WO2015173237A1 - Alliage - Google Patents

Alliage Download PDF

Info

Publication number
WO2015173237A1
WO2015173237A1 PCT/EP2015/060467 EP2015060467W WO2015173237A1 WO 2015173237 A1 WO2015173237 A1 WO 2015173237A1 EP 2015060467 W EP2015060467 W EP 2015060467W WO 2015173237 A1 WO2015173237 A1 WO 2015173237A1
Authority
WO
WIPO (PCT)
Prior art keywords
silicon
aluminium
composition
iron
alloy
Prior art date
Application number
PCT/EP2015/060467
Other languages
English (en)
Inventor
Emeka IKWUEZE
Pete BLACKMORE
Ashley BROUGH
Simon RUFFLE
Wayne MURCOTT
Original Assignee
Jaguar Land Rover Limited
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 Jaguar Land Rover Limited filed Critical Jaguar Land Rover Limited
Priority to EP15723479.0A priority Critical patent/EP3143174A1/fr
Publication of WO2015173237A1 publication Critical patent/WO2015173237A1/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • 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

Definitions

  • the invention relates to aluminium-silicon alloys for use in die casting of structural components.
  • the invention further relates to methods of making and using such alloys.
  • Aluminium alloys are used in the production of high pressure die castings for structural body parts used in the manufacture of motor vehicles and other heavy machinery. Aluminium is favoured for the production of such components due to its ease of handling, its low cost, ease of machinability and because it is relatively lightweight. Die castings typically comprise complex geometry including parts that may require welding or riveting to other structural components. As a result, structural die castings will be subjected to considerable loads when in use, particularly if they contribute to the chassis, powertrain, subframe or suspension system of a motor vehicle.
  • aluminium-silicon eutectic system alloys are favoured for the purposes of die castings.
  • aluminium-silicon alloys used in motor vehicle castings consist of a major component of aluminium, between 8 and 10 wt% silicon as well as minor amounts (between 0.1 wt% and 1 wt%) of additional grain refining and strengthening additive elements such as copper, zinc, manganese, magnesium, strontium and titanium.
  • iron represents an impurity due to the fact that it forms inter- metallics within the microstructure of the alloy that can lead to weakening, increased vulnerability to fatigue and reduced ductility. It is preferred, therefore, that the iron content in aluminium-silicon alloys is maintained at a level that is below 0.15 wt%, and preferably even lower. Consequently, such requirements discourage the use of recycled materials as a source of aluminium for die castings, so-called secondary alloys, because the levels of contaminating iron are simply too high.
  • the present invention provides alloy compositions that meet the aforementioned objectives.
  • the present invention relates to alternative compositions and processes for manufacturing an aluminium alloy that exhibits satisfactory mechanical and material properties such that it can be used in die castings for automotive and aerospace
  • a first aspect of the invention provides an aluminium-silicon alloy composition comprising:
  • the aluminium is derived from secondary sources, and therefore comprises a substantial proportion of recycled aluminium-containing material.
  • the aluminium-silicon alloy of the invention comprises at least 8.5 wt% silicon, optionally about 9 wt% silicon, more optionally around 10 wt % silicon.
  • the aluminium-silicon alloy of the invention will comprise less than 1 1 wt % silicon and optionally no more than 10.5 wt% silicon.
  • the aluminium-silicon alloy may comprise at least 0.01 wt% iron, however typically it is expected that the baseline iron content is likely to be in the region of at least 0.10 wt% and more typically at least 0.15 wt%. In specific embodiments of the invention the aluminium-silicon alloy comprises not less than 0.16 wt% iron.
  • the aluminium-silicon alloy of the invention further comprises manganese in an amount defined by a ratio that is dependent upon the iron content of the aluminium source. Hence the amount of manganese may vary from composition to composition but is within boundaries set by the invention.
  • the amount of manganese is always greater than the amount of iron and in specific embodiments of the invention the ratio of iron to manganese is at least about 0.2 and at most about 0.8. In specific embodiments of the invention the iron to manganese ratio is at least 0.3, suitably at least 0.4, optionally 0.5 and up to around 0.75.
  • the iron to manganese ratio is set at a level to ensure that majority of iron-containing intermetallic phase particles assume a polyhedral morphology within the microstructure of the alloy.
  • the aluminium-silicon alloy comprises less than 0.1 wt% of magnesium and/or is substantially free of elements such as: molybdenum and zirconium.
  • the composition is heat treated (i.e. annealed).
  • heat treatment occurs at a temperature of at least around 350 ⁇ €, optionally at least around 360 °C, suitably up to around 390 °C.
  • heat treatment occurs at a temperature of up to at most around 385 °C.
