EP2135965A1 - Hitzebeständige magnesiumlegierung - Google Patents

Hitzebeständige magnesiumlegierung Download PDF

Info

Publication number
EP2135965A1
EP2135965A1 EP08710964A EP08710964A EP2135965A1 EP 2135965 A1 EP2135965 A1 EP 2135965A1 EP 08710964 A EP08710964 A EP 08710964A EP 08710964 A EP08710964 A EP 08710964A EP 2135965 A1 EP2135965 A1 EP 2135965A1
Authority
EP
European Patent Office
Prior art keywords
magnesium alloy
heat
alloying element
crystalline
crystalline grains
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.)
Withdrawn
Application number
EP08710964A
Other languages
English (en)
French (fr)
Other versions
EP2135965A4 (de
Inventor
Tsukasa Sugie
Kyoichi Kinoshita
Motoharu Tanizawa
Manabu Miyoshi
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.)
Toyota Industries Corp
Original Assignee
Toyota Industries Corp
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 Toyota Industries Corp filed Critical Toyota Industries Corp
Publication of EP2135965A1 publication Critical patent/EP2135965A1/de
Publication of EP2135965A4 publication Critical patent/EP2135965A4/de
Withdrawn legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent

Definitions

  • the present invention is one which relates to a heat-resistant magnesium alloy that are capable of withstanding services under high loads and at high temperatures.
  • Magnesium alloy which is much more light weight than aluminum alloy is, is about to come to be used widely for aircraft material, vehicle material, and the like, from the viewpoint of weight saving.
  • magnesium alloy since the strength and heat resistance are not sufficient depending on applications, further improvement of the characteristics has been sought.
  • the metallic structure of alloy affects its characteristics greatly. Accordingly, in order to obtain a magnesium alloy that possesses strength and creep resistance being sufficient for services at high temperatures, it is necessary to adapt the types and amounts of additive elements into adequate ones in order to control the metallic structure.
  • a heat-resistant magnesium alloy according to the present invention is characterized in that it includes:
  • the "networks that are continuous microscopically” take on network structures (three-dimensionally mesh structures) macroscopically, and are states in which crystals exist continuously even inside the networks (see Fig. 2 ). Therefore, the following are not involved: discontinuous states whose interior is constituted of small crystals, even though they take on network structures (see Fig. 3 ).
  • the heat-resistant magnesium alloy according to the present invention includes the second alloying element "M2, " it has the plate-shaped precipitated substances within the grains of the Mg crystalline grains, and the grain-boundary crystallized substances, which form the networks that are continuous microscopically, at the grain boundaries, as will be detailed later. Since the plate-shaped precipitated substances exist within the Mg crystalline grains, the movements of dislocation within the Mg crystalline grains are prevented, and accordingly it becomes less likely to deform. Moreover, since the grain-boundary crystallized substances, which form the networks, are present continuously microscopically at the grain boundaries between the Mg crystalline grains, the strength at the grain boundaries improves.
  • the heat-resistant magnesium alloy according to the present invention exhibits high mechanical characteristics even in high-temperature regions. That is, in the magnesium alloy according to the present invention, the mechanical characteristics in high-temperature regions are improved by strengthening it not only within the Mg crystalline grains' granular interior but also at the grain boundaries between the Mg crystalline grains.
  • Said precipitated substances can desirably comprise a Laves-phase compound with type-"C15" crystalline structure. Moreover, said precipitated substances can desirably be precipitated parallel to the ⁇ 001 ⁇ plane of Mg crystal.
  • Said grain-boundary crystallized substances which form the networks that are continuous microscopically, can desirably comprise an Mg-"M1"-Ca-system compound.
  • said grain-boundary crystallized substances can desirably comprise a mixed-crystal phase of a Laves-phase compound with type-"C14" crystalline structure and a Laves-phase compound with type-"C36" crystalline structure; on this occasion, it is allowable that said mixed-crystal structure can include the type-"C14" crystalline structure more than the type-"C36" crystalline structure.
  • the grain-boundary crystallized substances comprise a mixed-crystal phase of a Laves-phase compound with type-"C14" crystalline structure and a Laves-phase compound with type-"C36" crystalline structure, compounds, which constitute the networks, do not undergo any phase separation, and consequently turn into single crystals virtually in appearance (see Fig. 4 ), the area of the crystalline-grain boundaries between crystalline grains that constitute the networks, and the number of the crystalline grains that constitute the networks become minimum.
