EP1190107B1 - Aluminum-base alloy for cylinder heads - Google Patents

Aluminum-base alloy for cylinder heads Download PDF

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Publication number
EP1190107B1
EP1190107B1 EP00926595A EP00926595A EP1190107B1 EP 1190107 B1 EP1190107 B1 EP 1190107B1 EP 00926595 A EP00926595 A EP 00926595A EP 00926595 A EP00926595 A EP 00926595A EP 1190107 B1 EP1190107 B1 EP 1190107B1
Authority
EP
European Patent Office
Prior art keywords
alloy
alloys
weight
magnesium
copper
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.)
Expired - Lifetime
Application number
EP00926595A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP1190107A1 (en
Inventor
Fernando Barata De Paula Pinto
Antonio Silvio Carmezini
Eduardo Celso Fonseca
Ricardo Fuoco
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.)
Ford Motor Co Brasil Ltda
Instituto de Pesquisa Tecnologicas do Estado Sao Paulo S/A (IPT)
Original Assignee
Ford Motor Co Brasil Ltda
Instituto de Pesquisa Tecnologicas do Estado Sao Paulo S/A (IPT)
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 Ford Motor Co Brasil Ltda, Instituto de Pesquisa Tecnologicas do Estado Sao Paulo S/A (IPT) filed Critical Ford Motor Co Brasil Ltda
Publication of EP1190107A1 publication Critical patent/EP1190107A1/en
Application granted granted Critical
Publication of EP1190107B1 publication Critical patent/EP1190107B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/04—Heavy metals
    • F05C2201/0469—Other heavy metals
    • F05C2201/0475—Copper or alloys thereof