  • a second aspect of the invention provides for a method of manufacturing an aluminium-silicon alloy composition that is suitable for use in automotive and aeronautical castings.
  • the method comprises adding to a source of aluminium that comprises at least 0.16 wt% iron, the following elements selected from:
  • the method comprises the additional step of forming the alloy into a die casting and heat treating the die casting.
  • a third aspect of the invention provides for a die casting manufactured from the alloys of the present invention.
  • the casting is for use in the automotive industry.
  • the die casting may constitute a part or component that is comprised within the body, chassis, powertrain, sub-frame or suspension system of a motor vehicle.
  • a fourth aspect of the invention provides for a method of die casting a component comprising, forming a die mould that defines the configuration of the component, injecting the molten aluminium-silicon alloy of the invention into the die mould and allowing the alloy to cool to form a solid die cast component.
  • the component may be subjected to additional heat treatment as described herein.
  • a fifth aspect of the invention provides a motor vehicle that comprises a part that includes or is comprised of a part or component manufactured from an aluminium-silicon alloy of the invention.
  • a sixth aspect of the invention provides for a use of an aluminium-silicon alloy comprising an iron content of at least 0.16 wt% for manufacturing a die casting for a body in white (BiW) component of a motor vehicle.
  • the aluminium-silicon alloy comprises at least 0.16 wt% iron and at most around 0.30 wt %.
  • the aluminium-silicon alloy comprises at least 0.30 wt% iron.
  • the use of the alloy contributes to a casting may be a part or component that is comprised within the body, chassis, powertrain, sub- frame or suspension system of a motor vehicle.
  • the die castings are suitable for use as components of Body in White (BiW) body panels and sub-assemblies.
  • a seventh aspect of the invention provides an aluminium-silicon alloy composition, for use in die casting, comprising at least 8 wt% and at most 1 1 wt % silicon, optionally no more than 10.5 wt% silicon, up to around 0.30 wt% iron, and manganese, wherein the amount of manganese present in the composition is greater than the amount of iron, wherein the balance of the composition comprises aluminium.
  • Embodiments in accordance with the aforementioned aspect are particularly useful for use in high pressure die casting of automotive components and, in a particular, structural components e.g. engine mount brackets.
  • the composition is heat treated (i.e. annealed).
  • a post casting heat treatment is particularly beneficial for the manufacture of Body in White (BiW) structural components, which may include, for example, shock absorber towers.
  • heat treatment occurs at a temperature of at least around 350 °C, optionally at least around 360 °C, suitably up to around 390 °C.
  • heat treatment occurs at a temperature of up to at most around 385 °C.
  • Figure 1 is a micrograph showing a section through a conventional Al-Si alloy that comprises iron inclusions, intermetallic phase particles, as impurities.
  • An iron inclusion that has adopted a 'script' configuration is marked as (A), whereas (B) denotes a particle that has adopted a more regular polyhedral shape.
  • FIG. 2 micrographs of showing sections through three Al-Si alloys of embodiments of the invention having increasing levels of iron content, the three alloys are denoted as Low Fe (0.16 wt%), Medium Fe (0.31 wt%), and High Fe (0.55 wt%).
  • a comparative conventional low iron content Al-Si alloy is also shown (denoted Comp).
  • Figure 3 shows an analysis of variation box plot of a proof stress test for Al-Si parts treated at the three different annealing temperatures (350 °C, 365 °C and 385 °C) as well as for a non-heat treated control (denoted AC for "as cast”).
  • Figure 4 shows an analysis of variation box plot of an elongation test for Al-Si parts treated at the three different annealing temperatures (350 °C, 365 °C and 385 °C) as well as for a non-heat treated control (denoted AC for "as cast”).
  • Figure 5 shows a scatter plot of the data from Figures 3 and 4 for the AC (diamond shaped points) and 385C alloys (square points) overlaid against results obtained for control parts manufactured from a conventional primary aluminium Al-Si alloy (Comparison) which is heat treated.
  • Figure 6 is a graph showing the results of a Coupon Test in which strain-life versus fatigue damage values for the control alloy (Comparison) are overlaid with results obtained from 385 °C heat treated Al-Si alloy of an embodiment of the invention (denoted "HT combined") and non-heat treated alloy embodiment (denoted "as cast”).
  • Figure 7 is a graph of Coupon Testing showing the results of cyclic strain versus cyclic stress in Al-Si alloys of the embodiments of the invention shown in Figure 6.
  • Figure 8 is a graph of the results of a tensile strength test on multiple samples of parts manufactured from control alloy (Comparison), 385 °C heat treated alloy of an embodiment of the invention (denoted Rivalloy HT) and non-heat treated alloy of an embodiment of the invention (denoted Rivalloy AC).
