EP1331281A1 - Aluminiumlegierung zum Druckgiessen, Herstellungsverfahren durch Druckgiessen dieser Legierung, und durch dieses Verfahren hergestelltes druckgegossenes Produkt - Google Patents

Aluminiumlegierung zum Druckgiessen, Herstellungsverfahren durch Druckgiessen dieser Legierung, und durch dieses Verfahren hergestelltes druckgegossenes Produkt Download PDF

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Publication number
EP1331281A1
EP1331281A1 EP03000610A EP03000610A EP1331281A1 EP 1331281 A1 EP1331281 A1 EP 1331281A1 EP 03000610 A EP03000610 A EP 03000610A EP 03000610 A EP03000610 A EP 03000610A EP 1331281 A1 EP1331281 A1 EP 1331281A1
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Prior art keywords
die casting
weight
aluminum alloy
amount ranging
product
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EP03000610A
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English (en)
French (fr)
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EP1331281B1 (de
Inventor
Sanji Kitaoka
Yukio Kuramasu
Shinichiro Sumi
Kenji Tsushima
Hiroshi Kambe
Masahiko Shioda
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Nissan Motor Co Ltd
Nippon Light Metal Co Ltd
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Nissan Motor Co Ltd
Nippon Light Metal Co Ltd
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Publication of EP1331281A1 publication Critical patent/EP1331281A1/de
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • B22D17/14—Machines with evacuated die cavity

Definitions

  • This invention relates to improvements in aluminum alloy for a die casting which alloy can obtain excellent mechanical properties upon die casting, and more particularly to the aluminum alloy for a die casting which alloy is excellent in static and dynamic mechanical performances and suitable to be applicable to vehicle body parts of an automotive vehicle such as various pillars, a roof, a joint of a space frame and an installation section of a suspension, and suspension parts of the automotive vehicle such as a suspension arm, a sub-frame, link parts of a suspension and an engine cradle, and further relates to a die casing product using the aluminum alloy and to a production method for the die casting product.
  • the die casting has been hitherto extensively used for producing parts of an engine and parts of a transmission of an automotive vehicle for the reasons why a casting having thin walls can be obtained, a dimensional accuracy is high, a productivity is high, and freedom in selecting a shape is high, and the like.
  • a joint of a space frame, a center pillar and the like constituting a vehicle body have become formed of an aluminum alloy die casting which is adjusted in mechanical properties such as tensile strength, 0.2 % proof stress, elongation and the like by applying a heat treatment on a die casting which has been produced by a vacuum die casting.
  • "365 alloy” according to Aluminum Association Standard is extensively used in Europe and the United States of America as disclosed in Japanese Patent Provisional Publication No. 8-41575.
  • weight-lightening of the vehicle is a very important technique.
  • application of the aluminum alloy die casting seems to be one of favorable measures for coping with the requirements.
  • Vehicle body parts of an automotive vehicle such as various pillars, joint sections of space frames are required to stably have high strength and elongation even in a high speed deformation region for the purpose of securing safety in the event of vehicle collision.
  • discussion of static strength and elongation has been made on the conventional aluminum alloys for die casting.
  • the conventional aluminum alloys for die casting have a theme to solve the above problems.
  • an object of the present invention to provide an improved aluminum alloy for a die casting which alloy can overcome drawbacks encountered in conventional aluminum alloys for die casting.
  • Another object of the present invention is to provide an improved aluminum alloy for a die casting which alloy can stably exhibit high strength and elongation in a high strain rate region in case of application as parts of an automotive vehicle, thereby enabling the body part to be further weight-lightened.
  • a further object of the present invention is to provide an improved aluminum alloy for a die casing, in which primary crystal ⁇ -phase is fined by single and large amount addition of B thereby ensuring an excellent balance between strength and elongation, while eutectic Si particle is fined by addition of Sb thereby ensuring further improved elongation and toughness.
  • a still further object of the present invention is to provide an improved method of producing a die casting product using the improved aluminum alloy, by which method the die casting product can be effectively obtained without lowering the excellent mechanical properties or performances (particularly the elongation and toughness) possessed by the improved aluminum alloy.
