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WO2017174185A1 - Alliage d'aluminium destiné notamment à un procédé de coulée, et procédé de fabrication d'une pièce dans un tel alliage d'aluminium - Google Patents

Alliage d'aluminium destiné notamment à un procédé de coulée, et procédé de fabrication d'une pièce dans un tel alliage d'aluminium Download PDF

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Publication number
WO2017174185A1
WO2017174185A1 PCT/EP2017/000411 EP2017000411W WO2017174185A1 WO 2017174185 A1 WO2017174185 A1 WO 2017174185A1 EP 2017000411 W EP2017000411 W EP 2017000411W WO 2017174185 A1 WO2017174185 A1 WO 2017174185A1
Authority
WO
WIPO (PCT)
Prior art keywords
aluminum alloy
weight
component
alloy
manganese
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.)
Ceased
Application number
PCT/EP2017/000411
Other languages
German (de)
English (en)
Inventor
Thomas Stürzel
Karl Weisskopf
Patrick Izquierdo
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.)
Mercedes Benz Group AG
Original Assignee
Daimler AG
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 Daimler AG filed Critical Daimler AG
Priority to CN201780020676.9A priority Critical patent/CN109072354A/zh
Priority to US16/091,840 priority patent/US20190093199A1/en
Priority to JP2018551959A priority patent/JP2019516013A/ja
Publication of WO2017174185A1 publication Critical patent/WO2017174185A1/fr
Anticipated expiration legal-status Critical
Ceased 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D18/00—Pressure casting; Vacuum casting
    • B22D18/04—Low pressure casting, i.e. making use of pressures up to a few bars to fill the mould
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium

Definitions

  • Aluminum alloy in particular for a casting method, and method for producing a component from such an aluminum alloy
  • the invention relates to an aluminum alloy, in particular for a casting method, according to the preamble of patent claim 1 and a method for producing a component from such an aluminum alloy.
  • Such an aluminum alloy in particular for a casting method, can already be taken as known from DE 10 2011 115 345 A1, for example.
  • Aluminum alloy at least aluminum (AI), magnesium (Mg), manganese (Mn) and copper (Cu) on.
  • Object of the present invention is to provide an aluminum alloy and a method of the type mentioned, so that particularly advantageous, in particular mechanical properties of the component can be realized.
  • Patent claim 5 solved.
  • Aluminum alloy manufactured component can be realized, it is
  • the aluminum alloy between 0.001
  • the aluminum alloy has magnesium in a range of 0.05 wt% to 0.45 wt%, manganese in a range of 0.05 wt% to 0.60 wt%, iron up to 1.5 Wt% and copper in a range of from 0.25 wt% to 4.00 wt% inclusive and vanadium in a range of 0.001 wt% to 0.25 wt%.
  • the aluminum alloy has at least 0.10 wt% and less than 0.40 wt% manganese.
  • AI15 Fe, Mn 3Si2 can be lowered so that they can not occur in too coarse blocky morphology.
  • the aluminum alloy has molybdenum (Mo) in a range of from 0.001% by weight to 0.50% by weight inclusive, it being preferred that the aluminum alloy is 0.10% by weight. Molybdenum has.
  • the targeted addition of molybdenum for example, with a proportion of 0.10 wt.%,
  • a rounding indentation up to a polygonal morphology and a finer distribution of the aforementioned iron / manganese phases (Fe / Mn phases) be effected, leading to another
  • the component can, for example, as a crankcase of a
  • Internal combustion engine be formed, which is preferably designed as a diesel engine.
  • the component may also be part of an internal combustion engine of a gasoline engine.
  • Such a component produced from the aluminum alloy has a sufficient strength, in particular high heat resistance, due to the strength mechanism of the aluminum alloy.
  • Aluminum alloy advantageously used to from the aluminum alloy, a cylinder head, for example, as a reciprocating internal combustion engine
  • the component in the heat treatment state T5mod a 0.2% proof stress R p0 , 2 of more than 180 megapascals, a tensile strength R m of more than 220 megapascals and an elongation at break A 5 of more than 1 percent at
  • Room temperature and in the heat treatment state T6red has a 0.2% proof stress Rpo, 2 of more than 200 megapascals, a tensile strength R m of more than 230 megapascals and an elongation at break A 5 of more than 1.5 percent at room temperature.
  • Rpo 0.2% proof stress
  • R m tensile strength
  • R m tensile strength
  • elongation at break A 5 of more than 1.5 percent at room temperature.
  • Heat treatment state T5mod the following values can be achieved: R p o, 2> 1 0
  • the invention is based in particular on the following findings: Due to the low magnesium content or magnesium content, in alloys with a high Fe content (Fe-iron), brittle intermetallic phases are suppressed, which leads to an increase in ductility. Copper leads to a strong increase in strength due to thermal aging as well as to an increased heat resistance of the aluminum alloy.
  • Fe-iron Fe-iron
  • the aluminum alloy according to the invention has proven to be particularly advantageous for the production of thick-walled components which have a wall thickness in a range of from 4 millimeters to 30 millimeters inclusive. Furthermore, it is preferably provided that the casting method in which the component is produced from the aluminum alloy is a die-casting method or laminar die-casting or a sand / mold method.
  • Aluminum alloy according to the invention is in particular a heat-resistant
  • Aluminum alloy in particular a heat-resistant cast aluminum alloy, which is particularly advantageous for the production of components for drive trains.
  • the invention also includes a method for producing a component from an aluminum alloy according to the invention.
  • Advantageous and advantageous embodiments The aluminum alloy according to the invention are advantageous and advantageous
  • Fig. 1 is a schematic representation of a backscattered electron image (BSE image) of the alloy 233 with Kuper (Cu) and molybdenum (Mo) in
  • Heat treatment state T5mod for example, as a
  • Crankcase formed component of said alloy is made by die casting
  • Fig. 2 is a schematic representation of a BSE image of the alloy 226D
  • Fig. 3 is a BSE image of the alloy 233 with Cu and Mo im
  • Fig. 4 is a BSE image of the alloy 226D in the heat treatment state T6red
  • Fig. 5 is a diagram illustrating mechanical characteristics of the component formed of the respective alloy at room temperature.
  • FIG. 6 shows a diagram for illustrating mechanical characteristics of the component produced from the respective alloy at 150 degrees Celsius.
  • Figures 1 to 4 show respective backscattered electron images (BSE images) of alloys from which respective components are made.
  • the respective alloy is, for example, an aluminum alloy, in particular an aluminum casting alloy and preferably a heat-resistant aluminum casting alloy.
  • the respective component produced from the respective alloy is, for example, a component which is used in a drive train of a motor vehicle, the component being, for example, a crankcase, in particular a die-cast crankcase. This means that the component is produced from the respective alloy by casting, in particular by die casting.
  • the component may be a thick-walled component which has a wall thickness in a range of 4 mm to 30 mm inclusive.
  • the respective aluminum alloy has the following composition:
  • the aluminum alloy comprises magnesium with at least 0.10% by weight and less than 0.30% by weight.
  • the aluminum alloy has manganese with at least 0.10 wt.% And less than 0.40 wt.%.
  • This phase does not dissolve at a solution annealing temperature of 465 degrees Celsius and would due to the increased Fe content additionally alloyed magnesium (Mg) only and lead to skeletal Fe-containing intermetallic phases, which are detrimental to the ductility in the form of waste Elongation at break and not more for one
  • the copper content (Cu content) is used for the targeted adjustment of the required strength due to the formation of strength-increasing precipitates during thermal aging. However, it must be ensured that an excessively high copper content during T5 heat treatment leads to embrittlement. In a T6 heat treatment, the full
  • Ti titanium
  • Zr zirconium
  • Ti, Zr zirconium
  • the addition of strontium (Sr) results in a refining of the Al / Si eutectic from coarse-plate to a refined, coral-like morphology, which increases ductility. This fine Si morphology can be easily and quickly formed by a T6 solution annealing and thus the ductility can be increased again.
  • the aforementioned aluminum alloy is melted from master alloys, pure elements, or prepared by alloying suitable secondary alloys such as 233 or 226 at a sufficiently high temperature. Furthermore, the alloy is poured off at at least 650 degrees Celsius to 720 degrees Celsius in a tempered and forced or vacuum-vented tempered permanent mold. If the casting temperature is too low, there is a risk of inadequate mold filling and cold runs as well as undesirable formation of intermetallic phases. Excessive casting temperatures increase the risk of porosity, shrinkage and shrinkage Hot cracking. After removal of the component produced by casting, the component is - to the realization of the heat treatment state T6red - in air or -
  • FIG. 1 shows a backscattered electron image of said secondary alloy 233 with copper and molybdenum. Roundish to polygonal molybdenum-containing AlFeMnSi intermetallic phases are recognizable.
  • FIG. 2 shows a backscatter electron image of said secondary alloy 226D
  • intermetallic Alis (Fe, Mn, Cr, Cu) 3 Si2 phases present, which have formed due to their size primarily in the casting chamber of the die casting machine.
  • Two-dimensional grinding appear as needles and are present in reality as three-dimensional plates and thus exist as large-scale, sharp-edged Geglagetrennungen between the ductile Al dendrites. These phases significantly reduce ductility.
  • Secondary alloy also form Al7Cu2 (Fe, Ni) phases, which can not be resolved by a solution annealing at 465 degrees Celsius and thus continue to exist as brittle phases and also set Cu (see Fig. 4).
  • Figs. 5 and 6 are diagrams for illustrating mechanical properties of components made of the aforementioned aluminum alloy.
  • beams 10 illustrate the 0.2% yield strength R p0 , 2, with bars 12 illustrating the yield strength R m .
  • triangles 14 illustrate the elongation at break A5.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Continuous Casting (AREA)
  • Cylinder Crankcases Of Internal Combustion Engines (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)

