WO2001011096A1 - Improved bainitic steel - Google Patents

Improved bainitic steel Download PDF

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Publication number
WO2001011096A1
WO2001011096A1 PCT/GB2000/002914 GB0002914W WO0111096A1 WO 2001011096 A1 WO2001011096 A1 WO 2001011096A1 GB 0002914 W GB0002914 W GB 0002914W WO 0111096 A1 WO0111096 A1 WO 0111096A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel
temperature
microstructure
carbon
bainite
Prior art date
Application number
PCT/GB2000/002914
Other languages
French (fr)
Inventor
Kankanange Jagath Ananda Mawella
Harshad Kumar Dharamshi Hansrat Bhadeshia
Francisca Garcia Cabellero
Original Assignee
Qinetiq Limited
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 Qinetiq Limited filed Critical Qinetiq Limited
Priority to EP00949724A priority Critical patent/EP1200638B1/en
Priority to DE60028979T priority patent/DE60028979T2/en
Priority to US10/048,619 priority patent/US6884306B1/en
Priority to JP2001515341A priority patent/JP3751250B2/en
Priority to AU62999/00A priority patent/AU6299900A/en
Publication of WO2001011096A1 publication Critical patent/WO2001011096A1/en

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Classifications

    • 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
    • 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
    • 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
    • C21D1/78—Combined heat-treatments not provided for above
    • 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
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a high carbon steel having good properties of strength hardness, and resistance to heat treatments. It also relates to a method of producing such steels.
  • the inventors have determined a steel composition which has high hardness, high strength and high ductility and have further devised a method to produce such a steel.
  • the invention comprised a steel having a composition by weight of carbon 0.6 to 1.1%, silicon 1.5 to 2.0%, manganese 1.8 to 4.0%>, nickel 0 to 3%, chromium 1.2 to 1.4%, molybdenum 0.2 to 0.5%, vanadium 0.1-0.2 %, balance iron save for incidental impurities.
  • the steel may have incidental impurities which are not deliberate additions.
  • the steel has the following composition in weight percent; carbon 0.7 to 0.9%; silicon 1.5 to 1.7%; manganese 1.9 to 2.2%; chromium 1.25 to 1.4%; nickel 0 to 0.05%; molybdenum 0.25 to 0.35%; vanadium 0.1 to 0.15%, balance iron save for incidental impurities.
  • the steel is of mainly bainitic microstructure improving hardness, yield stress and ultimate tensile strength.
  • Mainly bainitic microstructure is defined as at least 50%) of bainitic structure, preferably 65% and even more preferably 85% although 95%o is achievable.
  • the rest of the structure comprises retained austenite.
  • Figure 1 shows the microstructure showing a mixture martensite and austenite only, following a homogenisation heat treatment at 1200°C for two days.
  • Figure 2 shows a microstructure of a steel according to the invention having a bainitic structure.
  • Figure 3 shows hardness against three regimes of heat treatment.
  • FIG. 4 shows a time - temperature - transformation (TTT) diagram of a steel according to the invention.
  • Figures 5 and 6 show compression and tension curves for microstructure of the steel formed following isothermal transformation at 190°C for two weeks.
  • Figure 7 shows the microstructure formed at 190°C for two weeks from as-cast material.
  • Figure 1 shows the microstructure showing a mixture martensite and austenite only, following a homogenisation heat treatment at 1200°C for two days.
  • Table 1 lists all the temperatures holding times and hardness values of the micro structures obtained after isothermal decomposition of austenite Temperature/ Time Hv (kgf/mm2) Temperature/ Time Hv (kgf/mm2) (weeks) (weeks)
  • Figure 2 shows microstructure of the steel formed at 190°C for two weeks and shows a mixture of bainitic ferrite and carbon-enriched retained austenite.
  • Figure 3 shows a plot of hardness against isothermal transformation temperature.
  • the increase in hardness detected at 350°C after two weeks of isothermal treatment suggests that the start bainite temperature should be at this level.
  • the microstructures formed at 150°, 350° and 400° are different from those obtained between 190°C and 300°C for two weeks and tempering at 400°C for an hour has shown that the 150°C and 400°C microstructures are martensite whereas the 190-300°C microstructures were bainite.
  • a reduction the hardness after low temperature tempering usually confirms the presence of martensite instead of bainite in a microstructure.
  • the microstructures formed at 450°C and 500°C are mixture of pearlite and retained austenite.
  • the carbon composition of austenite after bainite transformation is much lower than expected from equilibrium and there is not significant enrichment of the residual austenite. This is because the carbide particles precipitate inside the plates of ferrite and lower bainite is formed instead of upper bainite.
  • the carbides in the lower bainite should be extremely fine.
  • the fine microstructure of lower bainite is expected to be much tougher than upper bainite in spite of fact that it should be stronger.
  • the lower bainite structure is formed when isothermal transformation temperatures of up to around 350°C are used.
  • the upper bainite structure is formed when isothermal transformation temperatures of over around 350°C are used.
  • Figure 4 shows a schematic representation of the TTT diagram of the steel.
  • Figures 5 and 6 show results of testing the compression and tension curves of samples which have been isothermally transformed at 190°C for two weeks to produce bainite.
  • the material has very high strength under both compression and tension. Charpy tests in this cast and heat treated condition gave absorbed energy values of only 5+/- 1 J.
  • FIG. 7 shows the microstructure obtained at 190°C for two weeks from fresh material; segregation is clear in the sample and the volume fraction of austenite appears to be higher. This microstructure was tested under compression and no significant difference from the yield strength estimated with homogenised sample was found. None the less toughness may be poorer because of the blocky austenite present in the dendrite microstructure.
  • Samples are homogenised at 1200°C for two days and then isothermally transformed to pearlite or bainite before cooling to room temperature. Then reheated to 1000°C to refme austenite grain size and then transformed again to bainite.

