EP3243920B1 - Sphärogusslegierung - Google Patents

Sphärogusslegierung Download PDF

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Publication number
EP3243920B1
EP3243920B1 EP17162715.1A EP17162715A EP3243920B1 EP 3243920 B1 EP3243920 B1 EP 3243920B1 EP 17162715 A EP17162715 A EP 17162715A EP 3243920 B1 EP3243920 B1 EP 3243920B1
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EP
European Patent Office
Prior art keywords
weight
alloy
nodular cast
perlitic
alloy according
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.)
Active
Application number
EP17162715.1A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3243920A1 (de
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
GF Casting Solutions Kunshan Co Ltd
GF Casting Solutions Leipzig 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 GF Casting Solutions Kunshan Co Ltd, GF Casting Solutions Leipzig GmbH filed Critical GF Casting Solutions Kunshan Co Ltd
Priority to EP17162715.1A priority Critical patent/EP3243920B1/de
Publication of EP3243920A1 publication Critical patent/EP3243920A1/de
Priority to BR102018004643A priority patent/BR102018004643A2/pt
Priority to US15/921,842 priority patent/US20180274066A1/en
Priority to MX2018003248A priority patent/MX2018003248A/es
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/de
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 spheroidal cast iron alloy with pearlitic-ferritic structure for cast iron products with a high static strength even in the as-cast state without subsequent heat treatment of a 0.2% proof stress ⁇ 600 MPa and a tensile strength ⁇ 750 MPa with good ductility from an elongation at break of 2% to 10%, including the non-iron components C, Si, P, Mg, S, Mn and Ni as well as the usual impurities.
  • Possible applications for motor vehicle construction include chassis components such as wheel carriers, vehicle structural parts and crankshafts.
  • the Ni-Mn range serves to adjust the variable ratio of strength to elongation.
  • the non-iron components are preferably 3.1 to 4% by weight of C and 1.8 to 3% by weight of Si.
  • a material of this composition with this structure 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% by weight of C, 1 to 3.5% by weight of Si, 1 to 6% by weight of Ni, ⁇ 5% by weight of Cr, ⁇ 3% by weight of Cu, ⁇ 3% by weight of Mo, ⁇ 1 wt% Mn, ⁇ 1 wt% V, ⁇ 0.4 %
  • P ⁇ 0.1% by weight S, ⁇ 0.08% by weight Mg, ⁇ 0.3% by weight Sn and manufacturing-related impurities.
  • a high-strength, higher-alloy spheroidal cast iron alloy is known, the non-iron components of which comprise 2.6 to 4% by weight of C, 1.5 to 4% by weight of Si, 6 to 11% by weight of Ni, ⁇ 7% by weight of Co, ⁇ 0.4% by weight of 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 having to be set by means of a required heat treatment in the form of tempering, which in turn requires additional effort.
  • 35 04 A describes an iron-based, higher-alloy cast material, the non-iron components of which comprise 0.8 to 3.5% by weight of C, 1 to 7% by weight of Si, 5 to 15% by weight of Ni, ⁇ 1% by weight of Mn, ⁇ 2% by weight of Cr, ⁇ 0.1% by weight of at least one element from the group Mg, Ca and Ce and ⁇ 2% by weight of at least one element from the group Mo, Nb, Ti and V.
  • the material has a hardness of at least 250 HV with a microstructure of at least 30% martensite, the Graphite formation is predominantly spherolithic.
  • a lapping wheel is named as the target product, preferably for use in semiconductor production.
  • a higher strength bainitic nodular cast iron alloy is known, the nodular iron alloy being non-iron components 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 contains.
  • 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%.
  • heat treatment is necessary; in addition, locally used cooling molds may be necessary for larger wall thicknesses.
  • DE 180 85 15 A1 a high-strength spheroidal cast iron alloy, the non-iron components of which comprise 2.9 to 3.9% by weight of C, 1.7 to 2.6% by weight of Si, 3.2 to 7% by weight of Ni, 0.15 to 0.4% by weight of Mo, ⁇ 0.1% by weight of Mg, 0 to 1% by weight of Mn and 0 to 0.25% by weight of Cr with a total content of Mo and Cr of at most 0.5% by weight.
  • 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 heat treatment in the form of tempering for several hours at temperatures of 200 to 315 ° C, since the specified values cannot be achieved without tempering the matrix structure.
  • Out EP 1 834 005 B1 is a higher strength, predominantly pearlitic spheroidal graphite cast iron alloy for applications in motor vehicle construction.
  • 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% by weight Mg, 0.01 to 0.03% by weight Cr, 0.003 to 0.017% by weight Al, 0.0005 to 0.012% by weight S and 0.0004 to 0.002% by weight B, 0.1 to 1.5% by weight % Cu, 0.1 to 1.0% by weight Mn and unavoidable impurities.
  • the chassis components produced in this composition already have a tensile strength of 600 to 900 MPa in the as-cast state without additional heat treatment, a 0.2% proof stress of 400 to 600 with an elongation at break of 14 to 5%.
  • the spheroidal cast alloy according to the invention comprising 2.8 to 3.7% by weight of C, 1.5 to 4% by weight of Si, 1 to 6.2% by weight of Ni, 0.02 to 0.05% by weight of P, 0.025 to 0.06% by weight of Mg, 0.01 to 0.03% by weight of Cr, 0.003 to 0.3% by weight of AI, 0.0005 to 0.012% by weight of S, 0.03 to 1.5% by weight of Cu and 0.1 to 2% by weight of Mn, remainder Fe and inevitable impurities, the spheroidal cast iron alloy being in the cast state Without subsequent heat treatment, a high static strength of a 0.2% proof stress ⁇ 600 MPa and a tensile strength ⁇ 750 MPa with a good ductility of an elongation at break A5 of 2 to 10% is achieved, whereby the matrix structure surrounding the spherulitic graphite precipitates is pearlitic-ferritic with> 50% pearlite, the pearlite being finely streaked and the matrix structure surrounding the
