EP1190107A1 - Alliage a base d'aluminium destine a la fabrication de culasses - Google Patents

Alliage a base d'aluminium destine a la fabrication de culasses

Info

Publication number
EP1190107A1
EP1190107A1 EP00926595A EP00926595A EP1190107A1 EP 1190107 A1 EP1190107 A1 EP 1190107A1 EP 00926595 A EP00926595 A EP 00926595A EP 00926595 A EP00926595 A EP 00926595A EP 1190107 A1 EP1190107 A1 EP 1190107A1
Authority
EP
European Patent Office
Prior art keywords
weight
content
less
alloy
magnesium
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
EP00926595A
Other languages
German (de)
English (en)
Other versions
EP1190107B1 (fr
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/fr
Application granted granted Critical
Publication of EP1190107B1 publication Critical patent/EP1190107B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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 Aluminum-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.
  • 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 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, 5 (Fe,Mn) 3 Si 2 kinds.
  • Figures la and lb present typical microstructures of an automotive cylinder head cast in the alloy described in Table IV (with a content of 4.5% of copper and 0.7% of magnesium respectively).
  • Figures 2a and 2b provide a detailed view of the microstructures seen in Figure 1 , showing the eutectics rich in copper and magnesium respectively of the alloy described in Table IV.
  • Figure 3 shows the Brinell hardness figures obtained with test specimens cast in sand molds in accordance with the copper content of the alloys described in Table IV, without magnesium.
  • Figure 4 shows the Brinell hardness figures obtained with test specimens cast in sand molds in accordance with the magnesium content of the alloys described in Table IV, without copper.
  • Figure 5 shows the Brinell hardness figures obtained with test specimens cast in sand molds in accordance with a magnesium content ranging from 0.4% to 0.9% of the alloys described in Table IV, with a 4.5% copper content.
  • Figure 6 shows the differential thermal analysis curve of the traditional B alloy (Table I) (DTA) and its respective derivative (DDTA- hatched line).
  • Figure 7 shows the differential thermal analysis curves of two specimens of the modified alloy (Table IV) with 4.5% of copper, by weight, and 0.7% of magnesium, by weight (DTA-1 and DTA-2).
  • Figure 8 shows the reproduction of one of the differential thermal analysis curves of the special modified alloy (Table IV), in which the four solidification stages (described in Table V) have been market out.
  • Figure 9 shows the Brinell hardness evolution curves in alloy test specimens described in Table IV, with a copper weight of 4.2% and a magnesium weight of 0.7%, relative to the three room temperatures (5°C, 22°C and 35°C). For all cases the process of precipitation is more intense in the first 24 hours.
  • Figures la and l b 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 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. Analogously, Wiss e Sanders' 4 ' observed the same phenomenon in the Al-Cu class of alloys (containing roughly 2.6% Cu, by weight, and 0.20% Mg, by weight).
  • 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
  • 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 magnesium. 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).
  • Solidification Characteristics of the Alloy 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).
  • 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 IV kinds present the same solidification reactions, for the same products, differing only in the volumetric fractions of the phases that occur at each stage of the solidification.
  • 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%.
  • 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%o.
  • 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)

Abstract

L'invention concerne un alliage à base d'aluminium destiné à la fabrication de culasses sans traitement thermique et comprenant les éléments suivants: silicium, dont la teneur varie entre 5,0 % et 10,0 % en poids; cuivre, dont la teneur varie entre 4,0 % et 6,0 % en poids; magnésium, dont la teneur varie entre 0,6 % et 1,0 % en poids; fer, avec une teneur inférieure à 0,7 % en poids; manganèse, avec une teneur inférieure à 0,3 % en poids; nickel, avec une teneur inférieure à 0,1 % en poids; zinc, avec une teneur inférieure à 1,0 % en poids; titane, avec une teneur inférieure à 0,2 % en poids; strontium, avec une teneur inférieure à 0,02 % en poids; et étain, avec une teneur inférieure à 0,20 % en poids; le reste étant de l'aluminium.
EP00926595A 1999-05-19 2000-05-19 Alliage a base d'aluminium destine a la fabrication de culasses Expired - Lifetime EP1190107B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
BR9901553 1999-05-19
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
PCT/BR2000/000056 WO2000071765A1 (fr) 1999-05-19 2000-05-19 Alliage a base d'aluminium destine a la fabrication de culasses