  • alloy is used herein to denote a metallic substance comprising a mixture of a predominating metallic element and other elements, including impurities.
  • the basic aluminium-silicon (Al-Si) alloy forms a simple eutectic system at around 12 weight% (wt%) silicon being the eutectic composition at 577 °C.
  • Al-Si alloys are usually referred to as near- eutectic alloys when silicon content is around about 10% and up to about 13% of the total weight of the alloys.
  • Eutectic (or near-eutectic) Al-Si alloys are used extensively in die casting applications particularly in the automotive and aerospace industries.
  • Al-Si alloys used in casting may contain 50-90 vol% eutectic.
  • Conventional Al-Si alloys suitable for use in die casting applications typically meet industry standards such as European Standard EN 1676 which defines the requirements for various grades of alloyed aluminium ingots intended for remelting. It is believed that the alloys of the present invention show high levels of equivalence in terms of suitability for use in die casting, especially for automotive and aerospace parts.
  • Die casting is a manufacturing process that can produce metal components through the use of reusable molds, called dies.
  • the die casting process involves a furnace, metal, die casting machine, and die.
  • the metal typically a non-ferrous alloy comprising aluminium, is first melted in the furnace and then injected, optionally under pressure, into the dies in the die casting machine. Once the casting has cooled and has set the part can be subjected to additional tooling or trimmed and finished.
  • Die casting processes can produce large and small component parts, with geometrically complex shapes.
  • the cast parts are typically of high strength and can be subjected to considerable loads when in use. The process supports a reasonably high rate of production and is favoured producing consistent parts with good surface finish.
  • components manufactured via die casting processes of the present invention are also referred to as parts and broadly refer to any metal object manufactured via the die casting process.
  • the parts are often comprised of geometrically complex shapes that perform a defined function.
  • Components manufactured according to the present invention are particularly suitable for use in motor vehicles and aircraft.
  • impurity refers to a metallic or non-metallic element that is present in an alloy but which is not added intentionally. Hence, no lower limit is specified for the presence of the impurity.
  • iron Fe
  • crystalline "inclusions" intermetallic phase particles, or crystalline "inclusions" within the microstructure of the alloy.
  • Iron is a common impurity in aluminium alloys that arises from a number of possible sources and which, at least for Al-Si based casting alloys, is usually considered detrimental for several reasons.
  • primary low values of between 0.10 and 0.15 wt% are the typical baseline levels found in primary pure aluminium and all further melt activities only serve to potentially increase the iron level further.
  • Intermetallic phase particles that adopt the script morphology are the most detrimental to the properties of the alloy contributing to the fracture mechanism and also bringing about an increase in porosity.
  • the microstructure of a solid alloy takes form when a metal cools from molten liquid phase to a solid metal. This solidification forms a polycrystalline metal with different orientations of the grains. These grains will form the microstructure of the alloy and will contribute to its material properties including strength, resistance to fatigue and ductility. The form of this microstructure depends not only upon the heat transfer but also upon the alloy composition.
  • the two major growth types of microstructures include the dendritic and the eutectic. Both types of growth are present in almost every aluminium alloy casting because of the improved castability of a near-eutectic or eutectic alloy than that of other compositions.
  • Al-Si alloys typically used in die casting applications will usually comprise a two-phase microstructure.
  • the alloy comprises larger grains (known as dendrites) that are predominantly comprised of aluminium with a small silicon component.
  • dendrites larger grains
  • the eutectic phase will begin to solidify between the dendrite arms filling this volume out.
  • the eutectic phase consists of a primary a- aluminium phase and a silicon phase. This will give a two-phase microstructure where the primary a-aluminium crystals (dendrites) are distributed within the Al-Si eutectic phase. The ratio between the two phases will depend on the content of silicon and also the solidification time.
  • Figure 1 shows a typical two-phase microstructure of a conventional Al-Si alloy.
  • an Al-Si alloy composition that is suitable for use in manufacture of die casting parts that tolerates an impurity content that is substantially elevated compared to that hitherto considered viable.