  • a still further object of the present invention is to provide an improved die casting product such as parts of an automotive vehicle, which product is high in strength and elongation in a high strain rate region such as vehicle collision, thereby enabling the parts to be further weight-lightened.
  • An aspect of the present invention resides in an aluminum alloy for a die casting, comprising or consisting essentially of Si in an amount ranging from 10 to 12 % by weight, Mg in an amount ranging from 0.15 to 0.50 % by weight, Mn in an amount ranging from 0.5 to 1.0 % by weight, Fe in an amount of not more than 0.15 % by weight, Ti in an amount of not more than 0.1 % by weight, Sb in an amount ranging from 0.05 to 0.20 % by weight, B in an amount ranging from 0.005 to 0.02%, and balance consisting of aluminum and inevitable impurities.
  • the method comprises forming an aluminum alloy into a die casting by high vacuum die casting to obtain the die casting product.
  • the aluminum alloy comprises or consists essentially of Si in an amount ranging from 10 to 12 % by weight, Mg in an amount ranging from 0.15 to 0.50 % by weight, Mn in an amount ranging from 0.5 to 1.0 % by weight, Fe in an amount of not more than 0.15 % by weight, Ti in an amount of not more than 0.1 % by weight, Sb in an amount ranging from 0.05 to 0.20 % by weight, B in an amount ranging from 0.005 to 0.02%, and balance consisting of aluminum and inevitable impurities.
  • a further aspect of the present invention resides in a die casting product produced by the method comprising forming an aluminum alloy into a die casting by high vacuum die casting to obtain the die casting product.
  • the aluminum alloy comprises or consists essentially of Si in an amount ranging from 10 to 12 % by weight, Mg in an amount ranging from 0.15 to 0.50 % by weight, Mn in an amount ranging from 0.5 to 1.0 % by weight, Fe in an amount of not more than 0.15 % by weight, Ti in an amount of not more than 0.1 % by weight, Sb in an amount ranging from 0.05 to 0.20 % by weight, B in an amount ranging from 0.005 to 0.02%, and balance consisting of aluminum and inevitable impurities.
  • an aluminum alloy for a die casting comprises or consists essentially of Si in an amount ranging from 10 to 12 % by weight, Mg in an amount ranging from 0.15 to 0.50 % by weight, Mn in an amount ranging from 0.5 to 1.0 % by weight, Fe in an amount of not more than 0.15 % by weight, Ti in an amount of not more than 0.1 % by weight, Sb in an amount ranging from 0.05 to 0.20 % by weight, B in an amount ranging from 0.005 to 0.02 % by weight, and balance consisting of aluminum and inevitable impurities.
  • Sb in the amount ranging from 0.05 to 0.20 % by weight may be replaced with Sr in an amount ranging from 0.005 to 0.020 % by weight.
  • a method of producing a die casting product according to the present invention comprises forming the aluminum alloy into a die casting by high vacuum die casting to obtain the die casting product.
  • the obtained die casting product is preferably subjected to a solution treatment at a temperature of not lower than 530 °C for a time of not longer than 1 hr., and thereafter subjected to an aging treatment.
  • the die casting product according to the present invention is preferably a vehicle body part of an automotive vehicle, such as a so-called A pillar, a so-called B pillar, a so-called C pillar, a roof, a joint of a space frame or an installation section of a suspension, or a suspension part of an automotive vehicle such as a suspension arm, a sub-frame, a link part of a suspension or an engine cradle.
  • the A pillar is, for example, a pillar located between the window glass of a front windshield and a front door in a sedan-type passenger car.
  • the B pillar is, for example, a pillar located between the window glass of a front door and the window glass of a rear door in the sedan-type passenger car.
  • the C pillar is, for example, a pillar located between the window glass of the rear door and a rear window glass in the sedan-type passenger car.
  • the space frame is a frame structure which is constituted by connecting pipes or the like and usually used in a vehicle body of aluminum.
