EP2924137A1 - Alliages d'aluminium pour la coulée sous pression - Google Patents
Alliages d'aluminium pour la coulée sous pression Download PDFInfo
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- EP2924137A1 EP2924137A1 EP14168188.2A EP14168188A EP2924137A1 EP 2924137 A1 EP2924137 A1 EP 2924137A1 EP 14168188 A EP14168188 A EP 14168188A EP 2924137 A1 EP2924137 A1 EP 2924137A1
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- aluminum
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 98
- 239000000956 alloy Substances 0.000 title claims abstract description 98
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 48
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 40
- 238000004512 die casting Methods 0.000 title claims abstract description 33
- 239000004411 aluminium Substances 0.000 title 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 20
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 13
- 239000010937 tungsten Substances 0.000 claims abstract description 13
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 239000011733 molybdenum Substances 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims abstract description 8
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 8
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 239000010949 copper Substances 0.000 claims abstract description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 239000011651 chromium Substances 0.000 claims abstract description 3
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 3
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 3
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 3
- 239000011777 magnesium Substances 0.000 claims abstract description 3
- 238000004519 manufacturing process Methods 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 239000010955 niobium Substances 0.000 claims abstract description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052706 scandium Inorganic materials 0.000 claims abstract description 3
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 3
- 239000010703 silicon Substances 0.000 claims abstract description 3
- 229910052712 strontium Inorganic materials 0.000 claims abstract description 3
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 3
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000010936 titanium Substances 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 230000007704 transition Effects 0.000 claims abstract description 3
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 3
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 239000011701 zinc Substances 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims description 57
- 239000011572 manganese Substances 0.000 claims description 41
- 229910000838 Al alloy Inorganic materials 0.000 claims description 15
- 239000013078 crystal Substances 0.000 claims description 12
- 239000011159 matrix material Substances 0.000 claims description 11
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 238000000034 method Methods 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- 239000002244 precipitate Substances 0.000 description 12
- 238000005728 strengthening Methods 0.000 description 9
- 238000012360 testing method Methods 0.000 description 7
- 238000005266 casting Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 229910000951 Aluminide Inorganic materials 0.000 description 4
- 230000008859 change Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910000676 Si alloy Inorganic materials 0.000 description 3
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 3
- -1 aluminum-nickel-manganese-tungsten Chemical compound 0.000 description 3
- 239000000155 melt Substances 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910018131 Al-Mn Inorganic materials 0.000 description 2
- 229910018461 Al—Mn Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001093 Zr alloy Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000000446 fuel Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000003878 thermal aging Methods 0.000 description 2
- 229910052723 transition metal Inorganic materials 0.000 description 2
- 150000003624 transition metals Chemical class 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 1
- ZGUQGPFMMTZGBQ-UHFFFAOYSA-N [Al].[Al].[Zr] Chemical compound [Al].[Al].[Zr] ZGUQGPFMMTZGBQ-UHFFFAOYSA-N 0.000 description 1
- DIVGJYVPMOCBKD-UHFFFAOYSA-N [V].[Zr] Chemical compound [V].[Zr] DIVGJYVPMOCBKD-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical class [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- HIMLGVIQSDVUJQ-UHFFFAOYSA-N aluminum vanadium Chemical compound [Al].[V] HIMLGVIQSDVUJQ-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000001427 coherent effect Effects 0.000 description 1
- 230000001609 comparable effect Effects 0.000 description 1
- 230000001010 compromised effect Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000010120 permanent mold casting Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005382 thermal cycling Methods 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
Images
Classifications
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- 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
-
- 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
Definitions
- the present invention relates to aluminum alloys that are dispersion-strengthened, age-hardenable, and can be processed by die-casting into shaped objects that have useful mechanical properties at temperatures up to at least 350°C.
- Automotive engines made with aluminum alloys have a high power-to-weight ratio, and therefore they have better fuel efficiency and less negative impact on the environment than cast iron engines.
- 'supercharged' engines are being designed to operate at even higher temperatures than regular engines. Accordingly, cylinder heads and engine blocks in 'supercharged' engines are subjected to thermal cycling over a wider temperature range, and the alloy used in their construction has to withstand the resulting severe thermo-mechanical loading over long periods of time.