  • an iron content of up to around 0.30 wt% of the alloy can be tolerated without a substantial effect upon the mechanical strength or ductility of the alloy that would compromise its ability to be used in die casting.
  • the present alloys do not require the presence of costly grain refining elements such as molybdenum or zirconium. This means that the alloys of the present invention may be manufactured using secondary sources of aluminium (including recycled material) that results in a significant reduction in cost and carbon footprint.
  • the ability to utilise recycled starting materials also enables the alloy to be produced from local sources of aluminium.
  • the effect of this is to reduce the considerable distances needed to transport high grade primary aluminium alloy from the foundry to the manufacturing site. This results in a significant reduction in the carbon footprint for the alloys of the present invention.
  • the energy savings made in recycling aluminium are considerable. Remelting requires only about 5 % of the energy initially required to produce primary aluminium. In an embodiment of the invention, it is estimated that the current process reduces the amount of C0 2 emitted by over 9 tonnes per tonne of metal alloy produced when compared to conventional primary Al-Si alloys.
  • alloys of the invention may suitably comprise anything up to about
  • the minimum content of silicon in the alloy will be at least 7 wt%, more suitably at least around 8 wt %, optionally at least about 9 wt%.
  • the alloys of the invention do not require the presence of additional grain refining elements such as zirconium and molybdenum, or iron neutralising elements such as beryllium, cobalt and chromium. Hence, the alloys of the invention provide a saving in terms of cost and ease of manufacture.
  • a specific embodiment of the invention provides for an Al-Si alloy in which the iron to manganese ratio is maintained at a level of at least 0.20 and optionally up to around 0.80. This is considerably higher than previously known, where iron is usually the more abundant component with ratio maintained at around 2.0 in order to prevent the formation of hard spots in the die casting which can hinder subsequent machining of the parts.
  • iron impurity levels can be tolerated that are double those typically found in Al-Si alloys made from primary sources of aluminium.
  • the present inventors have not observed any reduction in the handling or working-ability of parts and components manufactured from the novel Al-Si alloys.
  • Example 1 Qualitative analysis of alloys comprising increasing iron content
  • Three Al-Si alloys were prepared with increasing levels of iron (Fe) as an impurity.
  • the three alloys were denoted as Low Fe (0.16wt%), Medium Fe (0.31wt%), and High Fe (0.55wt%).
  • the manganese content was adjusted to maintain a greater proportion of manganese to iron.
  • Figure 2 to determine the number and size distribution of intermetallic phase particles of (FeMn) 3 Si 2 Ali 5 .
  • the sizes of these particles fell into two main bands: large (15-24 ⁇ in diameter) and small (approximately 3 ⁇ in diameter).
  • the large particles had most probably nucleated in the liquid alloy prior to casting which had allowed agglomerations to form.
  • the small particles conversely, had precipitated during investment of the castings and, thus, had little time to grow or agglomerate.
  • a comparison was made against a conventional die- casting Al-Si alloy made from low iron content primary aluminium (Comparison).
  • Example 2 Effects of heat treatment on parts made from Al-Si alloys of the invention
  • FIG. 1 An Al-Si alloy of the invention having a composition substantially as set out in Table 1 was used to form die casting parts.
  • the parts were subjected to annealing temperatures of 350 °C, 365 °C and 385 °C for a period of 25 minutes before being tested for mechanical properties.
  • Figure 3 shows an analysis of variation box plot displaying the results of a yield test with results presented as box plot of 0.2% proof stress for parts treated at the three different annealing temperatures as well as for a non-heat treated control (denoted AC).
  • the yield test provides an estimation of the performance of the alloy under load and particularly the minimum stress required to cause a 0.2% permanent plastic deformation of the die casting part.
  • Figure 4 shows an analysis of variation box plot of the results of a tensile test according to ASTM E8M-09 in which measurements are made of the extension of the test part under increasing load.
  • the results of the tests presented in Figures 3 and 4 show that whilst mechanical strength reduces somewhat upon heat treatment the ductility increases.
  • BiW Body in White
  • the die cast parts manufactured from Al-Si alloys of the invention whether heat treated or not have mechanical properties that are highly comparable to known Al-Si alloys that are manufactured from primary sources of aluminium and which comprise low levels of iron impurities.
