EP3243920A1 - Alliage en fonte à graphite - Google Patents

Alliage en fonte à graphite Download PDF

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Publication number
EP3243920A1
EP3243920A1 EP17162715.1A EP17162715A EP3243920A1 EP 3243920 A1 EP3243920 A1 EP 3243920A1 EP 17162715 A EP17162715 A EP 17162715A EP 3243920 A1 EP3243920 A1 EP 3243920A1
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EP
European Patent Office
Prior art keywords
weight
cast iron
casting
iron alloy
mpa
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.)
Granted
Application number
EP17162715.1A
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German (de)
English (en)
Other versions
EP3243920B1 (fr
Inventor
Konrad Papis
Sebastian Wierschke
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.)
GF Casting Solutions Kunshan Co Ltd
GF Casting Solutions Leipzig GmbH
Original Assignee
Georg Fischer Eisenguss GmbH
Georg Fischer Automotive Kunshan Co Ltd
Georg Fischer Automobilguss GmbH Germany
Georg Fischer GmbH
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 Georg Fischer Eisenguss GmbH, Georg Fischer Automotive Kunshan Co Ltd, Georg Fischer Automobilguss GmbH Germany, Georg Fischer GmbH filed Critical Georg Fischer Eisenguss GmbH
Priority to EP17162715.1A priority Critical patent/EP3243920B1/fr
Publication of EP3243920A1 publication Critical patent/EP3243920A1/fr
Priority to BR102018004643A priority patent/BR102018004643A2/pt
Priority to MX2018003248A priority patent/MX2018003248A/es
Priority to US15/921,842 priority patent/US20180274066A1/en
Priority to KR1020180033303A priority patent/KR20180108495A/ko
Priority to JP2018056599A priority patent/JP7369513B2/ja
Priority to CN201810244212.2A priority patent/CN108624803A/zh
Application granted granted Critical
Publication of EP3243920B1 publication Critical patent/EP3243920B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/04—Cast-iron alloys containing spheroidal graphite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C1/00—Refining of pig-iron; Cast iron
    • C21C1/10—Making spheroidal graphite cast-iron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/06—Cast-iron alloys containing chromium
    • C22C37/08—Cast-iron alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/10—Cast-iron alloys containing aluminium or silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D15/00—Casting using a mould or core of which a part significant to the process is of high thermal conductivity, e.g. chill casting; Moulds or accessories specially adapted therefor
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • C21D5/04—Heat treatments of cast-iron of white cast-iron
    • C21D5/06—Malleabilising
    • C21D5/14—Graphitising