  • composition of the aluminum alloy according to the present invention and reasons for determining conditions of treatments and the like along with effects obtained by the compositions and the conditions.
  • Si is an element effective for improving the flowability of molten metal during die casting. If the content of Si is less than 10 % by weight, the effect is little. If the amount of Si exceeds 12 % by weight, the crystallization amount of eutectic Si increases or the primary crystal Si crystallizes thereby lowering the elongation and toughness in a high strain rate region such as during vehicle collision. Accordingly, the Si content is within the range of from 10 to 12 % by weight.
  • Mg is an element contributable for improving the strength by crystallization of Mg 2 Si during the aging treatment upon coexistence of Si. If the content of Mg is less than 0.15 % by weight, the effect of improving the strength is little. If the content of Mg exceeds 0.5 % by weight, the crystallization amount of Mg 2 Si increases thereby lowering the elongation and toughness. Consequently, the Mg content is set within the range of from 0.15 to 0.5 by weight.
  • Mn is an element contributable for improving the strength by forming fine intermetallic compound upon coexistence of Fe and Si. Additionally, Mn is an element contributable for preventing burning of a product to a die during die casting. If the content of Mn is less than 0.5 % by weight, the sufficient effect cannot be obtained. If the content of Mn exceeds 1.0 % by weight, coarse Al-Mn-Fe-Si-based intermetallic compounds crystallize thereby lowering the elongation (particularly, elongation in the high strain rate region). Consequently, the Mn content is set within the range of from 0.5 to 1.0 % by weight.
  • Fe is an element for preventing burning of the product to the die during die casting. If the content of Fe exceeds 0.15 % by weight, the crystallization amount of needle-like Fe-based intermetallic compound increases thereby lowering the elongation and toughness. Consequently, the Fe content is set at a value of not more than 0.15 % by weight.
  • Ti and B are elements effective for improving the mechanical properties of aluminum casting because TiB 2 formed upon addition of Ti and B serves as a heterogeneous nuclear of aluminum solid solution thereby fining the primary crystal ⁇ (Al)-phase.
  • composite addition of Ti and B provides no effect for fining the primary crystal ⁇ -phase, and that addition of a large amount of only B fines the primary crystal ⁇ phase thereby improving the mechanical properties of the alloy.
  • Ti seems to be an impurity element for impeding fining of the primary crystal ⁇ -phase, and therefore the content of Ti is set within a range of not more than 0.1 % by weight.
  • B is the element for improving the mechanical properties of the alloy by fining the primary crystal ⁇ phase, in which the content of B is set within a range of from 0.05 to 0.02 % by weight because the effect is little if the B content is less than 0.05.
  • the effect of fining the primary crystal ⁇ -phase upon addition of B will be discussed in detail with reference to Examples after.
  • Sb and Sr are elements contributable for improving the elongation and toughness by fining eutectic Si particle crystallized in Al-Si based die casting. If the contents of Sb and Sr are respectively less than 0.05 and less than 0.005 % by weight, the effects are little. If the contents of Sb and Sr respectively exceed 0.20 and 0.020 % by weight, intermetallic compound of Al is formed thereby lowering the elongation and toughness. Consequently, the contents of Sb and Sr are respectively set within the range of from 0.05 to 0.20 % by weight and the range of from 0.005 to 0.020 % by weight. It has become apparent in the alloy of the present invention that Sb is larger in effect than Sr.
  • Solution treatment time not longer than 1 hour
  • the solution treatment is a very effective measure.
  • the solution treatment is carried out at a temperature exceeding 530 °C and a time exceeding 1 hour, spheroidization of eutectic Si progresses while coarsening the eutectic Si.
  • the solution treatment is carried out at a temperature lower than 530 °C, it is difficult to accomplish both the fining and granulating the eutectic Si particle. Consequently, the solution treatment temperature is set at a value not lower than 530 °C, and the solution treatment time is set at a value not longer than 1 hour.
  • Aluminum alloys of Examples 1 to 3 and Comparative Examples 1 to 3 and raw materials for the aluminum alloys had respectively compositions shown in Table 1.