Definitions

  • Automotive engine cylinder heads are usually manufactured by casting process in alloys of the Ahmainum-Silicon-Copper class. When the mechanical load imposed on the cylinder heads is extreme, the use of heat treatments becomes necessary as a means of improving the qualities of the alloys.
  • the present invention concerns an alloy of the Aluminum-Silicon-Copper class improved for the production of the said cylinder heads, presenting better mechanical properties than those obtained in the alloys traditionally used, thus doing away with the need for heat treatment.
  • the alloys used for the manufacture of cylinder heads with or without heat treatment are basically the same, differing only in the magnesium contents, lower than 0.20% for non-treated alloys, and lying between 0.30% and 0.50% for treated alloys. This increase in the magnesium content helps the response to the heat treatment, so that increases of hardness and mechanical resistance are obtained. Typical specifications of the aluminum alloys most often used in the production of automotive cylinder heads.
  • Table II shows the minimal mechanical property values obtained in these alloys when they are cast in sand molds in the rough casting state and after the solution and precipitation heat treatment (T6).
  • An alternative serving to improve the mechanical properties of the pieces without raising the cost of the final product would be to increase the speed of cooling during the solidification of the aluminum alloys. Since most cylinder heads are produced by casting in metal molds, containing some cores of sand in order to form the internal cavities, an increase in the speed of cooling might be obtained by means of the forced cooling of the metal molds. It is important to point out that this procedure improves the properties only of the regions that are in contact with the cooled metal molds, and, even so, its action is limited only to the superficial layer of the piece.
  • the present invention concerns an alloy that is modified in relation to those that are traditionally used in the production of cylinder heads, and presents, in the rough casting stage, mechanical properties similar to those obtained in pieces after the heat treatment.
  • the document DATABASE WPI Section Ch, Week 199848 Derwent Publications Ltd., London, GB; Class M26, AN 1998-563579 and JP-A-10 251790 discloses an aluminum-base alloy for the production of engine cylinder heads containing, in weight %, Si from 4.0% to 10.0%, Cu from 0% to 5.0%, Mg from 0% to 1.0%, balance Al.
  • the document US-A-4 336 076 describes an engine cylinder block made of an aluminum alloy containing in weight 4 to 14% of Si, 1 to 5% of Cu and 0.2 to 0.8% of Mg.
  • Method of manufacturing the cylinder block includes a heat treatment step after moulding of such aluminum alloy.
  • the microstructures of the alloys traditionally used in the production of cylinder heads are constituted by the ⁇ phase (dendrites), the ⁇ +Si eutectic, copper-rich eutectics, and intermetallic phases rich in iron, of the Al 5 FeSi and Al 15 (Fe,Mn) 3 Si 2 kinds.
  • the alloy that is the subject matter of this invention is described in Table IV. Specification of the alloy that is the subject matter of this invention, to be used in the production of automotive cylinder heads, without the need for heat treatments.
  • the specified contents of copper and magnesium are higher than those of the alloys traditionally used in this application.
  • Figures 1a and 1b show the general appearance of the microstructure of alloy B with a copper content of 4.5%, by weight, and a magnesium content of 0.7%, by weight, respectively, and Figures 2a and 2b show the detailed appearance of the eutectic that is rich in copper and magnesium respectively.
  • the aim is, by means of an increase of the copper and magnesium contents, to increase the volumetric fraction of hard phases without impairing the casting characteristics of the alloys.
  • Colwell and Kissling (2) studied the addition of magnesium from 0% to 0.6% in aluminum alloys, having observed results showing increasing mechanical resistance.
  • Hardening by the natural precipitation of coherent phases - Trela (3) mentions the existence of Al-Zn alloys developed in the 1950s which present a natural hardening, i.e., self aging, without the need for heat treatments. These alloys contain roughly 7% to 8% zinc, by weight; 0.4% magnesium, by weight; and 0.5% to 0.8% copper, by weight. With this composition, the principal difficulty in its use would be the low fusibility.
  • Figure 3 shows the evolution of hardness figures in test specimens cast in sand molds in respect of the alloys described in Table IV, without the presence of magnesium, when the copper content was raised.
  • the figures presented show hardness results right after the casting (on the outset of the natural precipitation), and after 5 days (at the end of the natural precipitation).
  • Figure 4 presents the evolution of the hardness figures in sand-mold-cast test specimens in respect of the alloys described in Table IV without the presence of copper, when the content of magnesium was increased.
  • the figures presented show hardness results right after the casting (on the outset of the natural precipitation), and after 5 days (at the end of the natural precipitation).
  • Figure 5 presents the evolution of the hardness values with the rising content of magnesium in respect of the alloys described in Table IV with a 4.5% copper content.
  • the figures presented show hardness results right after the casting, and after 2 days.
  • This invention concerns an aluminum-base alloy, the principal elements of which are silicon, copper and magnesiunL
  • the limits of chemical composition established for this alloy are described in detail in Table IV.
  • This alloy is that of the manufacture of automotive engine cylinder heads in the rough casting state (without heat treatments).
  • Figure 6 presents a typical differential thermal analysis curve of the traditional B alloy (Table I) and its derived curve (shown in the hatched line).
  • the solidification reactions are evidenced by increases in the differences of temperature between the sample and the standard, that is, since the figures are negative, the reactions correspond to the slumps in the DTA curve (from the points of maximum values of the DTA to the troughs).
  • the derivative curve can also be used to determine the regions of occurrence of reactions, being represented by values of the derivative above zero (peaks).
  • Figure 7 presents the differential thermal analysis curves of two samples of the alloy described in Table IV with a copper content of 4.2% and a magnesium content of 0.75%. The curves obtained with the two specimens are very similar, showing the reproducibility of the results.
  • Table V shows the principal reactions that occur during the solidification of the alloy described in Table IV.
  • Table VI presents the volumetric fractions that occur at each one of the solidification stages of the alloys of the traditional B and of the modified kinds with a copper content of 4.5% and a magnesium content of 0.7%. Description of the principal reactions that occur during the solidification of the type B alloy (Table I) modified by higher contents of copper and magnesium.
  • Stages Predominant phase* Volumetric fraction (%) Traditional B type alloy (Table I) B type alloy with 4.5% Cn + 0.7% Mg (Table IV) Stage 1 Phase ⁇ dendrites 38 43 Stage 2 ( ⁇ +Si) eutectic 59 39 Stage 3 ( ⁇ +Al 5 Mg 8 Cu 2 Si 6 ) eutectic 1 2 Stage 4 ( ⁇ +CuAl 2 +Al 5 Mg 8 Cu 2 Si 6 ) eutectic 2 16
  • This phenomenon is usually explained as being, the consequence of the metastability of the maintenance of certain alloying elements in a solid solution in the aluminum in the post-casting state.
  • Figure 9 show the curves of hardness evolution resulting from the natural precipitation in respect of three room temperatures applied. The results are very similar, showing that temperature variations between 5°C and 35°C effect only a very small change in the kinetics of natural precipitation and in the level of hardness reached at the end of the precipitation process.
  • Table VII presents the typical mechanical results obtained in the production of cylinder heads with the modified B-type alloy, with copper contents of roughly 4.5% and magnesium contents of roughly 0.7%.
  • the results in respect of the limits of resistance were obtained on the basis of tensile tests of test specimens cast according to the ASTM B 108 standard.
  • the hardness results were obtained by means of direct measurements of the cylinder head faces, on two surfaces: in contact with a metallic mold and in contact with sand cores.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Cylinder Crankcases Of Internal Combustion Engines (AREA)
EP00926595A 1999-05-19 2000-05-19 Aluminum-base alloy for cylinder heads Expired - Lifetime EP1190107B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
BR9901553-6A BR9901553A (pt) 1999-05-19 1999-05-19 Liga à base de alumìnio para a produção de cabeçotes de motor sem tratamento térmico
BR9901553 1999-05-19
PCT/BR2000/000056 WO2000071765A1 (en) 1999-05-19 2000-05-19 Aluminum-base alloy for cylinder heads