Abstract

La présente invention concerne un alliage d'aluminium, notamment destiné à un procédé de coulée, l'alliage d'aluminium présentant au moins de l'aluminium, du magnésium, du manganèse et du cuivre, l'alliage d'aluminium présentant : - de 0,001 % en poids à 0,50 % en poids de molybdène, - de 0,05 % en poids à 0,45 % en poids de magnésium, - de 0,05 % en poids à 0,60 % en poids de manganèse, - maximum 1,5 % en poids de fer, - de 0,25 % en poids à 4,00 % en poids de cuivre et - de 0,001 % en poids à 0,25 % en poids de Vanadium.
PCT/EP2017/000411 2016-04-07 2017-04-04 Alliage d'aluminium destiné notamment à un procédé de coulée, et procédé de fabrication d'une pièce dans un tel alliage d'aluminium Ceased WO2017174185A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201780020676.9A CN109072354A (zh) 2016-04-07 2017-04-04 用于铸造法的铝合金以及用这种铝合金制造构件的方法
US16/091,840 US20190093199A1 (en) 2016-04-07 2017-04-04 Aluminum Alloy, in Particular for a Casting Method, and Method for Producing a Component from Such an Aluminum Alloy
JP2018551959A JP2019516013A (ja) 2016-04-07 2017-04-04 特に鋳造法用のアルミニウム合金及びそのようなアルミニウム合金から部品を製造するための方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102016004216.8 2016-04-07
DE102016004216.8A DE102016004216A1 (de) 2016-04-07 2016-04-07 Aluminiumlegierung, insbesondere für ein Gießverfahren, sowie Verfahren zum Herstellen eines Bauteils aus einer solchen Aluminiumlegierung

Publications (1)

Publication Number Publication Date
WO2017174185A1 true WO2017174185A1 (fr) 2017-10-12

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2017/000411 Ceased WO2017174185A1 (fr) 2016-04-07 2017-04-04 Alliage d'aluminium destiné notamment à un procédé de coulée, et procédé de fabrication d'une pièce dans un tel alliage d'aluminium

Country Status (5)