  • the heat-resistant magnesium alloy according to the present invention can preferably include: Ca in an amount of from 2% by mass or more to 4% by mass or less; said first alloying element "M1” in an amount of from 0.9 or more to 1.1 or less by mass ratio with respect to Ca ("M1"/Ca); said second alloying element “M2” in an amount of from 0.3% by mass or more to 0.6% by mass or less; and the balance comprising Mg and inevitable impurities; when the entirety is taken as 100% by mass.
  • the heat-resistant magnesium alloy according to the present invention can preferably include: Ca in an amount of from 1.235 atomic % or more to 2.470 atomic % or less; said first alloying element "M1" in an amount of from 1.34 or more to 1.63 or less by atomic ratio with respect to Ca ("M1"/Ca); said second alloying element "M2" in an amount of from 0.13 atomic % or more to 0.27 atomic % or less; and the balance comprising Mg and inevitable impurities; when the entirety is taken as 100 atomic %.
  • Heat-resistance magnesium alloys which possess metallic structures that are desirable from the viewpoints of mechanical characteristics at high temperatures, are obtainable by setting the content proportions of the first alloying element, second alloying element and Ca that the heat-resistance magnesium alloy according to the present invention contains to appropriate ranges.
  • heat resistance being referred to in the present specification is one that is evaluated by mechanical properties of magnesium alloy in high-temperature atmospheres (creep characteristics or high-temperature strengths that are determined by means of stress relaxation tests or axial-force retention tests, for instance).
  • Fig. 1 is a metallic-structure photograph in which a cross section of a test specimen being labeled #01 was observed with a metallographic microscope.
  • Fig. 2 is a metallic-structure photograph in which an observational sample being labeled #01 was observed with a transmission electron microscope (or TEM).
  • Fig. 3 is a metallic-structure photograph in which an observational sample being labeled #C1 was observed with a TEM.
  • Fig. 4 is a dark-field scanning-transmission-electron-microscope (or DF-STEM) image on the observational sample being labeled #01.
  • Fig. 5 is a DF-STEM image on the observational sample being labeled #C1.
  • Fig. 6 is a TEM image on the observational sample being labeled #01, and an electron diffraction pattern thereof (the incident direction being ⁇ 110>).
  • Fig. 7 is another TEM image on the observational sample being labeled #01, and another electron diffraction pattern thereof (the incident direction being ⁇ 111>).
  • Fig. 8 is a TEM image on the observational sample being labeled #C1, and an electron diffraction pattern thereof (the incident direction being ⁇ 111>).
  • Fig. 9 is a DF-STEM image in which the interior of Mg crystalline grains in the observational sample being labeled #01 was observed.
  • magnesium alloy thebestmode for carrying out the heat-resistant magnesium alloy according to the present invention
  • the magnesium alloy according to the present invention includes: magnesium (Mg), a major component; a first alloying element "M1”; a second alloying element “M2”; and calcium (Ca) ; and it has a metallic structure that includes: Mg crystalline grains; plate-shaped precipitated substances being precipitated within grains of Mg crystalline grains; and grain-boundary crystallized substances being crystallized at grain boundaries between the Mg crystalline grains to form networks that are continuous microscopically.
  • Mg magnesium
  • M1 first alloying element
  • M2 second alloying element
  • Ca calcium
  • the plate-shaped precipitated substances are present within the Mg crystalline grains.
  • the plate-shaped precipitated substances prevent the movements of dislocation within the Mg crystalline grains.
  • the deformations of crystal occur because the dislocation moves on sliding plane. Therefore, it is allowable that they can be plate-shaped precipitated substances that are parallel to the "c" plane of hexagonal Mg crystal, that is, to the ⁇ 001 ⁇ plane of Mg crystal.
  • the plate-shaped precipitated substances come to exhibit a plate thickness of 2-20 nm, and that the thicker the plate thickness is the more mechanical characteristics improve.
  • the plate-shaped precipitated substances can comprise a Laves-phase compound with type-"C15" crystalline structure.
  • the "c" plane of Mg crystal, and the ⁇ 111 ⁇ plane of "C15" structure are likely to form interfaces that are stable to each other crystallographically, and therefore it is possible to predict that the formation of the plate-shaped precipitated substances is facilitated.