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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)
  • Heat Treatment Of Steel (AREA)

Abstract

A mainly bainitic steel having the following composition in weight percent: carbon 0.6-1.1; silicon 1.5 to 2.0; manganese 1.8 to 4.0; chromium 1.2 to 1.4; nickel 0-3; molybdenum 0.2 to 0.5; vanadium 0.1 to 0.2, balance iron save for incidental impurities.

Description

Improved bainitic steel
The invention relates to a high carbon steel having good properties of strength hardness, and resistance to heat treatments. It also relates to a method of producing such steels.
It is a continuing desire to improve the strength of high carbon, high silicon steels.
The inventors have determined a steel composition which has high hardness, high strength and high ductility and have further devised a method to produce such a steel.
The invention comprised a steel having a composition by weight of carbon 0.6 to 1.1%, silicon 1.5 to 2.0%, manganese 1.8 to 4.0%>, nickel 0 to 3%, chromium 1.2 to 1.4%, molybdenum 0.2 to 0.5%, vanadium 0.1-0.2 %, balance iron save for incidental impurities.
The steel may have incidental impurities which are not deliberate additions.
Preferably the steel has the following composition in weight percent; carbon 0.7 to 0.9%; silicon 1.5 to 1.7%; manganese 1.9 to 2.2%; chromium 1.25 to 1.4%; nickel 0 to 0.05%; molybdenum 0.25 to 0.35%; vanadium 0.1 to 0.15%, balance iron save for incidental impurities.
Preferably the steel is of mainly bainitic microstructure improving hardness, yield stress and ultimate tensile strength. Mainly bainitic microstructure is defined as at least 50%) of bainitic structure, preferably 65% and even more preferably 85% although 95%o is achievable. The rest of the structure comprises retained austenite.
The invention will now be described by way of example only and with reference to the following figures of which: Figure 1 shows the microstructure showing a mixture martensite and austenite only, following a homogenisation heat treatment at 1200°C for two days.
Figure 2 shows a microstructure of a steel according to the invention having a bainitic structure.
Figure 3 shows hardness against three regimes of heat treatment.
Figure 4 shows a time - temperature - transformation (TTT) diagram of a steel according to the invention.
Figures 5 and 6 show compression and tension curves for microstructure of the steel formed following isothermal transformation at 190°C for two weeks.
Figure 7 shows the microstructure formed at 190°C for two weeks from as-cast material.
Steel having the following composition by weight of carbon 0.79%>, silicon 1.59%, manganese 1.94%, chromium 1.33%, molybdenum 0.3%>, vanadium 0.11 %, nickel 0.02%) was supplied as cast 12 mm diameter bar. It was homogenised at 1200° C for two days in evacuated quartz capsules and subsequently air-cooled. 3 mm diameter rods were austenitised for 15 min at 1000°C isothermally transformed at temperature ranging from 150 to 500°C for different times and subsequently quenched into water. In all the figures and results given steels were formulated with this composition.
Figure 1 shows the microstructure showing a mixture martensite and austenite only, following a homogenisation heat treatment at 1200°C for two days.
Table 1 lists all the temperatures holding times and hardness values of the micro structures obtained after isothermal decomposition of austenite Temperature/ Time Hv (kgf/mm2) Temperature/ Time Hv (kgf/mm2) (weeks) (weeks)