  • the Comparative Examples 1 and 2 corresponded to the "365 alloy" according to Aluminum Association Standard. Items Chemical composition (wt.%) Si Mg Mn Fe Ti Sb Sr B Al Example 1 10.7 0.24 0.73 0.04 0.001 0.10 - 0.009 Balance 2 10.9 0.27 0.72 0.05 0.0009 0.10 - 0.005 Balance 3 11.0 0.26 0.68 0.05 0.001 - 0.010 0.010 Balance Comparative Example 1 10.5 0.25 0.67 0.07 0.10 - 0.009 - Balance 2 10.4 0.27 0.70 0.06 0.11 - 0.011 0.002 Balance 3 10.6 0.25 0.71 0.04 0.15 0.09 - 0.006 Balance
  • Each aluminum alloy of Examples and Comparative Examples shown in Table 1 was produced upon melting at 750 °C, thus preparing molten metal of the aluminum alloy.
  • the aluminum alloy molten metal was subjected to a bubbling treatment with argon gas for the purpose of removal of inclusions and degasfication.
  • the molten metal of the aluminum alloy underwent die casting by using a high vacuum die casting machine having a clamping force of 320 tons, after coating a mold releasing agent onto the cavity of dies, under the following conditions: a casting pressure was 60 MPa, a high speed injection rate was 3.5 m/s, a degree of vacuum within a sleeve through which the molten metal flowed was 0.96 atmosphere, and a degree of vacuum of a vacuum valve section was 0.95 atmosphere.
  • the temperature of the molten metal during die casting was 680 °C.
  • the cavity of the dies had such a cross-sectional shape shown in Fig. 1, which corresponded to a product (specimen material) having a thickness of 2 mm and a length of 410 mm.
  • the product or die casting produced as discussed above was subjected to the solution treat at 540 °C for 30 minutes and immediately thereafter underwent the aging treatment at 160 °C for 45 minutes, thus forming the specimen material corresponding to the shape of Fig. 1.
  • a specimen of the shape of JIS 13B as shown in Fig. 2 was cut out from the above specimen material and had a thickness (t) of 2 mm.
  • the shape of JIS 13B was according to JIS (Japanese Industrial Standard) Z 2201.
  • the specimen was subjected to a static tensile test at a strain rate of 0.001/s by using an Instron universal tester (AG-10TC) produced by Shimadzu Corporation.
  • AG-10TC Instron universal tester
  • a specimen of the shape as shown in Fig. 3 was cut out from the above specimen material.
  • the specimen was subjected to a dynamic tensile test at a strain rate of about 1000/s by using a so-called One-Bar Method high speed tensile tester as illustrated in Fig. 4.
  • the dynamic tensile test was conducted as follows: With reference to Fig. 4, the specimen 10 as shown in Fig. 3 was disposed between an output rod 12 and an impact block 14. The output shaft 12 was fixed at its one end. The specimen 10 was connected to the impact block 14 at a position A and connected to the other end of the output rod 12 at a position B. A hummer 16 was impacted against the impact block 14 at a rate or velocity of V 0 (t). At this time, a displacement rate or velocity V(t) at the position A was measured by an optical displacement meter (not shown), while a strain was measured by the strain gauge 18 attached to the output rod 12.
  • the thus determined nominal stress corresponds to a tensile strength (MPa).
  • ⁇ (t) was determined according to the following equation: where U A (t) is the displacement at the position A; U B (t) is the displacement at the position B; L is the distance of the specimen between the positions A and B; and V(t) is the speed of the impact block.
  • Each aluminum alloy of Examples and Comparative Example shown in Table 3 was produced upon melting at 750 °C, thus preparing molten metal of the aluminum alloy.
  • the aluminum alloy molten metal was subjected to a bubbling treatment with argon gas for the purpose of removal of inclusions and degasfication.
  • the molten metal of aluminum alloy was cast into a wedge-shaped specimen as shown in Figs. 5A to 5C by using a gravity casting, in which the temperature of the molten metal was 700 °C during casting.