Publications (2)

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

Family

ID=4072293

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00926595A Expired - Lifetime EP1190107B1 (fr) 1999-05-19 2000-05-19 Alliage a base d'aluminium destine a la fabrication de culasses

Country Status (5)

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

Families Citing this family (8)

* 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
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
EP4256099A1 (fr) * 2020-12-07 2023-10-11 Norsk Hydro ASA Alliage alsicu stable à haute température

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

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO0071765A1 *

Also Published As

Publication number Publication date
DE60001577D1 (de) 2003-04-10
EP1190107B1 (fr) 2003-03-05
BR9901553A (pt) 2001-01-16
WO2000071765A1 (fr) 2000-11-30
DE60001577T2 (de) 2003-07-10
AU4529400A (en) 2000-12-12

Similar Documents

Publication Publication Date Title
CN104093867B (zh) 高性能AlSiMgCu铸造合金
CN109868393B (zh) 用于气缸盖的高温铸造铝合金
CN105483465B (zh) 一种压铸用Al-Si-Mg铸造铝合金及其制备方法
WO1996010099A1 (fr) Alliages de fonderie d'aluminium a haute resistance pour applications structurelles
JP4914225B2 (ja) アルミニウム合金系の材料、その製造方法並びにその使用
MX2011000739A (es) Pieza moldeada de aleacion de aluminio que tiene resistencias elevadas a la fatiga y la fluencia en caliente.
Sigworth et al. The metallurgy of aluminum alloys for structural high-pressure die castings
EP1190107B1 (fr) Alliage a base d'aluminium destine a la fabrication de culasses
US4569702A (en) Copper base alloy adapted to be formed as a semi-solid metal slurry
JP4526768B2 (ja) マグネシウム合金
JPH01180938A (ja) 耐摩耗性アルミニウム合金
CN111979455B (zh) 一种压铸铝合金及其制备方法和应用
Kapranos Thixoforming of aluminum A201-expectations and fulfilment
JPH0448856B2 (fr)
CN106011507A (zh) 一种Al-Mg-Si-Y稀土铝合金及其制备方法
JP2004225121A (ja) ダイカスト鋳造ピストン用合金
Reznik et al. Influence of Al-Cu-Mn-Fe-Ti alloy composition and production parameters of extruded semi-finished products on their structure and mechanical properties
JPS6047898B2 (ja) 耐熱性のすぐれた鋳物用アルミニウム合金
JPS60152648A (ja) 成形鋳物用アルミニウム合金
CN85102237A (zh) 低硅铜镁镝系高强度铸造铝合金
JPH01108339A (ja) ピストン用耐熱高強度アルミニウム合金
Meinathan et al. Investigation of the influence of Cu on Mg added Al-Si-Cu (A319) alloy
JPH0565573B2 (fr)
RU2081934C1 (ru) Деформируемый термически неупрочняемый сплав на основе алюминия
SU1735419A1 (ru) Сплав на основе алюмини

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20011109

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

17Q First examination report despatched

Effective date: 20020508

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Designated state(s): DE FR GB

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 60001577

Country of ref document: DE

Date of ref document: 20030410

Kind code of ref document: P

LTIE Lt: invalidation of european patent or patent extension

Effective date: 20030305

ET Fr: translation filed
PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20031208

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: GB

Ref legal event code: 746

Effective date: 20050207

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20130531

Year of fee payment: 14

Ref country code: GB

Payment date: 20130425

Year of fee payment: 14

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20130531

Year of fee payment: 14

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 60001577

Country of ref document: DE

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20140519

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20150130

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 60001577

Country of ref document: DE

Effective date: 20141202

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20141202

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140519

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140602