150°C/0.06 734 300°C/2 442
150°C/ 1 761 350°C/1 409
150°C/2 763 350°C/2 745
190°C/ 1 618 400°C/1 732
190°C/2 648 400°C/2 769
250°C/ 1 617 450°C/1 642
250°C/2 654 500°C/1 476
300°C/ 1 434
Figure 2 shows microstructure of the steel formed at 190°C for two weeks and shows a mixture of bainitic ferrite and carbon-enriched retained austenite.
Figure 3 shows a plot of hardness against isothermal transformation temperature. The increase in hardness detected at 350°C after two weeks of isothermal treatment suggests that the start bainite temperature should be at this level. The microstructures formed at 150°, 350° and 400° are different from those obtained between 190°C and 300°C for two weeks and tempering at 400°C for an hour has shown that the 150°C and 400°C microstructures are martensite whereas the 190-300°C microstructures were bainite. A reduction the hardness after low temperature tempering usually confirms the presence of martensite instead of bainite in a microstructure. The microstructures formed at 450°C and 500°C are mixture of pearlite and retained austenite. Additionally some proeutectoid cementite with plate morphology seems to have been formed. A fully bainitic microstructure with extraordinary hardness and resistance to tempering is formed at 190° C when transformed for two weeks. Also the maximum volume fraction of bainite obtained increases with the decreasing transformation temperature.
According to the results from the inventors, the carbon composition of austenite after bainite transformation is much lower than expected from equilibrium and there is not significant enrichment of the residual austenite. This is because the carbide particles precipitate inside the plates of ferrite and lower bainite is formed instead of upper bainite. The carbides in the lower bainite should be extremely fine. The fine microstructure of lower bainite is expected to be much tougher than upper bainite in spite of fact that it should be stronger. The lower bainite structure is formed when isothermal transformation temperatures of up to around 350°C are used. The upper bainite structure is formed when isothermal transformation temperatures of over around 350°C are used.
Figure 4 shows a schematic representation of the TTT diagram of the steel.
Figures 5 and 6 show results of testing the compression and tension curves of samples which have been isothermally transformed at 190°C for two weeks to produce bainite. The material has very high strength under both compression and tension. Charpy tests in this cast and heat treated condition gave absorbed energy values of only 5+/- 1 J.
A homogenisation heat treatment is necessary in order to get a uniform and fully bainitic microstructure by isothermal heat treatment. Figure 7 shows the microstructure obtained at 190°C for two weeks from fresh material; segregation is clear in the sample and the volume fraction of austenite appears to be higher. This microstructure was tested under compression and no significant difference from the yield strength estimated with homogenised sample was found. Never the less toughness may be poorer because of the blocky austenite present in the dendrite microstructure.
A different homogenisation heat treatment avoids the formation of martensite. Samples are homogenised at 1200°C for two days and then isothermally transformed to pearlite or bainite before cooling to room temperature. Then reheated to 1000°C to refme austenite grain size and then transformed again to bainite.

