution and thus the austenitisation conditions for a given quench.
  • a higher austenitisation temperature or longer time leads to more dissolution of carbides.
  • the optimum carbon content in solid solution to give the highest hardness is considered to be somewhere between 0.6 to 0.8 weight% for an oil quenched component.
  • a lower carbon content will give a softer martensite.
  • a higher carbon content will lead to an increased retained austenite content which would decrease the hardness and give a disadvantageous martensite morphology. Furthermore, a too large amount of retained austenite will give poor structural stability.
  • Hardened bearing steels are often subjected to wear. To improve wear properties it is necessary to maximize the hardness. However, this could also be further improved by introducing a fraction of hard carbides such as VC.
  • the toughness of a component made from a bearing steel is relatively low. This could result in catastrophically failure and it would therefore be appreciated to increase the toughness. This could be achieved by alloying with Ni which is an element that improves the toughness.
  • Structural stability is important for critical applications and could be improved by Si alloying. Si retards the precipitation of carbide during tempering and thus improves the stability. This could also be beneficial for reducing tempering embrittlement since the precipitation of grain boundary carbides could be reduced.
  • the object of the invention is to provide a steel designed to exhibit greater tolerances in austenitising temperature and time to give optimum carbon content.
  • carbide formers preferably V and also Cr
  • carbide formers preferably V and also Cr
  • an optimal carbon content is obtained.
  • a higher wear resistance is obtained because of the presence hard VC carbides.
  • Improved toughness can be obtained by Ni addition and a high structural stability can be obtained with Si additions.
  • the required hardenability is balanced by adding Cr, Mo and Mn.
  • the steel has the following analysis, in weight-%: C 0.60 - 1.00 Si 0.40 - 2.10 Mn 0.10 - 1.00 Ni 0.50 - 2.00 Cr 0 - 2.00 Mo 0 - 0.50 V 0.25 - 1.00 Fe incl. possible impurities - ad. 100%.
  • the steel has the following analysis, in weight-%: C 0.75 - 0.95 Si 0.80 - 1.80 Mn 0.10 - 1.00 Ni 0.50 - 1.50 Cr 0 - 2.00 Mo 0 - 0.50 V 0.40 - 0.80 Fe incl. possible impurities - ad. 100%.
  • the steel should have sufficient vanadium content to form vanadium carbides which stops excessive carbon from going into solid solution at the austenitisation temperature range.
  • the carbon content and vanadium content should be balanced so that the equilibrium carbon content is optimal at the chosen austenitisation temperature.
  • Such a composition is shown in Table 1.
  • Vanadium alloyed bearing steel according to the invention C Si Mn Cr Ni Mo V min 0.60 0 0 0 0 0.25 max 1.10 2.10 2.00 2.00 2.00 0.75 1.00
  • a graph illustrating the mole percentage of phases in equilibrium versus temperature is shown for a steel according to Table 2.
  • a carbide VC
  • Fig. 2 the corresponding graph illustrates that steel B does not have this fraction of carbides.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)
  • Rolling Contact Bearings (AREA)

Abstract

An improved vanadium alloyed bearing steel having the following alloying elements, in weight-%: C 0.60 - 1.10 Si 0 - 2.10 Mn 0 - 2.00 Ni 0 - 2.00 Cr 0 - 2.00 Mo 0 - 0.75 V 0.25 - 1.00 Fe incl. possible impurities - ad. 100%.