  • Figure 5 shows a scatterplot of elongation versus yield (0.2% proof stress) in which values for the control alloy (Comparison) are overlaid with results obtained from 385 °C heat treated alloy of the invention (denoted Rivalloy annealed) and non-heat treated alloy of the invention (denoted Rivalloy as cast). It is apparent from Figure 5 that the mechanical performance of both the annealed and non-heat treated die cast alloys of the invention are highly comparable to that of the control.
  • FIG. 6 shows the results of a conventional Coupon Test. This procedure describes a method for performing strain-controlled, axial fatigue testing on specimens with the aim of producing the data necessary for the generation of the characteristic strain-life fatigue properties of metallic materials. The testing method, based upon guidance contained within standards BS 7270, ASTM E 606 and ISO 12106, and is restricted to uniaxially loaded, parallel section samples tested at ambient temperature in laboratory air.
  • An 8 mm gauge length extensometer was used.
  • the calibration procedure of the test equipment is fully in line with BS EN ISO 9513:2002.
  • the frequency used is 1 Hz as maximum, and 10% of load drop was defined as the crack initiation life.
  • the results are presented as strain versus life with 99.9% survival probability in which values for the control alloy (Comparison) are overlaid with results obtained from all heat treated variants of the invention (denoted HT combined).
  • alloys of the invention are characterised by the finding iron content has no effect on fatigue, all the heat treated versions were assessed as a single population.
  • Non- heat treated alloy of the invention (denoted "as cast”).
  • the performance of the Al-Si alloys of the invention is broadly similar to that of the low iron control, with the heat treated alloy having a near identical response to fatigue in spite of the significantly higher (almost twofold) iron content.
  • Figure 7 shows the results of Coupon Testing showing the results of cyclic strain versus cyclic stress. The results show that the fatigue profile of annealed Al-Si alloy of the invention is highly comparable to that of the heat treated low iron control.
  • the die cast parts manufactured from Al-Si alloys of the invention whether heat treated or not have comparable static strength properties when compared to the known Al-Si alloys that are manufactured from low iron content primary sources of aluminium.
  • Figure 8 shows the results of a tensile strength rig test under constant load. Multiple samples of parts manufactured from control alloy (Comparison), 385 °C heat treated alloy of the invention (denoted Rivalloy HT) and non-heat treated alloy of the invention (denoted Rivalloy AC) were tested. All parts successfully passed the 120 kN target threshold prior to fracture.
  • the performance of the Al-Si alloys of the invention is broadly similar to that of the low iron control (Comparison), with the heat treated alloy (Rivalloy HT) having a near identical response to fatigue in spite of the significantly higher iron content.
  • the present invention extends to the following aspects as detailed in the following numbered paragraphs (clauses):
  • An aluminium-silicon alloy composition comprising:
  • composition comprises manganese in an amount that is greater than the amount of iron present in the composition; wherein the balance of the composition comprises aluminium.
  • composition of clause 1 wherein the aluminium comprises a proportion of recycled material.
  • the aluminium-silicon alloy comprises at least 8.5 wt% silicon, optionally about 9 wt% silicon, more optionally around 10 wt % silicon.
  • composition of clause 3 wherein the aluminium-silicon alloy comprises less than 1 1 wt % silicon and optionally no more than 10.5 wt% silicon. 5. The composition of clause 1 , wherein the aluminium-silicon comprises at least 0.16 wt% iron.
  • composition of any previous clause, wherein the amount of manganese in the composition is determined by an iron to manganese ratio of at least about 0.2 and at most about 0.8.
  • composition of clause 7, wherein the ratio of iron to manganese is at least 0.3, suitably at least 0.4, optionally 0.5, and up to 0.75.
  • composition of any previous clause wherein the aluminium-silicon alloy comprises less than 0.1 wt% of magnesium and/or is substantially free of elements such as: molybdenum and zirconium. 1 1 .
  • composition of any previous clause wherein the composition is heat treated.
  • composition of clause 1 1 wherein the heat treatment occurs at a temperature of at least around 350 °C, optionally at least around 360 °C, suitably up to around 390 °C.
  • a method of manufacturing an aluminium-silicon alloy composition that is suitable for use in automotive and aeronautical castings, the method comprising adding to a source of aluminium that comprises at least 0.16 wt% iron, the following elements selected from:
  • a motor vehicle that comprises a part that includes or is comprised of a part or component manufactured from an aluminium-silicon alloy of any of clauses 1 to 13.
  • 27. Use of an aluminium-silicon alloy comprising an iron content of at least 0.16 wt% and a manganese content that is greater than the amount of iron present in the composition, for manufacturing a die cast part for a motor vehicle.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Vehicle Body Suspensions (AREA)