Definitions

  • the invention relates to a nodular cast iron alloy with pearlitic-ferritic structure for cast iron products with a high static strength of 0.2% proof stress ⁇ 600 MPa and a tensile strength ⁇ 750 MPa with a good ductility of at least 2% until a ductile state without subsequent heat treatment 10%, comprising the non-iron components C, Si, P, Mg, S, Mn and Ni and the usual impurities.
  • Possible applications for motor vehicle construction are, for example, chassis components such as wheel carriers, vehicle structural parts and crankshafts.
  • a higher strength bainitic nodular cast iron alloy having 2 to 4% by weight of Ni and 0.05 to 0.45 by weight of Mn is known as non-iron components, and the Ni-Mn margin is to adjust the variable ratio of strength to elongation.
  • the non-iron components are preferably 3.1 to 4% wt.% C and 1.8 to 3 wt.% Si.
  • a material of this composition with this microstructure is characterized by a tensile strength of 650 to 850 MPa and a 0.2% proof stress of ⁇ 500 MPa with an elongation at break of 14.5 to 7%.
  • Another cast iron alloy is known, which is described as high and wear resistant and corrosion resistant. It is composed of 3 to 4.2 wt.% C, 1 to 3.5 wt.% Si, 1 to 6 wt.% Ni, ⁇ 5 wt.% Cr, ⁇ 3 wt.% Cu, ⁇ 3 wt.% Mo, ⁇ 1% by weight Mn, ⁇ 1% by weight V, ⁇ 0.4 % P, ⁇ 0.1% by weight S, ⁇ 0.08% by weight Mg, ⁇ 0.3% by weight Sn and manufacturing impurities.
  • nodular cast iron alloy From CA 122 40 66 A1 / US 448 49 53 A a higher-strength nodular cast iron alloy is known, wherein the nodular cast iron alloy as non-iron constituents 3 to 3.6 wt.% C, 3.5 to 5 wt.% Si, 0.7 to 5 wt.% Ni, 0 to 0.3 wt.% Mo, 0.2 to 0.4 wt. % Mn, ⁇ 0.06 wt% P and ⁇ 0.015 wt% S.
  • From the US 370 22 69 A is a high strength high alloyed nodular cast iron alloy whose non-iron constituents comprise 2.6 to 4 wt% C, 1.5 to 4 wt% Si, 6 to 11 wt% Ni, ⁇ 7 wt% Co, ⁇ 0.4 wt% Mo, ⁇ 1 wt% Mn and ⁇ 0.2 wt% Cr.
  • the high tensile strength of ⁇ 1000 MPa is due to a fine-grained bainitic structure, the target structure must be adjusted by means of a required heat treatment in the form of tempering, which in turn requires more effort.
  • 35 04 A describes an iron-based higher alloy cast material whose non-iron constituents comprise 0.8 to 3.5 wt% C, 1 to 7 wt% Si, 5 to 15 wt% Ni, ⁇ 1 wt% Mn, ⁇ 2 wt% Cr, ⁇ 0.1% by weight of at least one element of the group Mg, Ca and Ce and ⁇ 2 wt.% Of at least one element of the group Mo, Nb, Ti and V.
  • the material has a hardness of at least 250 HV at a microstructural content of at least 30% martensite, the Graphite formation is predominantly spherulitic.
  • the target product is a lapping disk, preferably for use in semiconductor production.
  • From the US 354 94 30 A is a high-strength bainitic ductile iron alloy known, wherein the nodular cast iron alloy as non-iron constituents 2.9 to 3.9 wt.% C, 1.7 to 2.6 wt.% Si, 3.2 to 7 wt.% Ni, 0.15 to 0.4 wt.% Mo, ⁇ 0.2 wt. % Cr and ⁇ 1 wt.% Mn.
  • the alloy is characterized by a high tensile strength ⁇ 820 MPa, a 0.2% proof stress of ⁇ 520 MPa with an elongation at break of at least 2%.
  • a heat treatment is required; in addition, locally used cooling molds may be required for larger wall thicknesses.
  • DE 180 85 15 A1 a high strength nodular cast iron alloy whose non-iron components comprise 2.9 to 3.9 wt% C, 1.7 to 2.6 wt% Si, 3.2 to 7 wt% Ni, 0.15 to 0.4 wt% Mo, ⁇ 0.1 wt% Mg, 0 to 1 wt.% Mn and 0 to 0.25 wt.% Cr at a total content of Mo and Cr of at most 0.5 wt.%.
  • This material has a tensile strength of ⁇ 1000 MPa and a 0.2% proof stress of ⁇ 750 MPa with an elongation at break of at least 4%.
  • the central feature of the material is a heat treatment in the form of a tempering of several hours at temperatures of 200 to 315 ° C, since the specified parameters can not be achieved without starting the matrix structure.
  • Out EP 1 834 005 B1 is a high-strength, mainly pearlitic ductile iron alloy known for automotive applications. This contains the non-iron components 3.0 to 3.7 wt.% C, 2.6 to 3.4 wt.% Si, 0.02 to 0.05 % P, 0.025 to 0.045 wt% Mg, 0.01 to 0.03 wt% Cr, 0.003 to 0.017 wt% Al, 0.0005 to 0.012 wt% S and 0.0004 to 0.002 wt% B, 0.1 to 1.5 wt. % Cu, 0.1 to 1.0 wt% Mn and unavoidable impurities.
  • the chassis components produced in this composition already have a tensile strength of 600 to 900 MPa, a 0.2% proof stress of 400 to 600 at an elongation at break of 14 to 5% already in the cast state without an additional heat treatment.
  • the nodular cast iron alloy according to the invention comprising 2.8 to 3.7% by weight C, 1.5 to 4% by weight Si, 1 to 6.2% by weight Ni, 0.02 to 0.05% by weight P, 0.025 to 0.06% by weight Mg, 0.01 to 0.03 wt.% Cr, 0.003 to 0.3 wt.% Al, 0.0005 to 0.012 wt.% S, 0.03 to 1.5 wt.% Cu and 0.1 to 2 wt.% Mn, remainder Fe and unavoidable impurities achieved, the nodular cast iron alloy in the cast state without subsequent heat treatment achieves a high static strength of a 0.2% proof stress ⁇ 600 MPa and a tensile strength ⁇ 750 MPa with simultaneously good ductility of an elongation at break A5 of 2 to 10%.
  • the matrix structure surrounding the spherulitic graphite precipitates is perlitic-ferritic with> 50% perlite, preferably the perlite is finely striated and the ferrite is globular.
  • the nodular cast iron alloy according to the invention differs markedly from that of the present invention US 585 35 04 A known alloy with a partially overlapping Ni alloy region.