  • the nodular cast iron alloy is preferably designed as a sand nodular cast iron alloy.
  • the core idea of the invention is to provide a spheroidal cast iron alloy which, owing to suitably coordinated compositions of the spheroidal cast iron alloy according to the invention and the resulting combinations of mechanical properties, can be used in motor vehicle construction, for example for axle and chassis parts which have to deform plastically in the event of a collision of the motor vehicle must not break, but also for structural parts and crankshafts that are exposed to high dynamic loads.
  • the spheroidal cast alloy according to the invention in view of its mechanical properties and possible uses, already suffices for moderate alloy additions compared to austenitic spheroidal cast iron alloys.
  • Ni and Si are known to increase the 0.2% proof stress. This is attributed on the one hand to solid-solution strengthening (Si and Ni), on the other hand to pearlite refinement by lowering the austenite-ferrite transition temperature to lower temperatures (Ni). It is advantageous that the alloy has the highest possible 0.2% proof stress with not too low elongation at break values (high lightweight construction potential). This is achieved primarily in that the spheroidal cast iron alloy has 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 spheroidal cast iron alloy according to the invention has a clear advantage over the alloy DE 10 2004 040 056 A1 With similar Ni content limits, a safe martensite structure is achieved even with small wall thicknesses of approx. 8 mm without the need for subsequent tempering.
  • the spheroidal cast iron alloy according to the invention this is possible by maintaining certain compositional ratios of Ni, Si and Mn contents.
  • the sum of the contents of Ni and Si is ⁇ 9% by weight, at the same time the ratio (Ni + 0.5 ⁇ Mn) / (1.5 ⁇ Si) do not exceed 1.5.
  • Levels of Si ⁇ 1.5% by weight increase the risk of carbide formation, in the worst case white solidification can result.
  • Si> 4% by weight 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 the austenite.
  • Si content should also be limited for the reason that silicon shifts the austenite-ferrite transition temperature to higher temperatures and thus counteracts the pearlite refinement sought by adding nickel.
  • Alloying from 0.03 to 1.5% by weight of Cu is carried out - in particular with low Ni contents with respect to the limits specified for the spheroidal cast iron alloy according to the invention with high Si contents at the same time - in order to ensure that Achievement of the mechanical properties predominantly pearlitic structure with> 50% pearlite, rest ferrite, ferrite globular.
  • Mn is a scrap companion in increasing proportions. Mn up to a moderate content is advantageous for increasing the yield strength. Mn also lowers the martensite start temperature and can thus help to reduce the risk of martensite formation in thin parts with faster cooling parts.
  • the upper limit for the spheroidal cast alloy according to the invention of 2% by weight of Mn is due to a strong embrittlement due to carbide formation, but an increase in segregating grain boundary carbides, in particular with simultaneously higher Si contents, is already evident at lower Mn contents.
  • Alloying from 0.003 to 0.3% by weight of Al can be carried out in order to achieve a further increase in strength by solid-solution strengthening.
  • the Al content is to be limited to ⁇ 0.3% by weight, since Al also acts as a ferrite stabilizer and thus contrary to the predominantly pearlitic microstructure formation with> 50% pearlite, which is necessary for the mechanical properties.
  • P is to be limited due to the well-known embrittling effect of low-melting P-rich phases, which can form at grain boundaries (former, P-enriched residual melt areas).
  • the graphite portion is spherical immediately after the casting process in the as-cast state, ie after casting and cooling in the mold, to more than 90% of the graphite present.
  • the matrix structure of the cast part immediately after the casting process in the as-cast state i.e. after casting and cooling in the mold, 50 to 90% pearlitic.
  • the structure of the cast part immediately after the casting process in the as-cast state i.e. after casting and cooling in the mold, 200 to 1200 spherulites per mm2.
  • the graphite particles preferably have a size distribution of at least 5% of size 8, 40% to 70% of size 7 and at most 35% of size 6 according to DIN EN ISO 945.
  • the cast part has a Brinell hardness of 260 to 320 HBW.
  • the yield strength Rp0.2 is shown as a function of the elongation at break A5.
  • the described exemplary embodiment of the spheroidal cast iron alloy according to the invention and representatives of the spheroidal cast iron alloys standardized in DIN EN 1563 and DIN EN 1564 are entered.
  • the gray lines in Figure 2 combine the minimum values according to the DIN EN 1563 standard for spheroidal graphite cast iron of grades produced in the as-cast state.
  • the solid black line in Figure 2 combines the minimum values according to the DIN EN 1564 standard for spheroidal graphite cast iron of heat-treated ADI grades.
  • Patented nodular cast iron alloys from Georg Fischer shown in black on the dashed line ( EP 1 834 005 B1 and EP 1 270 747 B1 ).

