US20110073222A1 - Heat-Treatment Process for a Steel - Google Patents

Heat-Treatment Process for a Steel Download PDF

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Publication number
US20110073222A1
US20110073222A1 US12/681,762 US68176208A US2011073222A1 US 20110073222 A1 US20110073222 A1 US 20110073222A1 US 68176208 A US68176208 A US 68176208A US 2011073222 A1 US2011073222 A1 US 2011073222A1
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United States
Prior art keywords
component
steel
induction heating
martensite
hardening
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US12/681,762
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English (en)
Inventor
Ingemar Strandell
Peter Neuman
Mikael B. Sundqvist
Steven Lane
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SKF AB
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SKF AB
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Assigned to AKTIEBOLAGET SKF reassignment AKTIEBOLAGET SKF ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: LANE, STEVEN, SUNDQVIST, MIKAEL B., NEUMANN, PETER, STRANDELL, INGEMAR
Publication of US20110073222A1 publication Critical patent/US20110073222A1/en
Abandoned legal-status Critical Current

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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
    • C21D1/06—Surface hardening
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
    • 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
    • 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
    • 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
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/02—Mechanical properties
    • F16C2202/04—Hardness
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates generally to the field of metallurgy and a heat-treatment process for a steel component.
  • the process induces a compressive residual stress (CRS) in a surface region of the component with the corollary of an improvement in mechanical properties, for example fatigue performance.
  • CRS compressive residual stress
  • Shot peening involves bombarding the surface of the metal component with rounded shot to locally harden surface layers.
  • this process results in a rough surface finish which can create other problems and therefore additional steps need to be taken to improve the surface finish. This adds to productions costs.
  • Case-hardening may also be achieved by heating the steel component in a carbonaceous medium to increase the carbon content, followed by quenching and tempering.
  • This thermochemcial process is known as carburizing and results in a surface chemistry that is quite different from that of the core of the component.
  • the hard surface layer may be formed by rapidly heating the surface of a medium/high carbon steel to above the ferrite/austenite transformation temperature, followed by quenching and tempering to result in a hard surface layer. Heating of the surface has traditionally been achieved by flame hardening, although laser surface-hardening and induction hardening are now often used.
  • Induction hardening involves heating the steel component by exposing it to an alternating magnetic field to a temperature within or above the transformation range, followed by quenching.
  • Heating occurs primarily in the surface of the component, with the core of the component remaining essentially unaffected.
  • the penetration of the field is inversely proportional to the frequency of the field and thus the depth of the hardening can be adjusted in a simple manner.
  • the penetration of the field also depends on the power density and interaction time.
  • Through-hardened components differ from case-hardened components in that the hardness is uniform or substantially uniform throughout the component. Through-hardened components are also generally cheaper to manufacture than case-hardened components because they avoid the complex heat-treatments associated with carburizing, for example.
  • the steel grades that are used depend on the component section thickness. For components having a wall thickness of up to about 20 mm, DIN 100Cr6 is typically used. For larger section sizes, higher alloyed grades are used such as for example, DIN 100CrMo7-3, DIN 100CrMnMo7, DIN 100CrMo7-4, or DIN 100CrMnMo8.
  • the martensite through-hardening process involves austenitising the steel prior to quenching below the martensite start temperature.
  • the steel may then be low-temperature tempered to stabilize the microstructure.
  • the martensite through-hardening process typically results in a compressive residual stress (CRS) of from 0 to +100 MPa between the WCS (working contact surface) and down to an approximately 1.5 mm depth below the WCS.
  • CCS compressive residual stress
  • the bainite through-hardening process involves austenitising the steel prior to quenching above the martensite start temperature. Following quenching, an isothermal bainite transformation is performed. Bainite through-hardening is sometimes preferred in steels instead of martensite through-hardening. This is because a bainitic structure may possess superior mechanical properties, for example toughness and crack propagation resistance.
  • the bainite though-hardening process results in a CRS of from 0 to ⁇ 100 MPa between the WCS and down to an approximately 1.5 mm depth below the WCS.
  • the present invention aims to address at least some of the problems associated with the prior art.
  • the present invention provides a process for inducing a compressive residual stress in a surface region of a steel component, the process comprising a heat-treatment having the following steps:
  • said at least part of the component is preferably heated to a depth of from 0.5 to 3 mm, more preferably from 0.75 to 2.5 mm, still more preferably from 1 to 2 mm. That is the induction heating preferably penetrates to a depth of at least about 0.5 mm and up to a maximum depth of up to about 3 mm. Induction heating to such depths, in conjunction with the other steps of the process, has been found to induce a compressive residual stress (CRS) in a surface region of the component with the corollary of an improvement in mechanical properties, for example fatigue performance.