Abstract

L'invention concerne un alliage d'aluminium et de silicium approprié pour être utilisé dans des pièces coulées sous pression pour l'automobile ou l'aérospatial. L'alliage comprend au moins 8 % en poids et au maximum 12 % en poids de silicium; jusqu'à environ 0,30 % en poids de fer; et du manganèse, la composition comprenant du manganèse en une quantité qui est supérieure à la quantité de fer présent dans la composition; et le reste de la composition comprenant de l'aluminium. L'invention concerne également des procédés de fabrication de l'alliage et pour la fabrication de pièces coulées sous pression.
PCT/EP2015/060467 2014-05-12 2015-05-12 Alliage WO2015173237A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP15723479.0A EP3143174A1 (fr) 2014-05-12 2015-05-12 Alliage

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
GB1408299.4A GB2526085A (en) 2014-05-12 2014-05-12 An alloy
GB1408299.4 2014-05-12

Publications (1)

Publication Number Publication Date
WO2015173237A1 true WO2015173237A1 (fr) 2015-11-19

Family

ID=51032549

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2015/060467 WO2015173237A1 (fr) 2014-05-12 2015-05-12 Alliage

Country Status (3)

Country Link
EP (1) EP3143174A1 (fr)
GB (1) GB2526085A (fr)
WO (1) WO2015173237A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112522648A (zh) * 2020-12-29 2021-03-19 重庆慧鼎华创信息科技有限公司 一种提高压铸铝合金导热率的工艺方法
CN113909448A (zh) * 2021-10-09 2022-01-11 润星泰(常州)技术有限公司 新能源车铆接用铝合金压铸件制备方法及压铸件

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3184659A1 (fr) * 2015-12-23 2017-06-28 Wifama-Prexer Sp. z o.o. Silumine pour moulage sous pression, avec un additif de tungstène et de vanadium
CN113423853B (zh) * 2019-02-08 2022-11-15 麦格纳国际公司 用于结构高压真空压铸应用的铝合金

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08282295A (ja) * 1995-01-19 1996-10-29 Nippon Light Metal Co Ltd ダイカスト製ドアパネル及びその製造方法
JPH093610A (ja) * 1995-06-15 1997-01-07 Nippon Light Metal Co Ltd 寸法精度及び延性に優れた薄肉アルミダイカスト製品及び製造方法
GB2421735A (en) * 2004-12-28 2006-07-05 Denso Corp Aluminium-silicon casting alloy