Landscapes

  • 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)
  • Heat Treatment Of Steel (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
EP17162715.1A 2017-03-24 2017-03-24 Sphärogusslegierung Active EP3243920B1 (de)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP17162715.1A EP3243920B1 (de) 2017-03-24 2017-03-24 Sphärogusslegierung
BR102018004643A BR102018004643A2 (pt) 2017-03-24 2018-03-08 liga fundida nodular
US15/921,842 US20180274066A1 (en) 2017-03-24 2018-03-15 Nodular cast alloy
MX2018003248A MX2018003248A (es) 2017-03-24 2018-03-15 Aleacion de fundido nodular.
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 (de) 2017-03-24 2017-03-24 Sphärogusslegierung

Publications (2)

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

Family

ID=58412966

Family Applications (1)

Application Number Title Priority Date Filing Date
EP17162715.1A Active EP3243920B1 (de) 2017-03-24 2017-03-24 Sphärogusslegierung

Country Status (7)

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

Families Citing this family (5)

* 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
WO2023111403A1 (fr) * 2021-12-13 2023-06-22 Sediver Nuance de fonte ductile à matrice ferritique renforcée
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

Family Cites Families (16)

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Publication number Priority date Publication date Assignee Title
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
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
US4484953A (en) 1983-01-24 1984-11-27 Ford Motor Company Method of making ductile cast iron with improved strength
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
JP3691913B2 (ja) 1996-09-05 2005-09-07 株式会社東芝 研磨工具用材料およびそれを用いた研磨定盤
AU5106400A (en) 1999-06-08 2000-12-28 Asahi Tec Corporation Non-austempered spheroidal graphite cast iron
JP2001059127A (ja) 1999-06-08 2001-03-06 Asahi Tec Corp 球状黒鉛鋳鉄
DE10129382A1 (de) 2001-06-20 2003-01-02 Fischer Georg Fahrzeugtech Sphärogusslegierung
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
FI118738B (fi) * 2005-01-05 2008-02-29 Metso Paper Inc Pallografiittivalurauta ja menetelmä pallografiittivaluraudan valmistamiseksi lujuutta ja sitkeyttä vaativia koneenrakennusosia varten
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
DE102008050152B4 (de) * 2008-10-01 2013-05-23 Claas Guss Gmbh Hochfeste, duktile Gusseisenlegierung mit Kugelgraphit sowie Verfahren zu deren Herstellung

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Title
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Also Published As

Publication number Publication date
JP7369513B2 (ja) 2023-10-26
KR20180108495A (ko) 2018-10-04
EP3243920A1 (de) 2017-11-15
US20180274066A1 (en) 2018-09-27
CN108624803A (zh) 2018-10-09
JP2018162516A (ja) 2018-10-18
MX2018003248A (es) 2018-11-09
BR102018004643A2 (pt) 2018-10-30

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