  • CRS compressive residual stress
  • the surface of said at least part of the component preferably reaches a temperature of from 1000 to 1100° C., more preferably from 1020 to 1080° C.
  • the surface microstructure comprises martensite or at least martensite as the predominant phase.
  • the process may further comprising, after step (iii):
  • the present invention provides a process for inducing a compressive residual stress in a surface region of a steel component, the process comprising a heat-treatment having the following steps:
  • said at least part of the component is preferably heated to a depth of from 1 to 6 mm, more preferably from 2 to 5 mm.
  • the surface of said at least part of the component preferably reaches a temperature of from 900 to 1000° C., more preferably from 920 to 980° C.
  • the surface microstructure comprises martensite or at least martensite as the predominant phase.
  • the component is preferably subjected to tempering, preferably low temperature tempering at a temperature of up to about 250° C.
  • the present invention involves either pre- or post-induction processing in relation to a through-hardening heat-treatment process in order to introduce thermal strains and/or phase transformation strains such that a large compressive residual stress (CRS) is achieved.
  • CRS compressive residual stress
  • the present invention enables a steel product to be produced with a CRS in the range of ⁇ 200 to ⁇ 900 MPa at the near surface, typically being maintained at ⁇ 300 to ⁇ 500 MPa at 1 mm depth below the surface.
  • the near surface is typically less than 300 microns below the heat-treated surface.
  • the process is applicable to all though-hardening steel grades.
  • the steel will typically be a medium (0.3 to 0.8% carbon) or high carbon steel (>0.8% carbon) such as a high carbon chromium steel or a low alloy bearing steel.
  • the induction heating is preferably medium and/or high frequency induction heating and is advantageously performed at a frequency of from 2-100 kHz.
  • the interaction time and power level may be varied having regard to the component size and desired depth.
  • the inducting heating is preferably followed by quenching, for example to room temperature (20 to 25° C.) or even to 0° C. or less.
  • the induction heating step advantageously achieves rapid surface heating using medium and/or high frequency induction heating (preferably at a frequency of 2-100 kHz, more preferably 5 to 20 kHz) to a depth of typically 0.5 to 3 mm, more typically 1 to 2 mm.
  • the surface preferably reaches a temperature of from 1000 to 1100° C., more preferably from 1020 to 1080° C.
  • the component is preferably quenched using, for example, oil or a polymer solution in order to ‘freeze’ the effect of the surface conditioning.
  • the induction heating step advantageously achieves rapid surface heating using medium or high frequency induction heating (preferably at a frequency of 2-100 kHz, more preferably 40 to 130 kHz) to a depth of typically 1 to 6 mm, more typically 2 to 5 mm.
  • the surface preferably reaches a temperature of from 900 to 1000° C., more preferably from 920 to 980° C.
  • the component is preferably quenched using, for example, oil or a polymer solution in order to ‘freeze’ the effect of the surface conditioning.
  • the process of either the first or second aspects involves a martensite through-hardening step, then conventional processes may be relied on.
  • the martensite through-hardening step will typically comprise austenitising the steel and subsequently quenching the steel below the martensite start temperature (Ms is typically 180 to 220° C., more typically 190 to 200° C., still more typically approximately 200° C.). Quenching may be performed using, for example, molten salt.
  • the component is preferably post-quenched in, for example, cold water to promote further austenite to martensite transformation.
  • the component is preferably subjected to low temperature tempering to stabilize the microstructure.
  • the bainite through-hardening step will typically comprise austenitising the steel and quenching the steel above the martensite start temperature (Ms is typically 180 to 220° C., more typically 190 to 200° C., still more typically approximately 200° C.). Quenching may be performed using, for example, oil or molten salt. This is followed by an isothermal bainite transformation, which is preferably performed at a temperature in the range of from 200 to 250° C., more preferably from 210 to 240° C. The steel is preferably held within this temperature range for from 1 to 30 hours, more preferably from 2.5 to 20 hours depending on the steel grade and section thickness.
  • the steel is preferably austenitised (prior to the quench below/above the martensite start temperature).
  • Austenitising is well known in the art.
  • the inventors have found (particularly in relation to the first aspect) that applying through-hardening using a 10-50° C. lower hardening temperature than what would normally be used (e.g. 840 to 890° C.) further promotes the CRS build-up. This is believed to be because the core is under-austenitised in relation to the slightly over-austenitised surface portion. Therefore, the phase transformation differences will be more pronounced.
  • austenitising is preferably performed at a temperature in the range of from 790 to 890° C., more preferably from 790 to 880° C., still more preferably from 790 to 840° C.
  • the steel is preferably held within this temperature range for from 10 to 70 minutes, more preferably from 20 to 60 minutes.