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH01218795A (ja) * 1988-02-29 1989-08-31 Mitsubishi Alum Co Ltd フイレット強度の高いＡｌ合金ろう材
US20060177688A1 (en) * 2005-02-04 2006-08-10 Corus Aluminium Walzprodukte Gmbh Aluminium alloy brazing material
DE102009019269A1 (de) * 2009-04-28 2010-11-11 Audi Ag Aluminium-Silizium-Druckgusslegierung für dünnwändige Strukturbauteile

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08282295A (ja) * 1995-01-19 1996-10-29 Nippon Light Metal Co Ltd ダイカスト製ドアパネル及びその製造方法
JPH093610A (ja) * 1995-06-15 1997-01-07 Nippon Light Metal Co Ltd 寸法精度及び延性に優れた薄肉アルミダイカスト製品及び製造方法
GB2421735A (en) * 2004-12-28 2006-07-05 Denso Corp Aluminium-silicon casting alloy

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
KOCH HUBERT ET AL: "Ductile high-pressure die casting alloy with low iron content", GIESSEREI, GIESSEREI VERLAG, DUSSELDORF, DE, vol. 82, no. 15, 31 July 1995 (1995-07-31), pages 517 - 523, XP009099456, ISSN: 0016-9765 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112522648A (zh) * 2020-12-29 2021-03-19 重庆慧鼎华创信息科技有限公司 一种提高压铸铝合金导热率的工艺方法
CN113909448A (zh) * 2021-10-09 2022-01-11 润星泰(常州)技术有限公司 新能源车铆接用铝合金压铸件制备方法及压铸件

Also Published As

Publication number Publication date
EP3143174A1 (fr) 2017-03-22
GB201408299D0 (en) 2014-06-25
GB2526085A (en) 2015-11-18

Similar Documents

Publication Publication Date Title
US7108042B2 (en) Aluminum diecasting alloy
JP6090725B2 (ja) アルミニウム合金製塑性加工品の製造方法
US9322086B2 (en) Aluminum pressure casting alloy
US11286542B2 (en) Aluminum alloy for die casting and functional component using the same
US6767506B2 (en) High temperature resistant magnesium alloys
KR101971846B1 (ko) 다이 캐스팅 합금
CN106661682B (zh) 用于压铸的抗蠕变、可延展的镁合金
US20180010214A1 (en) High strength high creep-resistant cast aluminum alloys and hpdc engine blocks
US20120087826A1 (en) High strength aluminum casting alloy
JP6229130B2 (ja) 鋳造用アルミニウム合金及びそれを用いた鋳物
EP3143174A1 (fr) Alliage
Afshari et al. Effects of pre-deformation on microstructure and tensile properties of Al—Zn—Mg—Cu alloy produced by modified strain induced melt activation
JP4801386B2 (ja) アルミ合金製塑性加工品、その製造方法、自動車用部品、時効処理炉、およびアルミ合金製塑性加工品の製造システム
Wang et al. Influence of heat treatment on microstructures and mechanical properties of gravity cast Mg–4.2 Zn–1.5 RE–0.7 Zr magnesium alloy
Kliauga et al. The influence of impurity level and tin addition on the ageing heat treatment of the 356 class alloy
WO2018161311A1 (fr) Alliages d'aluminium
Kilicli et al. Tensile fracture behavior of AA7075 alloy produced by thixocasting
JP2004292937A (ja) 輸送機構造材用アルミニウム合金鍛造材およびその製造方法
JP5275321B2 (ja) アルミ合金製塑性加工品の製造方法
US7547411B2 (en) Creep-resistant magnesium alloy for casting
JP5532462B2 (ja) アルミ合金製塑性加工品の製造方法
JP2008025003A (ja) 鋳造用アルミニウム合金および同アルミニウム合金鋳物
JP7467633B2 (ja) 粉末アルミニウム材料
Nafari et al. Microstructure and mechanical properties of the Mg–Zn–Cu/SiCp composite in the as-cast and as-extruded conditions
Trudonoshyn et al. Design of a new casting alloys containing Li or Ti+ Zr and optimization of its heat treatment

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 15723479

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

REEP Request for entry into the european phase

Ref document number: 2015723479

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2015723479

Country of ref document: EP