Publications (2)

Publication Number Publication Date
EP1190107A1 EP1190107A1 (en) 2002-03-27
EP1190107B1 true EP1190107B1 (en) 2003-03-05

Family

ID=4072293

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00926595A Expired - Lifetime EP1190107B1 (en) 1999-05-19 2000-05-19 Aluminum-base alloy for cylinder heads

Country Status (5)

Country Link
EP (1) EP1190107B1 (pt)
AU (1) AU4529400A (pt)
BR (1) BR9901553A (pt)
DE (1) DE60001577T2 (pt)
WO (1) WO2000071765A1 (pt)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108265205A (zh) * 2018-01-29 2018-07-10 铜陵市腾发铝制品加工有限责任公司 一种轻质环保铝合金及其制备工艺

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100435375B1 (ko) * 2001-12-20 2004-06-10 현대자동차주식회사 실린더헤드의 강도 및 고주파피로 특성이 개선된 합금조성물
KR20030051051A (ko) * 2001-12-20 2003-06-25 현대자동차주식회사 실린더헤드의 강도 및 고주파피로 특성이 개선된 합금조성물
KR20030083146A (ko) * 2002-04-19 2003-10-30 현대자동차주식회사 강도 및 고온 특성이 향상된 실린더 헤드용 알루미늄 합금조성물
KR20030092718A (ko) * 2002-05-31 2003-12-06 현대자동차주식회사 디젤 엔진의 실린더 헤드용 알루미늄 합금
DE102006059899A1 (de) * 2006-12-19 2008-06-26 Bayerische Motoren Werke Ag Hochwarmfeste Aluminium-Gusslegierung
CN109957683A (zh) * 2017-12-25 2019-07-02 比亚迪股份有限公司 一种高强度压铸铝合金及其制备方法和应用
US20240018631A1 (en) * 2020-12-07 2024-01-18 Norsk Hydro Asa A high temperature stable alsicu alloy

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53115407A (en) * 1977-03-17 1978-10-07 Mitsubishi Keikinzoku Kogyo Kk Engine cylinder block and the manufacture thereof
JP3513281B2 (ja) * 1995-08-17 2004-03-31 ヤンマー株式会社 耐圧・高強度アルミニウムの鋳造法
JPH09263867A (ja) * 1996-01-24 1997-10-07 Mitsubishi Chem Corp 鋳物用アルミニウム合金
JPH10251790A (ja) * 1997-03-13 1998-09-22 Hitachi Metals Ltd 熱疲労強度に優れるアルミニウム合金鋳物

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108265205A (zh) * 2018-01-29 2018-07-10 铜陵市腾发铝制品加工有限责任公司 一种轻质环保铝合金及其制备工艺

Also Published As

Publication number Publication date
EP1190107A1 (en) 2002-03-27
DE60001577T2 (de) 2003-07-10
AU4529400A (en) 2000-12-12
DE60001577D1 (de) 2003-04-10
BR9901553A (pt) 2001-01-16
WO2000071765A1 (en) 2000-11-30

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