  • the austenitisation is typically performed in an atmosphere furnace where the component can reach a homogeneous temperature throughout its cross-section. Consequently, a homogenous austenitisation and cementite dissolution is advantageously achieved.
  • the chemical composition of the steel remains essentially unchanged. In other words, the process does not need to involve a thermochemical enrichment process. This is in contrast conventional case-hardening treatments.
  • the final microstructure comprises either (tempered) martensite or bainite as the major phase or a combination of the two. Cementite may also be present. In general, the microstructure appears to be essentially homogeneous from the surface to the core. However, some inherent segregation of alloying elements (e.g. N, C, Cr, Si, Mn) may be present.
  • alloying elements e.g. N, C, Cr, Si, Mn
  • the hardness within the surface is typically 50-75 HRC, more typically 56-68 HRC.
  • the retained austenite content is typically 0-30%.
  • the underlying core also comprises either martensite and/or bainite or mixtures thereof.
  • the hardness of the core microstructure is typically greater than 50 HRC, more typically greater than 56 HRC.
  • the hardness of the core generally does not exceed 67 HRC, more typically it does not exceed 64 HRC.
  • the retained austenite content is typically 0-20%.
  • the heat-treatment steps result in a transition zone visible both in hardness and in microstructure.
  • the component may be any type of steel component.
  • component for a bearing such as a raceway or a rolling element.
  • the present invention enables a product to be produced with a CRS in the range of ⁇ 200 to ⁇ 900 MPa at the near surface, being maintained at ⁇ 300 to ⁇ 500 MPa at 1 mm depth below the surface.
  • a CRS profile compares very favourably to conventional components.
  • the present invention provides a component formed from steel, wherein the component comprises through-hardened martensite and/or through-hardened bainite and has a substantially homogeneous chemical composition and microstructure, at least a part of the component having a compressive residual stress profile comprising ⁇ 200 to ⁇ 900
  • the present invention provides a process involving a combination of the first and second aspects.
  • a first induction heating step corresponding to the first aspect, introduces mainly a carbide dissolution gradient that affects the phase transformation characteristics. This is followed by martensite and/or bainite though-hardening.
  • a second induction heating step corresponding to the second aspect, is performed to introduce thermal strains between the surface and the core.
  • FIG. 1 is a plot showing the compressive residual stress profile for the component of Example 1;
  • FIGS. 2 a and 2 b are micrographs showing the surface (a) and core (b) microstructures for the component of Example 1;
  • FIG. 3 is a plot showing the hardness profile for the component of Example 1 after the induction heating step but before the bainite through-hardening step;
  • FIG. 4 is a plot showing the hardness profile for the component of Example 1 after the induction heating and bainite through-hardening steps;
  • FIG. 5 is a plot showing the compressive residual stress profile for the component of Example 2 after the heat-treatment and compared to standard martensite and standard bainite;
  • FIGS. 6 a , 6 b and 6 c are micrographs showing the surface (a), transitional zone (b), and core (c) microstructures for the component of Example 2 after the bainite through-hardening and induction heating steps;
  • FIG. 7 is a plot showing the hardness profile for the component of Example 2 after the bainite through-hardening and induction heating steps.
  • FIG. 8 is a plot showing the compressive residual stress profile for the component of Example 3 after the martensite through-hardening and induction heating steps.
  • FIG. 1 is a plot showing the compressive residual stress profile for the component of Example 1.
  • the plot shows a near surface CRS of ⁇ 300 to ⁇ 800 MPa.
  • the CRS is maintained at ⁇ 300 down to at least 1.2 mm.
  • FIGS. 2 a and 2 b are micrographs showing the surface (a) and core (b) microstructures for the component of Example 1.
  • the micrographs show a bainite microstructure.
  • the surface microstructure is slightly coarser with less residual carbides (cementite) than the core.
  • FIG. 3 is a plot showing the hardness profile for the component of Example 1 after pre-induction process only
  • FIG. 4 is a plot showing the hardness profile for the component of Example 1 after the complete process.
  • FIG. 5 is a plot showing the compressive residual stress profile for the component of Example 2 after the heat-treatment and compared to standard martensite and standard bainite.
  • FIGS. 6 a , 6 b and 6 c are micrographs showing the surface (a), transitional zone (b), and core (c) microstructures for the component of Example 2 after the bainite through-hardening and induction heating steps.
  • the micrographs show a martensite surface microstructure, a tempered bainite microstructure in the transition zone, and a bainite core microstructure.
  • FIG. 7 is a plot showing the hardness profile for the component of Example 2 after the bainite through-hardening and induction heating steps.
  • the hardness profile shows a transition zone.
  • FIG. 8 is a plot showing the CRS profile for the component of Example 3 after the martensite through-hardening and induction heating steps with different levels of hoop stress.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • General Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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US12/681,762 2007-10-04 2008-10-03 Heat-Treatment Process for a Steel Abandoned US20110073222A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
GBGB0719457.4A GB0719457D0 (en) 2007-10-04 2007-10-04 Heat-treatment process for a steel
GB0719457.4 2007-10-04
PCT/SE2008/000544 WO2009045146A1 (en) 2007-10-04 2008-10-03 Heat-treatment process for a steel