  • there is a difference to this DE 10 2004 040 056 A1 well-known cast iron alloy since mechanical properties of a needle-like ferrite differ significantly from those of a globular formed ferrite.
  • the nodular cast iron alloy is formed as a sand nodular cast iron alloy.
  • the core idea of the invention is to specify a nodular cast iron alloy which can be used on the basis of suitably coordinated compositions of the nodular cast iron alloy according to the invention and the resulting combinations of mechanical properties in motor vehicle construction, for example for axle and chassis parts which must plastically deform in the event of a collision of the motor vehicle and not allowed to break, but also for structural parts and crankshafts, which are exposed to high dynamic loads.
  • the nodular cast iron alloy according to the invention already satisfies moderate alloy additions compared with austenitic nodular cast iron alloys.
  • Ni and Si are known to increase the 0.2% proof stress. This is attributed on the one hand to the solid solution hardening (Si and Ni), on the other hand to a pearlite refining by lowering the austenite-ferrite transformation temperature to lower temperatures (Ni). It is advantageous that the alloy has the highest possible 0.2% proof strength at not inconsiderable elongation at break values (high lightweight potential). This is achieved primarily by the nodular cast iron alloy having from 1 to 6.2% by weight of Ni, preferably 2.5 to 5.2% by weight of Ni and particularly preferably 4 to 5.2% by weight of Ni.
  • the nodular cast iron alloy according to the invention has a distinct advantage over the alloy DE 10 2004 040 056 A1 with similar Ni content limits, so even with small wall thicknesses of about 8 mm, a sure martensittransports structure is achieved without the need for a subsequent annealing.
  • the nodular cast iron alloy according to the invention this is possible by observing certain composition ratios of Ni, Si and Mn contents.
  • the sum of the contents of Ni and Si is ⁇ 9 wt.%,
  • the ratio should be (Ni + 0.5 * Mn) / (1.5 * Si) do not exceed 1.5.
  • Levels of Si ⁇ 1.5 wt% increase the risk of carbide formation, in the worst case, white whitening may result.
  • Si> 4 wt.% Lead to a significant decrease in the elongation at break and also increase the risk of martensite formation due to the reduced carbon solubility in austenite.
  • the Si content must also be limited for the reason that silicon shifts the austenite-ferrite transformation temperature toward higher temperatures and thus counteracts pearlite refinement aimed at via nickel additions.
  • the alloying of 0.03 to 1.5% by weight of Cu takes place - in particular with respect to the limits specified for the ductile iron alloy according to the invention, low Ni contents and simultaneously high Si contents - to secure> 50% of the predominantly pearlitic microstructure for achieving the mechanical properties.
  • Perlite, remainder ferrite, while ferrite is preferably globular.
  • Mn is in increasing proportions a scrap companion. For an increase in yield strength, Mn is advantageous up to a moderate level. Mn also lowers the martensite start temperature and can thus help to reduce the risk of martensite formation in faster cooling thin-walled component parts.
  • the upper limit for the nodular cast iron alloy according to the invention of 2% by weight Mn is due to a strong embrittlement due to carbide formation, but an increase of segregating grain boundary carbides, especially with simultaneously higher Si contents, can be observed even at lower Mn contents.
  • the alloying of 0.003 to 0.3 wt.% Al can be carried out in order to achieve a further increase in strength through solid solution hardening.
  • the Al content must be limited to ⁇ 0.3% by weight, since Al simultaneously acts as a ferrite stabilizer and thus, contrary to the predominantly pearlitic microstructure with> 50% perlite necessary for the mechanical properties.
  • the graphite content is in the casting condition immediately after the casting process, i. after casting and cooling in the mold, formed spherical to more than 90% of the graphite present.
  • the matrix structure of the casting immediately after the casting process in the cast state, ie after casting and cooling in the mold, is formed to 50 to 90% pearlitic.
  • the structure of the casting immediately after the casting process in the cast state, i. after casting and cooling in the mold from 200 to 1200 spherulites per mm 2.
  • the graphite particles preferably have a size distribution of at least 5% of the size 8, 40% to 70% of the size 7 and at most 35% of the size 6 according to DIN EN ISO 945.
  • the casting has a Brinell hardness of 260 to 320 HBW.
  • the yield strength Rp0.2 is shown as a function of the breaking elongation A5.
  • Registered is the described embodiment of the inventive nodular cast iron alloy as well as representatives of the standardized in DIN EN 1563 and DIN EN 1564 ductile iron alloys.
  • the gray lines in Figure 2 combine the minimum values according to the standard DIN EN 1563 for spheroidal graphite cast irons of grades produced in the cast state.
  • the solid black line in Figure 2 combines the minimum values according to DIN EN 1564 for spheroidal graphite cast iron of heat-treated ADI grades.
  • Black dashed lines show patented nodular cast iron alloys from Georg Fischer ( EP 1 834 005 B1 and EP 1 270 747 B1 ).