  • compounds constituting the precipitated substances that have such crystalline structures can be "M1"-Ca-system compounds and/or Mg-"M1"-Ca-system compounds.
  • the magnesium alloy according to the present invention can have fine particles within the granular interior of the Mg crystalline grains.
  • the fine particles are present within the Mg crystalline grains, and most of them exist around the plate-shaped precipitated substances. It is believed that, although these fine particles are present within the Mg crystalline grains, they are not those which contribute to the improvement of strength inside the Mg crystalline grains. However, the presence of the fine particles is related to the generation of the precipitated substances (will be described later), and the fine particles are fine particles, which include "M2,” like "M1"-"M2"-system compounds, for instance. Note that the fine particles are sphere-shaped ones substantially and exhibit particle diameters of 10-15 nm approximately.
  • the grain-boundary crystallized substances which form networks that are continuous microscopically, are crystallized at the grain boundaries between the Mg crystalline grains to be present therein.
  • grain-boundary crystallized substances might be crystallized at the grain boundaries between the Mg crystalline grains, and additionally might form networks.
  • magnesium alloys that do not include any "M2” it has been understood that no microscopic continuity can be seen in the grain-boundary crystallized substances that form the networks.
  • the grain-boundary crystallized substances form the networks that are continuous microscopically. Because of the fact that the networks are continuous microscopically, the crystalline grain-boundary area of compounds that constitute the networks, and the number of crystalline grains are reduced greatly. As a result, the grain-boundary strength is improved, and is then strengthened. On this occasion, it is desirable that the networks of the grain-boundary crystallized substances can cover 70% or more of the grain boundaries between the Mg crystalline grains that are observed linearly in a regional cross section with 400 ⁇ m ⁇ 600 ⁇ m approximately in the magnesium alloy (this value will be abbreviated to as a "covering ratio of networks").
  • the grain-boundary crystallized substances can comprise a mixed-crystal phase of a Laves-phase compound with type-"C14" crystalline structure and a Laves-phase compound with type-"C36" crystalline structure.
  • the type-"C14" crystalline structure, and the type-"C36" crystalline structure are desirable, because they are hexagonal ones to each other and are likely to form mixed-phases.
  • the grain-boundary crystallized substances are continuous microscopically; and accordingly the crystalline-grain boundary area of crystalline grains, that is, compounds that constitute the networks, and the number of the crystalline grains that constitute the networks become minimum.
  • the grain-boundary crystallized substances can comprise an Mg-"M1"-Ca-system compound. Since Mg 2 Ca has a type-"C14" crystalline structure, it is assumed that a mixed-crystal phase of a type-"C14" crystalline structure and a type-"C36" crystalline structure is formed by solidifying "M1" into Mg 2 Ca. In this instance, it is allowable that the mixed-crystal phase can include the type-"C14" crystalline structure more than the type-"C36" crystalline structure.
  • the magnesium alloy according to the present invention that has the metallic structure as described above includes: magnesium (Mg), a major component; a first alloying element "M1"; a second alloying element “M2”; and calcium (Ca).
  • the first alloying element "M1” it is possible to use at least one member that is selected from the group consisting of aluminum (Al) and nickel (Ni). Although not only Al but also Ni are elements that react with Ca to form compounds and take on a type-"C15" Laves structure, a mixed-crystal phase of a type-"C14" Laves structure and a type-"C36" Laves structure is formed under such a condition that Mg 2 Ca, which takes on a type-"C14" Laves structure, is dominant, because Al and/or Ni are dissolved into Mg 2 Ca.
  • Al aluminum
  • Ni nickel
  • the second alloying element "M2” it is possible to use at least one member that is selected from the group consisting of manganese (Mn), barium (Ba), chromium (Cr) and iron (Fe).
  • Mn manganese
  • Ba barium
  • Cr chromium
  • Fe iron
  • the magnesium alloy according to the present invention includes at least one species of the aforementioned first alloying elements and second alloying elements, respectively. It is also allowable that it can include one species of them as for the first element and second element, respectively; and it is even allowable that it can include plural species of them as for either one of them or both of them.