Claims

Claims
1. A mainly bainitic steel having the following composition in weight percent; carbon 0.6 - 1.1; silicon 1.5 to 2.0; manganese 1.8 to 4.0; chromium 1.2 to 1.4; nickel 0-3; molybdenum 0.2 to 0.5; vanadium 0.1 to 0.2, balance iron save for incidental impurities.
2. A steel as claimed in claim 1 having the following composition in weight percent; carbon 0.7 to 0.9; silicon 1.5 to 1.7; manganese 1.9 to 2.2; chromium 1.25 to 1.4; nickel 0 to 0.05; molybdenum 0.25 to 0.35; vanadium 0.1 to 0.15 , balance iron save for incidental impurities.
3. A method of heat treating a steel to produce a mainly bainitic structure as claimed in claim 1 or claim 2 comprising the steps of: homogenising the steel at a temperature of at least 1150°C for at least 24 hours; air cooling the steel at a temperature between 190 and 250°C; subjecting the steel to a temperature between 900°C and 1000°C; isothermally transforming the steel at a temperature between 190°C and 260°C for 1 to 3 weeks.
PCT/GB2000/002914 1999-08-04 2000-08-02 Improved bainitic steel WO2001011096A1 (en)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP00949724A EP1200638B1 (en) 1999-08-04 2000-08-02 Method for producing an improved bainitic steel
DE60028979T DE60028979T2 (en) 1999-08-04 2000-08-02 METHOD FOR PRODUCING AN IMPROVED BAINITIC STEEL
US10/048,619 US6884306B1 (en) 1999-08-04 2000-08-02 Baintic steel
JP2001515341A JP3751250B2 (en) 1999-08-04 2000-08-02 Improved bainite steel
AU62999/00A AU6299900A (en) 1999-08-04 2000-08-02 Improved bainitic steel

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
GB9918240A GB2352726A (en) 1999-08-04 1999-08-04 A steel and a heat treatment for steels
GB9918240.4 1999-08-04

Publications (1)

Publication Number Publication Date
WO2001011096A1 true WO2001011096A1 (en) 2001-02-15

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Country Status (8)

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US (1) US6884306B1 (en)
EP (1) EP1200638B1 (en)
JP (1) JP3751250B2 (en)
AT (1) ATE331051T1 (en)
AU (1) AU6299900A (en)
DE (1) DE60028979T2 (en)
GB (1) GB2352726A (en)
WO (1) WO2001011096A1 (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010013054A2 (en) 2008-07-31 2010-02-04 The Secretary Of State For Defence Bainite steel and methods of manufacture thereof
WO2013117953A1 (en) * 2012-02-10 2013-08-15 Ascometal Process for making a steel part, and steel part so obtained
CN111566246A (en) * 2018-01-11 2020-08-21 罗伯特·博世有限公司 Component for contact with hydrogen

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5463662B2 (en) * 2008-03-10 2014-04-09 Ｊｆｅスチール株式会社 Bearing steel excellent in rolling fatigue characteristics and manufacturing method thereof
EP2268841A1 (en) 2008-03-25 2011-01-05 Aktiebolaget SKF A bearing component
US8066828B2 (en) * 2008-06-18 2011-11-29 Tata Consultancy Services, Ltd. Method for efficient heat treatment of steel
JP5463675B2 (en) * 2009-01-30 2014-04-09 Ｊｆｅスチール株式会社 Bearing steel and manufacturing method thereof
WO2011023988A2 (en) * 2009-08-24 2011-03-03 The Secretary Of State For Defence Armour
WO2012031771A1 (en) 2010-09-09 2012-03-15 Tata Steel Uk Limited Super bainite steel and method for manufacturing it
EP2834378B1 (en) * 2012-04-04 2016-02-24 Aktiebolaget SKF Steel alloy
CN103160667B (en) * 2013-03-15 2014-04-02 武汉科技大学 High-strength intermediate-carbon ultrafine bainitic steel and preparation method thereof
CN103468906A (en) * 2013-09-17 2013-12-25 北京科技大学 Process for preparing 2000 MPa nano-scale bainitic steel through low temperature rolling
PL228168B1 (en) 2014-08-18 2018-02-28 Politechnika Warszawska Method for producing nanocrystalline structure in the bearing steel
GB201604910D0 (en) * 2016-03-23 2016-05-04 Rolls Royce Plc Nanocrystalline bainitic steels, shafts, gas turbine engines, and methods of manufacturing nanocrystalline bainitic steels
SE544951C2 (en) * 2021-06-29 2023-02-07 Sandvik Materials Tech Emea Ab A new super bainite steel, method for manufacturing an object of said steel and an object manufactured by the method