Country Link
US (1) US20190093199A1 (fr)
JP (1) JP2019516013A (fr)
CN (1) CN109072354A (fr)
DE (1) DE102016004216A1 (fr)
WO (1) WO2017174185A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019205267B3 (de) * 2019-04-11 2020-09-03 Audi Ag Aluminium-Druckgusslegierung

Families Citing this family (7)

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Publication number Priority date Publication date Assignee Title
DE102017007475A1 (de) 2017-08-08 2018-02-22 Daimler Ag Verfahren zum Auflegieren einer Al-haltigen Ausgangslegierung
CN107815560A (zh) * 2017-10-11 2018-03-20 徐长勇 一种高质量合金铝棒制备工艺
KR20210042639A (ko) 2019-10-10 2021-04-20 주식회사 삼기 알루미늄 다이캐스팅 제품의 제조방법 및 이 방법에 의해 제조된 알루미늄 다이캐스팅 제품
DE102021102268A1 (de) * 2021-02-01 2022-08-04 Trimet Aluminium Se Aluminiumlegierung, Bauteil aus einer Aluminiumlegierung und Verfahren zum Herstellen eines Bauteils aus einer Aluminiumlegierung
JP2022142192A (ja) * 2021-03-16 2022-09-30 日立金属株式会社 アルミニウム合金線
CN116623047A (zh) * 2023-05-04 2023-08-22 深圳南科强正轻合金技术有限公司 一种铝合金及其制备方法、压铸件
CN118109723B (zh) * 2024-04-28 2024-06-25 内蒙金属材料研究所 一种氮化铝增强铝基复合材料及其制备方法

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DE102009036056A1 (de) * 2009-08-04 2011-02-10 Daimler Ag Al-Druckgusslegierung für dickwandige Druckgussteile
DE102011115345A1 (de) 2011-10-07 2013-04-11 Daimler Ag Aluminiumlegierung, insbesondere für ein Druckgussverfahren
EP2735621A1 (fr) * 2012-11-21 2014-05-28 Georg Fischer Druckguss GmbH & Co. KG Alliage à coulée sous pression en aluminium
CN105401005A (zh) * 2015-10-30 2016-03-16 重庆宗申动力机械股份有限公司 一种Al-Si合金材料及其生产方法

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FR2857378B1 (fr) * 2003-07-10 2005-08-26 Pechiney Aluminium Piece moulee en alliage d'aluminium a haute resistance a chaud
SI1612286T1 (sl) * 2004-06-29 2011-10-28 Rheinfelden Aluminium Gmbh Aluminijeva legura za tlačno litje
JP2006283124A (ja) * 2005-03-31 2006-10-19 Kobe Steel Ltd 耐磨耗性冷間鍛造用アルミニウム合金
CN102796925B (zh) * 2011-05-27 2015-04-15 广东鸿泰科技股份有限公司 一种压力铸造用的高强韧压铸铝合金
CN105316542B (zh) * 2015-11-25 2019-02-05 广东鸿图科技股份有限公司 一种高强度高韧性压铸铝合金及其制品

Patent Citations (4)

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Publication number Priority date Publication date Assignee Title
DE102009036056A1 (de) * 2009-08-04 2011-02-10 Daimler Ag Al-Druckgusslegierung für dickwandige Druckgussteile
DE102011115345A1 (de) 2011-10-07 2013-04-11 Daimler Ag Aluminiumlegierung, insbesondere für ein Druckgussverfahren
EP2735621A1 (fr) * 2012-11-21 2014-05-28 Georg Fischer Druckguss GmbH & Co. KG Alliage à coulée sous pression en aluminium
CN105401005A (zh) * 2015-10-30 2016-03-16 重庆宗申动力机械股份有限公司 一种Al-Si合金材料及其生产方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019205267B3 (de) * 2019-04-11 2020-09-03 Audi Ag Aluminium-Druckgusslegierung

Also Published As

Publication number Publication date
CN109072354A (zh) 2018-12-21
DE102016004216A1 (de) 2016-09-29
US20190093199A1 (en) 2019-03-28
JP2019516013A (ja) 2019-06-13

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