  • the magnesium alloy according to the present invention can include: Ca in an amount of from 2% by mass or more to 4% by mass or less; said first alloying element "M1” in an amount of from 0.9 or more to 1. 1 or less by mass ratio with respect to Ca ("M1"/Ca); said second alloying element “M2” in an amount of from 0.3% by mass or more to 0.6% by mass or less; and the balance comprising Mg and inevitable impurities; when the entirety is taken as 100% by mass.
  • the magnesium alloy according to the present invention can include: Ca in an amount of from 1.235 atomic % or more to 2.470 atomic % or less; said first alloying element "M1" in an amount of from 1.34 or more to 1.63 or less by atomic ratio with respect to Ca ("M1"/Ca); said second alloying element "M2" in an amount of from 0.13 atomic % or more to 0.27 atomic % or less; and the balance comprising Mg and inevitable impurities; when the entirety is taken as 100 atomic %.
  • type-"C36" crystalline structure when type-"C36" crystalline structure is exposed to high temperatures, it is likely to undergo phase transition to type-"C15" crystalline structure ( Scripta Materialia 51 (2004) 1005-1010 ). Since the type-"C15" crystalline structure is likely to undergo massive agglomeration in high-temperature regions, and since it does not form the networks of the crystallized substances, networks which are continuous microscopically, the mechanical characteristics at high temperatures lower remarkably.
  • a more preferable "M1"/Ca value can be from 0.95 or more to 1.05 or less (namely, being 1.42-1.56 by atomic ratio).
  • the lower limit of a more preferable content proportion of "M2" can be 0.34% by mass (namely, 0.15 atomic %) or more.
  • the upper limit of a more preferable content proportion of "M2” can be 0.55% by mass (namely, 0.25 atomic %) or less, and can much more preferably be 0.5% by mass (namely, 0.23 atomic %) or less.
  • Ca is an element that forms type-"C14" and type-"C36" Laves structures together with Mg.
  • a content proportion of Ca is less than 2% by mass (namely, 1.235 atomic %), it is not preferable because the precipitated substances and grain-boundary crystallized substances are not generated sufficiently so that the effect of improving the heat-resistant characteristic is not sufficient.
  • the content proportion of Ca surpasses 4% by mass (namely, 2.470 atomic %), it is not preferable because the generation amounts of the precipitated substances and grain-boundary crystallized substances become too great so that problems might arise in post-processes.
  • a more preferable content proportion of Ca can be from 2.5% by mass or more to 3.5% by mass or less (namely, from 1.54 atomic % or more to 2.16 atomic % or less).
  • the magnesium alloy according to the present invention is not limited to those made by ordinary gravity casting and pressure casting, but can even be those made by die-cast casting. Moreover, even the casting mold being utilized for the casting does not matter if it is sand molds, metallic molds, and the like. Although even the solidification rate in the solidifying step is not limited in particular, it is allowable to let it stand to cool in air atmosphere.
  • the magnesium alloy according to the present invention can be utilized in products being utilized in high-temperature environments, such as engines, transmissions, compressors for air conditioner or their related products that are put in place within the engine room of automobile, for instance.
  • high-temperature environments such as engines, transmissions, compressors for air conditioner or their related products that are put in place within the engine room of automobile, for instance.
  • the following can be given: cylinder heads, cylinder blocks and oil pans of internal combustion engine; impellers for turbocharger of internal combustion engine, transmission cases being used for automobile and the like, and so forth.
  • a chloride-system flux was coated onto the inner surface of a crucible being made of iron that had been preheated within an electric furnace, and then a weighed pure magnesium base metal, pure Al, and an Mg-Mn alloy, if needed, were charged into it and were then melted. Further, weighed Ca was added into this molten metal that was held at 750 °C (i.e., a molten-metal preparing step).
  • test specimens with 30 mm ⁇ 300 mm ⁇ 40 mm were made by means of gravity casting.
  • the obtained test specimens were labeled #01 (an example including Mn), and #C1 (a comparative example not including Mn).
  • the chemical compositions of the respective test specimens were specified in Table 1. Note that, in the magnesium-alloy compositions being given in Table 1, the balances are Mg, respectively.
  • Test specimens #01 and #C1 were observed with a met allographic microscope or transmission electron microscope (TEM).
  • Fig. 1 is a metallic-structure photograph in which a cross section of the test specimen being labeled #01 was observed with a metallographic microscope.