  • FIG. 6A to 6D A slowly cooled section (indicated as "Observed Position" in Fig. 5C) of the wedge-shaped specimen formed by the gravity casting was cut out and ground, and thereafter was etched by using an etching reagent of cupric chloride, followed by observation of the macro-structure thereof.
  • the result of the observation is shown in Figs. 6A to 6D.
  • Figs. 6A, 6B, 6C and 6D which are respectively photographs showing the macro-structures of Example 1, Comparative Example 3, Comparative Example 4 and Comparative Example 5.
  • the alloy (Example 1) of the B single and large amount addition type has finer macro-structure than the alloy (Comparative Example 4) of the Ti addition type and the alloys (Comparative Examples 3 and 5) of the Ti-B addition type which have been conventionally considered effective for fining the primary crystal ⁇ phase. From this test result, the reason why the aluminum alloy according to the present invention possesses an excellent balance between the strength and the elongation resides in the fact that the primary crystal ⁇ phase is fined by the single and large amount addition of B.
  • Each aluminum alloy of Examples and Comparative Example shown in Table 4 was produced in an amount of 8 kg upon melting at 750 °C, thus preparing molten metal of the aluminum alloy.
  • the aluminum alloy molten metal was subjected to a bubbling treatment with argon gas for the purpose of removal of inclusions and degasfication. Thereafter, the molten metal was cooled to 700 °C and kept at a constant temperature as it was in a crucible. During keeping at the constant temperature, the molten metal was sampled at every predetermined time lapse.
  • the sampled molten metal was subjected to an ICP (induction couple plasma) emission spectral analysis according to JIS H 1307, in which the concentration of B in the sampled molten metal was measured.
  • ICP induction couple plasma
  • a line a represents the result of Example 4
  • a line b represents the result of Comparative Example 6
  • a line c represents the result of Comparative Example 7.
  • the primary crystal ⁇ phase is fined by the single and large amount addition of B, thereby ensuring an excellent balance between strength and elongation.
  • the eutectic Si particle is fined by addition of Sb, thereby ensuring further improved elongation and toughness.
  • the alloy of the present invention can be applied, for example, to the vehicle body parts of an automotive vehicle such as the A pillar, the B pillar, the C pillar, the roof, the joint of a space frame, the installation section of a suspension, and additionally the suspension parts of an automotive vehicle such as the suspension arm, the sub-frame, the link parts of the suspension and the engine cradle.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Body Structure For Vehicles (AREA)
  • Continuous Casting (AREA)
EP03000610A 2002-01-18 2003-01-14 Aluminiumlegierung zum Druckgiessen, Herstellungsverfahren durch Druckgiessen dieser Legierung, und durch dieses Verfahren hergestelltes druckgegossenes Produkt Expired - Fee Related EP1331281B1 (de)

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JP2002009839A JP4007488B2 (ja) 2002-01-18 2002-01-18 ダイカスト用アルミニウム合金、ダイカスト製品の製造方法およびダイカスト製品
JP2002009839 2002-01-18

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7108042B2 (en) * 2004-06-29 2006-09-19 Aluminum Rheinfelden Gmbh Aluminum diecasting alloy
EP2226397A1 (de) * 2009-03-06 2010-09-08 Rheinfelden Alloys GmbH & Co. KG Aluminiumlegierung