Description

    Technical field
  • The present invention relates to an improved vanadium alloyed bearing steel.
  • Background
  • The hardness after martensitic hardening of a soft annealed bearing steel, e.g. AISE 52100 is highly dependent on the carbon content in solid solution and thus the austenitisation conditions for a given quench. A higher austenitisation temperature or longer time leads to more dissolution of carbides. The optimum carbon content in solid solution to give the highest hardness is considered to be somewhere between 0.6 to 0.8 weight% for an oil quenched component. A lower carbon content will give a softer martensite. A higher carbon content will lead to an increased retained austenite content which would decrease the hardness and give a disadvantageous martensite morphology. Furthermore, a too large amount of retained austenite will give poor structural stability.
  • Hardened bearing steels are often subjected to wear. To improve wear properties it is necessary to maximize the hardness. However, this could also be further improved by introducing a fraction of hard carbides such as VC.
  • The toughness of a component made from a bearing steel is relatively low. This could result in catastrophically failure and it would therefore be appreciated to increase the toughness. This could be achieved by alloying with Ni which is an element that improves the toughness.
  • Structural stability is important for critical applications and could be improved by Si alloying. Si retards the precipitation of carbide during tempering and thus improves the stability. This could also be beneficial for reducing tempering embrittlement since the precipitation of grain boundary carbides could be reduced.
  • Large components require a high hardenability to enable thorough hardening. The hardenability could be increased with alloying additions.
  • The Invention
  • The object of the invention is to provide a steel designed to exhibit greater tolerances in austenitising temperature and time to give optimum carbon content.
  • This is achieved with the steel according to the present invention, having the following analysis, in weight-%:
    C 0.60 - 1.10
    Si 0   - 2.10
    Mn 0   - 2.00
    Ni 0   - 2.00
    Cr 0   - 2.00
    Mo 0   - 0.75
    V 0.25 - 1.00
    Fe incl. possible impurities - ad. 100%.
  • By alloying with carbide formers, preferably V and also Cr, compared to standard bearing steels, an optimal carbon content is obtained. A higher wear resistance is obtained because of the presence hard VC carbides. Improved toughness can be obtained by Ni addition and a high structural stability can be obtained with Si additions. The required hardenability is balanced by adding Cr, Mo and Mn.
  • According to one embodiment of the invention the steel has the following analysis, in weight-%:
    C 0.60 - 1.00
    Si 0.40 - 2.10
    Mn 0.10 - 1.00
    Ni 0.50 - 2.00
    Cr 0   - 2.00
    Mo 0   - 0.50
    V 0.25 - 1.00
    Fe incl. possible impurities - ad. 100%.
  • According to another embodiment of the invention the steel has the following analysis, in weight-%:
    C 0.75 - 0.95
    Si 0.80 - 1.80
    Mn 0.10 - 1.00
    Ni 0.50 - 1.50
    Cr 0   - 2.00
    Mo 0   - 0.50
    V 0.40 - 0.80
    Fe incl. possible impurities - ad. 100%.
  • Brief description of the Drawings
  • The invention will be described more in detail below with reference to the accompanying drawings, in which
  • Fig. 1 shows mole-% of phases in equilibrium versus temperature for steel A,
  • Fig. 2 shows a graph corresponding to Fig. 1, for a steel B,
  • Fig. 3 shows the carbon content in the austenite versus temperature for the steel A, and
  • Fig. 4 shows a graph corresponding to Fig. 3 for the steel B.
  • Description of preferred embodiments
  • The steel should have sufficient vanadium content to form vanadium carbides which stops excessive carbon from going into solid solution at the austenitisation temperature range. The carbon content and vanadium content should be balanced so that the equilibrium carbon content is optimal at the chosen austenitisation temperature. Such a composition is shown in Table 1.
    Vanadium alloyed bearing steel according to the invention
    C Si Mn Cr Ni Mo V
    min 0.60 0 0 0 0 0 0.25
    max 1.10 2.10 2.00 2.00 2.00 0.75 1.00
    Example 0.85 1.30 0.30 1.40 1.00 - 0.60
  • A theoretical calculation using the thermodynamic simulation program Thermocalc shows the effect of a vanadium addition. The addition will lead to the formation of a carbide that is stable at higher temperatures. Two steels are compared; steel A with a vanadium addition and steel B without vanadium. The compositions are shown in Table 2.
    Chemical composition in weight-%.
    Steel C Si Mn Cr Ni Mo V
    A
    0,85 1,30 0,30 1,40 1,00 - 0,60
    B 0,85 1,30 0,30 1,40 1,00 - -
  • In Fig. 1 a graph illustrating the mole percentage of phases in equilibrium versus temperature is shown for a steel according to Table 2. For this vanadium steel a carbide (VC) is stable up to approximately 1200°C. In Fig. 2, the corresponding graph illustrates that steel B does not have this fraction of carbides.
  • The fact that vanadium forms carbides which are stable at a higher temperature results in a wider temperature range for dissolving carbides and thus saturating the austenitic matrix with carbon. This is schematically shown in Figs. 3 and 4, wherein the equilibrium carbon content in austenite (the rest of the carbon is bonded in carbides) is plotted versus temperature. For steel A, Fig. 3, the maximum carbon content (equilibrium) in austenite for a austenitisation temperature of 830-900°C is 0.72 to 0.74 weight-%. For steel B, Fig. 4, the same temperature range gives a carbon content of between 0.75 and 0.85 weight-%. This means that for steel B the time at austenitisation temperature is much more critical for the carbon content obtained. Furthermore, steel B will not have the fraction of hard vanadium carbides which is beneficial for the wear properties.