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3519497A (en) * 1965-04-28 1970-07-07 Lorraine Escaut Sa Method for the thermal treatment of steel rails
JPH0257637A (en) * 1988-08-23 1990-02-27 Nippon Steel Corp Manufacture of spring with high fatigue strength and steel wire for spring for use therein
JPH03215623A (en) * 1990-01-19 1991-09-20 Nisshin Steel Co Ltd Production of tough high strength steel
EP0849368A1 (en) * 1996-12-19 1998-06-24 Voest-Alpine Schienen GmbH Shaped rolled product and method of making the same

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB399643A (en) * 1931-09-30 1933-10-12 Electro Metallurg Co Improvements in alloy steel springs and spring blanks
GB517118A (en) * 1938-07-13 1940-01-22 Ver Oberschlesische Huttenwerk Improvements in and relating to improved steels and the application thereof
US4957702A (en) * 1988-04-30 1990-09-18 Qinghua University Air-cooling duplex bainite-martensite steels
AU633737B2 (en) * 1990-06-19 1993-02-04 Nisshin Steel Company, Ltd. Method of making steel for springs
JPH04301031A (en) 1991-03-29 1992-10-23 Mazda Motor Corp Steel member excellent in wear resistance and its production
JPH05320749A (en) 1992-05-20 1993-12-03 Nisshin Steel Co Ltd Production of ultrahigh strength steel
JPH06228734A (en) * 1993-02-02 1994-08-16 Nisshin Steel Co Ltd Production of steel for clutch diaphragm spring
JPH06271930A (en) * 1993-03-18 1994-09-27 Nisshin Steel Co Ltd Production of high strength and high toughness steel excellent in fatigue property
JP3580938B2 (en) 1996-03-05 2004-10-27 アイシン・エィ・ダブリュ株式会社 Heated bainite treatment method

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3519497A (en) * 1965-04-28 1970-07-07 Lorraine Escaut Sa Method for the thermal treatment of steel rails
JPH0257637A (en) * 1988-08-23 1990-02-27 Nippon Steel Corp Manufacture of spring with high fatigue strength and steel wire for spring for use therein
JPH03215623A (en) * 1990-01-19 1991-09-20 Nisshin Steel Co Ltd Production of tough high strength steel
EP0849368A1 (en) * 1996-12-19 1998-06-24 Voest-Alpine Schienen GmbH Shaped rolled product and method of making the same

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
BULL. OSAKA PREFECT. UNIV., SER. A (1997), 46(2), 125-131, 1997 *
CHEMICAL ABSTRACTS, vol. 132, no. 16, 17 April 2000, Columbus, Ohio, US; abstract no. 210668, TOMITA, YOSHIYUKI ET AL: "Modified austempering effects on Fe-0.6C-1.5Si-0.8Mn steel" XP002153889 *
PATENT ABSTRACTS OF JAPAN vol. 014, no. 232 (C - 0719) 17 May 1990 (1990-05-17) *
PATENT ABSTRACTS OF JAPAN vol. 015, no. 496 (C - 0894) 16 December 1991 (1991-12-16) *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010013054A2 (en) 2008-07-31 2010-02-04 The Secretary Of State For Defence Bainite steel and methods of manufacture thereof
EP2410070A1 (en) 2008-07-31 2012-01-25 The Secretary Of State For Defence Bainite steel and methods of manufacture thereof
US8956470B2 (en) 2008-07-31 2015-02-17 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Bainite steel and methods of manufacture thereof
WO2013117953A1 (en) * 2012-02-10 2013-08-15 Ascometal Process for making a steel part, and steel part so obtained
CN111566246A (en) * 2018-01-11 2020-08-21 罗伯特·博世有限公司 Component for contact with hydrogen

Also Published As

Publication number Publication date
GB9918240D0 (en) 1999-10-06
DE60028979D1 (en) 2006-08-03
JP2003506572A (en) 2003-02-18
ATE331051T1 (en) 2006-07-15
EP1200638B1 (en) 2006-06-21
US6884306B1 (en) 2005-04-26
DE60028979T2 (en) 2007-01-04
JP3751250B2 (en) 2006-03-01
EP1200638A1 (en) 2002-05-02
AU6299900A (en) 2001-03-05
GB2352726A (en) 2001-02-07

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