WO2010124835A1 (de) * 2009-04-28 2010-11-04 Belte Ag Aluminium-silizium-druckgusslegierung für dünnwandige strukturbauteile
EP2455505A1 (de) 2010-11-19 2012-05-23 Martinrea Honsel Germany GmbH Zylinderkopf für Verbrennungsmotoren aus einer Aluminiumlegierung
WO2012138767A2 (en) 2011-04-04 2012-10-11 Emerson Climate Technologies, Inc. Aluminum alloy compositions and methods for die-casting thereof
EP2735621A1 (de) * 2012-11-21 2014-05-28 Georg Fischer Druckguss GmbH & Co. KG Aluminium-Druckgusslegierung
US11584977B2 (en) 2015-08-13 2023-02-21 Alcoa Usa Corp. 3XX aluminum casting alloys, and methods for making the same

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JP4341438B2 (ja) * 2004-03-23 2009-10-07 日本軽金属株式会社 耐摩耗性に優れたアルミニウム合金及び同合金を用いた摺動部材
JP2006183122A (ja) * 2004-12-28 2006-07-13 Denso Corp ダイカスト用アルミニウム合金およびアルミニウム合金鋳物の製造方法
JP5076455B2 (ja) * 2006-11-17 2012-11-21 日産自動車株式会社 アルミニウム合金ダイカスト及びその製造方法
RU2536566C2 (ru) * 2009-03-06 2014-12-27 Райнфельден Эллойз Гмбх & Ko.Кг Сплав алюминия
CN102019967A (zh) * 2010-06-13 2011-04-20 贾秉成 一种车架部件
EP2653579B1 (de) * 2012-04-17 2014-10-15 Georg Fischer Druckguss GmbH & Co. KG Aluminium-Legierung
US9677158B2 (en) * 2013-03-15 2017-06-13 GM Global Technology Operations LLC Aluminum alloy suitable for high pressure die casting
CN105483465B (zh) * 2015-12-21 2018-07-31 河北立中有色金属集团有限公司 一种压铸用Al-Si-Mg铸造铝合金及其制备方法
CN107876725B (zh) * 2017-11-29 2019-12-27 沈阳工业大学 一种镁合金方向盘骨架的制备方法

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Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7108042B2 (en) * 2004-06-29 2006-09-19 Aluminum Rheinfelden Gmbh Aluminum diecasting alloy
US8480822B2 (en) 2009-03-06 2013-07-09 Rheinfelden Alloys Gmbh & Co. Kg Aluminum alloy
EP2226397A1 (de) * 2009-03-06 2010-09-08 Rheinfelden Alloys GmbH & Co. KG Aluminiumlegierung
WO2010100204A1 (de) * 2009-03-06 2010-09-10 Rheinfelden Alloys Gmbh & Co. Kg Aluminiumlegierung
WO2010124835A1 (de) * 2009-04-28 2010-11-04 Belte Ag Aluminium-silizium-druckgusslegierung für dünnwandige strukturbauteile
EP2455505A1 (de) 2010-11-19 2012-05-23 Martinrea Honsel Germany GmbH Zylinderkopf für Verbrennungsmotoren aus einer Aluminiumlegierung
DE102010060670A1 (de) * 2010-11-19 2012-05-24 Martinrea Honsel Germany Gmbh Zylinderkopf für Verbrennungsmotoren aus einer Aluminiumlegierung
WO2012138767A2 (en) 2011-04-04 2012-10-11 Emerson Climate Technologies, Inc. Aluminum alloy compositions and methods for die-casting thereof
EP2694692A2 (de) * 2011-04-04 2014-02-12 Emerson Climate Technologies, Inc. Aluminiumlegierungszusammensetzungen und verfahren zu ihrer herstellung durch druckgiessen
EP2694692A4 (de) * 2011-04-04 2014-08-27 Emerson Climate Technologies Aluminiumlegierungszusammensetzungen und verfahren zu ihrer herstellung durch druckgiessen
US9038704B2 (en) 2011-04-04 2015-05-26 Emerson Climate Technologies, Inc. Aluminum alloy compositions and methods for die-casting thereof
EP2735621A1 (de) * 2012-11-21 2014-05-28 Georg Fischer Druckguss GmbH & Co. KG Aluminium-Druckgusslegierung
US9322086B2 (en) 2012-11-21 2016-04-26 Georg Fischer Druckguss Gmbh & Co Kg Aluminum pressure casting alloy
US11584977B2 (en) 2015-08-13 2023-02-21 Alcoa Usa Corp. 3XX aluminum casting alloys, and methods for making the same

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JP4007488B2 (ja) 2007-11-14
EP1331281B1 (de) 2005-05-18
DE60300659T2 (de) 2005-11-17
JP2003213354A (ja) 2003-07-30
DE60300659D1 (de) 2005-06-23
US20030136477A1 (en) 2003-07-24

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