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US (1) US20110073222A1 (zh)
EP (1) EP2198061A4 (zh)
JP (1) JP5535922B2 (zh)
CN (1) CN101868556B (zh)
GB (1) GB0719457D0 (zh)
WO (1) WO2009045146A1 (zh)

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WO2014031051A1 (en) 2012-08-21 2014-02-27 Aktiebolaget Skf Method for heat treating a steel component and a steel component
EP2871254A1 (en) * 2012-09-13 2015-05-13 JFE Steel Corporation Hot-rolled steel sheet and method for manufacturing same
US20160333449A1 (en) * 2014-01-16 2016-11-17 Uddeholms Ab Stainless steel and a cutting tool body made of the stainless steel
US9617613B2 (en) * 2012-03-14 2017-04-11 Osaka University Method for manufacturing ferrous material
US10047416B2 (en) 2012-09-13 2018-08-14 Jfe Steel Corporation Hot rolled steel sheet and method for manufacturing the same
KR20180118158A (ko) * 2016-02-23 2018-10-30 슈바츠 게엠베하 열처리 방법 및 열처리 장치
US20220288469A1 (en) * 2021-03-15 2022-09-15 Tat Wong Method for manufacturing golf putter clubhead, golf putter clubhead, and golf putter

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KR20180118158A (ko) * 2016-02-23 2018-10-30 슈바츠 게엠베하 열처리 방법 및 열처리 장치
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KR102592707B1 (ko) * 2016-02-23 2023-10-20 슈바츠 게엠베하 열처리 방법 및 열처리 장치
US20220288469A1 (en) * 2021-03-15 2022-09-15 Tat Wong Method for manufacturing golf putter clubhead, golf putter clubhead, and golf putter
US11731015B2 (en) * 2021-03-15 2023-08-22 Tat Wong Method for manufacturing golf putter clubhead, golf putter club head, and golf putter

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EP2198061A4 (en) 2015-10-14
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JP5535922B2 (ja) 2014-07-02
GB0719457D0 (en) 2007-11-14

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