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Heat Treatment Of Steel (AREA)
EP17162715.1A 2017-03-24 2017-03-24 Alliage en fonte à graphite sphéroidal Active EP3243920B1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP17162715.1A EP3243920B1 (fr) 2017-03-24 2017-03-24 Alliage en fonte à graphite sphéroidal
BR102018004643A BR102018004643A2 (pt) 2017-03-24 2018-03-08 liga fundida nodular
MX2018003248A MX2018003248A (es) 2017-03-24 2018-03-15 Aleacion de fundido nodular.
US15/921,842 US20180274066A1 (en) 2017-03-24 2018-03-15 Nodular cast alloy
KR1020180033303A KR20180108495A (ko) 2017-03-24 2018-03-22 노듈형 주조 합금
JP2018056599A JP7369513B2 (ja) 2017-03-24 2018-03-23 球状黒鉛鋳鉄合金
CN201810244212.2A CN108624803A (zh) 2017-03-24 2018-03-23 球墨铸合金

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP17162715.1A EP3243920B1 (fr) 2017-03-24 2017-03-24 Alliage en fonte à graphite sphéroidal

Publications (2)

Publication Number Publication Date
EP3243920A1 true EP3243920A1 (fr) 2017-11-15
EP3243920B1 EP3243920B1 (fr) 2020-04-29

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ID=58412966

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EP17162715.1A Active EP3243920B1 (fr) 2017-03-24 2017-03-24 Alliage en fonte à graphite sphéroidal

Country Status (7)

Country Link
US (1) US20180274066A1 (fr)
EP (1) EP3243920B1 (fr)
JP (1) JP7369513B2 (fr)
KR (1) KR20180108495A (fr)
CN (1) CN108624803A (fr)
BR (1) BR102018004643A2 (fr)
MX (1) MX2018003248A (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023110683A1 (fr) * 2021-12-13 2023-06-22 Sediver Nuance de fonte ductile a matrice ferritique renforcee

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109402496A (zh) * 2018-11-28 2019-03-01 精诚工科汽车系统有限公司 具有均匀壁厚的球墨铸铁铸件中合金元素添加量的确定方法与球墨铸铁铸件及其铸造和模具
US11618937B2 (en) * 2019-10-18 2023-04-04 GM Global Technology Operations LLC High-modulus, high-strength nodular iron and crankshaft
CN113897538A (zh) * 2021-10-12 2022-01-07 安徽裕隆模具铸业有限公司 一种高强度、高伸长率铸态qt500-18球墨铸铁及其制备方法
CN114411049B (zh) * 2021-12-29 2022-12-02 天润工业技术股份有限公司 一种低成本、高强度的铁素体球墨铸铁及其制备方法与应用