Claims (3)

  1. An improved vanadium alloyed bearing steel having the following analysis, in weight-%: C 0.60 - 1.10 Si 0   - 2.10 Mn 0   - 2.00 Ni 0   - 2.00 Cr 0   - 2.00 Mo 0   - 0.75 V 0.25 - 1.00 Fe incl. possible impurities - ad. 100%.
  2. A steel according to claim 1 having the following analysis, in weight-%: C 0.60 - 1.00 Si 0.40 - 2.10 Mn 0.10 - 1.00 Ni 0.50 - 2.00 Cr 0   - 2.00 Mo 0   - 0.50 V 0.25 - 1.00 Fe incl. possible impurities - ad. 100%.
  3. A steel according to claim 1 having the following alloying elements, in weight-%: C 0.75 - 0.95 Si 0.80 - 1.80 Mn 0.10 - 1.00 Ni 0.50 - 1.50 Cr 0   - 2.00 Mo 0   - 0.50 V 0.40 - 0.80 Fe incl. possible impurities - ad. 100%.
EP98850125A 1997-08-01 1998-07-30 Vanadium alloyed bearing steel Withdrawn EP0894873A1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE9702851 1997-08-01
SE9702851A SE9702851D0 (en) 1997-08-01 1997-08-01 Vanadium alloyed bearing steel

Publications (1)

Publication Number Publication Date
EP0894873A1 true EP0894873A1 (en) 1999-02-03

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EP98850125A Withdrawn EP0894873A1 (en) 1997-08-01 1998-07-30 Vanadium alloyed bearing steel

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EP (1) EP0894873A1 (en)
JP (1) JPH11117040A (en)
CN (1) CN1211634A (en)
SE (1) SE9702851D0 (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1035226A1 (en) * 1999-03-10 2000-09-13 Ovako Steel AB An improved bearing steel

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8894779B2 (en) 2010-11-29 2014-11-25 Jfe Steel Corporation Bearing steel being excellent both in post spheroidizing-annealing workability and in post quenching-tempering hydrogen fatigue resistance property
WO2012073488A1 (en) 2010-11-29 2012-06-07 Jfeスチール株式会社 Bearing steel exhibiting excellent machinability after spheroidizing annealing and excellent resistance to hydrogen fatigue after quenching/tempering
CN102399533A (en) * 2011-09-26 2012-04-04 宁国市东方碾磨材料有限责任公司 Wear-resistant corrosion-resistant nano grinding material and preparation method thereof
CN111926255A (en) * 2020-08-11 2020-11-13 江苏联峰实业有限公司 High-carbon chromium bearing steel and production method thereof
CN112011739B (en) * 2020-08-27 2021-08-06 江苏大学 High-toughness iron alloy and preparation method and application thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0458646A1 (en) * 1990-05-23 1991-11-27 Aichi Steel Works, Ltd. Bearing steel
JPH06287708A (en) * 1993-03-30 1994-10-11 Kawasaki Steel Corp Bearing stress excellent in property of retarding microstructural change due to repeated stress load
JPH07216508A (en) * 1994-02-04 1995-08-15 Daido Steel Co Ltd Bearing steel
JPH07238341A (en) * 1994-02-24 1995-09-12 Daido Steel Co Ltd Steel for induction hardening, excellent in high bearing fatigue strength

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0458646A1 (en) * 1990-05-23 1991-11-27 Aichi Steel Works, Ltd. Bearing steel
JPH06287708A (en) * 1993-03-30 1994-10-11 Kawasaki Steel Corp Bearing stress excellent in property of retarding microstructural change due to repeated stress load
JPH07216508A (en) * 1994-02-04 1995-08-15 Daido Steel Co Ltd Bearing steel
JPH07238341A (en) * 1994-02-24 1995-09-12 Daido Steel Co Ltd Steel for induction hardening, excellent in high bearing fatigue strength

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 095, no. 001 28 February 1995 (1995-02-28) *
PATENT ABSTRACTS OF JAPAN vol. 095, no. 011 26 December 1995 (1995-12-26) *
PATENT ABSTRACTS OF JAPAN vol. 096, no. 001 31 January 1996 (1996-01-31) *
WEGST C.W.: "Stahlschlüssel", 1986, VERLAG STAHLSCHLÜSSEL WEGST, MARBACH, GERMANY, XP002083413 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1035226A1 (en) * 1999-03-10 2000-09-13 Ovako Steel AB An improved bearing steel

Also Published As

Publication number Publication date
CN1211634A (en) 1999-03-24
SE9702851D0 (en) 1997-08-01
JPH11117040A (en) 1999-04-27

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