  • the Mg crystalline grains (bright parts), and the grain-boundary crystallized substances (black parts) that existed like networks at the grain boundaries between the Mg crystalline grains were observed. Note that, although not being shown diagrammatically, a metallic-structure photograph being similar to Fig. 1 was obtained even when a cross section of the test specimen being labeled #C1 was observed. That is, in either one of the test specimens, network-shaped grain-boundary crystallized substances were observed macroscopically.
  • test specimens were adapted into a flake-shaped observational sample, respectively, and were then observed using a TEM.
  • Fig. 2 and Fig. 3 are metallic-structure photographs in which the observational samples being labeled #01 and #C1 were observed with the TEM. In both of them, crystalline grain boundaries in which two or more crystalline grains of primary-crystal Mg neighbor to each other were observed.
  • Fig. 2 (#01)
  • the grain-boundary crystallized substances black parts
  • Fig. 3 (#C1)
  • the grain-boundary crystallized substances were interrupted partially, and were discontinuous. Note that the covering ratio of networks in #01 was about 90%.
  • Fig. 4 and Fig. 5 are a dark-field scanning-transmission-electron-microscope (DF-STEM) images in which the grain-boundary crystallized substances in the observational samples according to #01 and #C1 were observed, respectively.
  • DF-STEM dark-field scanning-transmission-electron-microscope
  • the crystals in which Mg, Al and Ca were distributed uniformly were a mixed-crystal phase of type-"C14" crystalline structure and type-"C36" crystalline structure, and were virtually single crystals visually. Therefore, in the test specimens being labeled #01, the grain-boundary crystallized substances forming the networks were continuous microscopically, and they virtually turned into single crystals visually. On the contrary, in the test specimen being labeled #C1, although the grain-boundary crystallized substances formed networks macroscopically, the networks were discontinuous microscopically, and the Laves-phase compounds, which comprised type-"C36" crystalline structure alone and had undergone phase separation, were present.
  • Fig. 6 and Fig. 7 are TEM images on Test Specimen #01
  • Fig. 8 is a TEM image on Test Specimen #C1.
  • Fig. 6 the interior of the Mg crystalline grains was observed while setting the incident direction to ⁇ 110>, whereas it was observed while setting the incident angle to ⁇ 111> in Fig. 7 and Fig. 8 .
  • Fig. 6 (#01) streak-shaped precipitated substances that were parallel to the ⁇ 001 ⁇ plane were seen.
  • Fig. 7 in which the observation was carried out at the same position as that in Fig. 6 but while inclining the incident direction, the precipitated substances were found to have plate shapes that were parallel to the ⁇ 001 ⁇ plane.
  • Fig. 9 is a DF-STEM image in which the interior of the Mg crystalline grains in the observational sample being labeled #01 was observed. A plurality of fine particles were seen around the plate-shaped precipitated substances. When an elementary analysis was carried out onto the fine particles (e.g., "B” in Fig. 9 ), Mn was detected. Note that no Mn was detected even when the plate-shaped precipitated substances (e.g., "A” in Fig. 9 ) were analyzed.
  • a stress relaxation test was carried out not only onto Test Specimens #01 and #C1 given in Table 1 but also onto AXE662, AE42 and AZ91D (all as per ASTM standards), thereby examining the magnesium alloys' heat resistance (e.g., creep resistance).
  • the stress relaxation test a process was measured, process in which the stress, which was needed when a load was applied to a test specimen until it exhibited a predetermined deformation magnitude, decreased with time in the course of testing time.
  • a compression stress of 100 MPa was loaded to the test specimens, and then the compression stress was lowered in agreement with the elapse of time so as to keep the displacements of the test specimens at that time constant.
  • Test Specimen #01 exhibited a decrease proportion of the loaded stress especially less, compared with those of the other test specimens, and therefore showed high creep resistance even under high temperatures. This is due to the following: the firm networks, which were continuous microscopically, were formed at the grain boundaries between the Mg crystalline grains because of the presence of Mn; and the deformation resistance of Test Specimen #01 enlarged so that the strength thereof improved because the movements of dislocation were suppressed by the plate-shaped precipitated substances within the Mg crystalline grains.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
  • Continuous Casting (AREA)
EP08710964A 2007-04-03 2008-02-01 Hitzebeständige magnesiumlegierung Withdrawn EP2135965A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2007097760 2007-04-03
PCT/JP2008/052085 WO2008120497A1 (ja) 2007-04-03 2008-02-01 耐熱性マグネシウム合金