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1808515A1 (de) 1967-11-14 1969-07-17 Int Nickel Ltd Gusseisen mit Kugelgraphit
US3702269A (en) 1971-01-22 1972-11-07 Int Nickel Co Ultra high strength ductile iron
US4484953A (en) 1983-01-24 1984-11-27 Ford Motor Company Method of making ductile cast iron with improved strength
US5853504A (en) 1996-09-05 1998-12-29 Kabushiki Kaisha Toshiba Material for lapping tools and lapping surface plate using the same
EP1225239A1 (fr) 1999-06-08 2002-07-24 Asahi Tec Corporation Fonte a graphite spheroide obtenue sans transformation bainitique
DE102004040056A1 (de) 2004-08-18 2006-02-23 Federal-Mogul Burscheid Gmbh Hoch- und verschleißfester, korrosionsbeständiger Gusseisenwerkstoff
DE102004056331A1 (de) * 2004-11-22 2006-05-24 Georg Fischer Fahrzeugtechnik Ag Sphärogusslegierung und Verfahren zur Herstellung von Gussteilen aus der Sphärogusslegierung
WO2006072663A2 (fr) * 2005-01-05 2006-07-13 Metso Paper, Inc. Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees
EP1270747B1 (fr) 2001-06-20 2006-10-04 Georg Fischer Fahrzeugtechnik AG Fonte à graphite sphéroidal
DE102008050152A1 (de) * 2008-10-01 2010-04-08 Claas Guss Gmbh Hochfeste, duktile Gusseisenlegierung mit Kugelgraphit sowie Verfahren zu deren Herstellung

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JPS5917186B2 (ja) * 1977-03-30 1984-04-19 日立金属株式会社 球状黒鉛鋳鉄とその製造方法
JP3597211B2 (ja) * 1993-10-21 2004-12-02 株式会社日本製鋼所 高温強度に優れた球状黒鉛鋳鉄
JP2001059127A (ja) 1999-06-08 2001-03-06 Asahi Tec Corp 球状黒鉛鋳鉄
KR100681270B1 (ko) 2005-09-05 2007-02-09 한금태 고강도 고연신율 구상흑연주철
JP2007327083A (ja) 2006-06-06 2007-12-20 I Metal Technology Co Ltd 球状黒鉛鋳鉄及びその製造方法
JP4963444B2 (ja) 2007-06-21 2012-06-27 旭テック株式会社 球状黒鉛鋳鉄部材

Patent Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1808515A1 (de) 1967-11-14 1969-07-17 Int Nickel Ltd Gusseisen mit Kugelgraphit
US3549430A (en) 1967-11-14 1970-12-22 Int Nickel Co Bainitic ductile iron having high strength and toughness
US3702269A (en) 1971-01-22 1972-11-07 Int Nickel Co Ultra high strength ductile iron
US4484953A (en) 1983-01-24 1984-11-27 Ford Motor Company Method of making ductile cast iron with improved strength
CA1224066A (fr) 1983-01-24 1987-07-14 Roman M. Nowicki Fabrication de fer ductile a tenacite accrue
US5853504A (en) 1996-09-05 1998-12-29 Kabushiki Kaisha Toshiba Material for lapping tools and lapping surface plate using the same
EP1225239A1 (fr) 1999-06-08 2002-07-24 Asahi Tec Corporation Fonte a graphite spheroide obtenue sans transformation bainitique
EP1270747B1 (fr) 2001-06-20 2006-10-04 Georg Fischer Fahrzeugtechnik AG Fonte à graphite sphéroidal
DE102004040056A1 (de) 2004-08-18 2006-02-23 Federal-Mogul Burscheid Gmbh Hoch- und verschleißfester, korrosionsbeständiger Gusseisenwerkstoff
DE102004056331A1 (de) * 2004-11-22 2006-05-24 Georg Fischer Fahrzeugtechnik Ag Sphärogusslegierung und Verfahren zur Herstellung von Gussteilen aus der Sphärogusslegierung
EP1834005B1 (fr) 2004-11-22 2010-08-18 Georg Fischer Automotive AG Alliage coule nodulaire et procede pour produire des pieces coulees a partir de cet alliage coule nodulaire
WO2006072663A2 (fr) * 2005-01-05 2006-07-13 Metso Paper, Inc. Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees
DE102008050152A1 (de) * 2008-10-01 2010-04-08 Claas Guss Gmbh Hochfeste, duktile Gusseisenlegierung mit Kugelgraphit sowie Verfahren zu deren Herstellung

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023110683A1 (fr) * 2021-12-13 2023-06-22 Sediver Nuance de fonte ductile a matrice ferritique renforcee
WO2023111403A1 (fr) * 2021-12-13 2023-06-22 Sediver Nuance de fonte ductile à matrice ferritique renforcée

Also Published As

Publication number Publication date
EP3243920B1 (fr) 2020-04-29
MX2018003248A (es) 2018-11-09
CN108624803A (zh) 2018-10-09
BR102018004643A2 (pt) 2018-10-30
KR20180108495A (ko) 2018-10-04
JP7369513B2 (ja) 2023-10-26
US20180274066A1 (en) 2018-09-27
JP2018162516A (ja) 2018-10-18

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