Publications (2)

Publication Number Publication Date
EP2135965A1 true EP2135965A1 (de) 2009-12-23
EP2135965A4 EP2135965A4 (de) 2010-03-31

Family

ID=39808082

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08710964A Withdrawn EP2135965A4 (de) 2007-04-03 2008-02-01 Hitzebeständige magnesiumlegierung

Country Status (5)

Country Link
US (1) US20100116378A1 (de)
EP (1) EP2135965A4 (de)
JP (1) JPWO2008120497A1 (de)
CN (1) CN101652489A (de)
WO (1) WO2008120497A1 (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8435444B2 (en) 2009-08-26 2013-05-07 Techmag Ag Magnesium alloy
EP2365102A4 (de) * 2008-10-03 2014-01-15 Toyota Jidoshokki Kk Hitzebeständige magnesiumlegierung

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5375482B2 (ja) * 2009-09-24 2013-12-25 株式会社Ｇｓユアサ 非水電解質二次電池用負極活物質、非水電解質二次電池用負極及び非水電解質二次電池
JP6048216B2 (ja) * 2013-02-28 2016-12-21 セイコーエプソン株式会社 マグネシウム基合金粉末およびマグネシウム基合金成形体
CN106119646A (zh) * 2016-08-17 2016-11-16 浙江特富锅炉有限公司 一种锅炉管及其制作工艺

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2741642B2 (ja) * 1992-03-25 1998-04-22 三井金属鉱業株式会社 高強度マグネシウム合金
JPH08269609A (ja) * 1995-03-27 1996-10-15 Toyota Central Res & Dev Lab Inc ダイカスト性に優れたＭｇ−Ａｌ−Ｃａ合金
JP3522963B2 (ja) * 1996-04-04 2004-04-26 三井金属鉱業株式会社 耐熱マグネシウム合金部材の製造方法およびそれに用いるマグネシウム合金、並びにマグネシウム合金成形部材
JP3415987B2 (ja) * 1996-04-04 2003-06-09 マツダ株式会社 耐熱マグネシウム合金成形部材の成形方法
JP2000104137A (ja) * 1998-09-30 2000-04-11 Mazda Motor Corp マグネシウム合金鍛造素材、及び鍛造部材並びに該鍛造部材の製造方法
US6264763B1 (en) * 1999-04-30 2001-07-24 General Motors Corporation Creep-resistant magnesium alloy die castings
JP3611759B2 (ja) * 1999-10-04 2005-01-19 株式会社日本製鋼所 耐熱性と鋳造性に優れたマグネシウム合金およびマグネシウム合金耐熱部材
JP3737440B2 (ja) * 2001-03-02 2006-01-18 三菱アルミニウム株式会社 耐熱マグネシウム合金鋳造品およびその製造方法
JP3592659B2 (ja) * 2001-08-23 2004-11-24 株式会社日本製鋼所 耐食性に優れたマグネシウム合金およびマグネシウム合金部材
JP2004162090A (ja) * 2002-11-11 2004-06-10 Toyota Industries Corp 耐熱性マグネシウム合金
JP4575645B2 (ja) * 2003-01-31 2010-11-04 株式会社豊田自動織機 鋳造用耐熱マグネシウム合金および耐熱マグネシウム合金鋳物

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2365102A4 (de) * 2008-10-03 2014-01-15 Toyota Jidoshokki Kk Hitzebeständige magnesiumlegierung
US8435444B2 (en) 2009-08-26 2013-05-07 Techmag Ag Magnesium alloy

Also Published As

Publication number Publication date
US20100116378A1 (en) 2010-05-13
EP2135965A4 (de) 2010-03-31
WO2008120497A1 (ja) 2008-10-09
CN101652489A (zh) 2010-02-17
JPWO2008120497A1 (ja) 2010-07-15

Similar Documents

Publication Publication Date Title
CA2238070C (en) Magnesium alloy having superior elevated-temperature properties and die castability
EP2369025B1 (de) Magnesiumlegierung und magnesiumlegierungsguss
US20100119405A1 (en) Magnesium alloy for casting and magnesium-alloy cast product
EP0799901A1 (de) Hitzebeständige Magnesiumlegierung
EP2088217A1 (de) Giessung einer magnesiumlegierung und verfahren zur herstellung einer gussmagnesiumlegierung
JP5703881B2 (ja) 高強度マグネシウム合金およびその製造方法
EP2135965A1 (de) Hitzebeständige magnesiumlegierung
EP2365102B1 (de) Hitzebeständige magnesiumlegierung
JP2004162090A (ja) 耐熱性マグネシウム合金
EP2138595A1 (de) Magnesiumlegierung für guss und magnesiumlegierungsguss
JP5590413B2 (ja) 高熱伝導性マグネシウム合金
JP2011219820A (ja) 耐熱マグネシウム合金
US20260117344A1 (en) Aluminium casting alloy
Nguyen et al. Improving compressive strength and oxidation resistance of AZ31B magnesium alloy by addition of nano-Al2O3 particulates and Ca
CN117604341A (zh) 高冲击韧性铝镁硅合金材料及构件的铸造方法
JPH0261023A (ja) 耐熱、耐摩耗性アルミニウム合金材及びその製造方法
JPH09316586A (ja) 耐熱・耐摩耗マグネシウム合金
JP2007291447A (ja) マグネシウム合金製摺動部品
JP4065977B2 (ja) 高温強度に優れた鋳造用アルミニウム合金
JPS61246339A (ja) 溶湯鍛造された高靭性アルミニウム合金及びその製造法
JP2018168427A (ja) マグネシウム合金及びその製造方法
Chen et al. Microstructure, Mechanical Properties and Electrical Conductivity of Heat-Resistant Al-Ce and Al-Ni Eutectic Alloys
JP2018062701A (ja) マグネシウム合金

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: 20090923

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

A4 Supplementary search report drawn up and despatched

Effective date: 20100226

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 23/02 20060101ALI20100222BHEP

Ipc: C22C 23/00 20060101AFI20081020BHEP

DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION HAS BEEN WITHDRAWN

18W Application withdrawn

Effective date: 20120201