- Conventional casting aluminum alloys are not capable of withstanding these temperatures because their precipitation hardening effects disappear at about 200°C.
- the alloys represented in WO 2011/124590 have better mechanical properties at elevated temperatures than traditional aluminum casting alloys.
- the volume fraction of the fine zirconium-vanadium tri-aluminide (Al 3 V 1-x Zr x ) particles in the prior art alloys do not exceed 1 % by volume; they have a limited strengthening effect.
- an option of the prior art invention calls for adding up to 5 % by weight manganese to the alloy.
- manganese, together with aluminum forms metastable manganese aluminide particles (Al 12 Mn) that further increase the strength of the alloy.
- these additional precipitate particles add strength to the alloy at room temperature, their strengthening effect disappears with increased service time at elevated temperatures.
- the present invention relates to a class of aluminum alloys that (i) are dispersion-strengthened, (ii) can be processed by die-casting to produce useful shaped objects, and (iii) can be age-hardened for improved room temperature mechanical properties that are retained at temperatures up to at least 350°C.
- Alloys of the present invention have the general chemical composition: aluminum-nickel-manganese-tungsten/molybdenum-zirconium-vanadium, and their chemical composition is optimized such that their liquidus temperature is less than 725°C. Such low liquidus temperature allows the alloys of the present invention to be processed into useful objects by traditional high-pressure die-casting.
- alloys of the present invention contain a eutectic structure that is stable at temperatures approaching 640°C, and it contains strengthening precipitate particles that are thermally stable at temperatures approaching 350°C.
- the microstructure of the aluminum alloys of the present invention contains nickel trialuminide and aluminum as its eutectic structure, together with other transition metal tri-aluminide particles, namely Al 3 V 1-x Zr x .
- transition metal trialuminide particles have the highly symmetric L1 2 crystal structure, which is analogous to the face centered cubic crystal structure of aluminum. It is this similarity in crystal structure between the aluminum matrix and these strengthening particles that allows for a coherent interface between the two phases; and by doing so, it maximizes the strengthening ability of the particles, impedes their coarsening, and enhances the thermal stability of the alloy.
- alloys of the present invention A feature of the alloys of the present invention that distinguishes them from the prior art aluminum alloys that contain nickel, vanadium, and zirconium together with manganese, but without tungsten is that in the alloys of the present invention, the Al 3 V 1-x Zr x particles are not the only thermally stable strengthening precipitates in the alloy. Alloys of the present invention rely on a relatively large amount of Al 12 Mn 1-x W x precipitate particles for added strength at elevated temperature. Alloys of the present invention also rely on carefully designed tungsten containing manganese-aluminide (Al 12 Mn 1-x W x ) precipitate particles for strength at elevated temperature.
- Al 12 Mn 1-x W x precipitate particles have the body centered cubic crystal structure, which is akin to the face centered cubic crystal structure of the ⁇ -aluminum matrix; and therefore they are semi-coherent with the ⁇ -aluminum matrix. Moreover, Al 12 Mn 1-x W x particles do not readily coarsen when exposed to elevated temperatures and therefore - as shown in figure 1 - unlike the aluminum alloys of the prior art, alloys of the present invention retain a significant fraction of their room temperature mechanical properties at elevated temperatures.
- alloys of the present invention contain tungsten and/ or molybdenum.
- the Al 3 V 1-x Zr x particles are not the only thermally stable strengthening precipitates. Because of their small quantity in the alloy ( ⁇ 1 % by volume), by themself the Al 3 V 1-x Zr x particles can contribute only limited high temperature strength. Alloys of the present invention rely on a relatively large amount of Al 12 Mn 1-x W x precipitate particles for added strength at elevated temperature.
- the precipitation sequence during thermal aging of binary Al-Mn alloys starts with formation of metastable Al 12 Mn particles. These particles are, to a large extent, responsible for the observed strength of thermally aged binary Al-Mn alloys. With extended time at an elevated temperature, these metastable Al 12 Mn particles coarsen and eventually they transform to the stable Al 6 Mn phase. The Al 6 Mn particles have the rhombohedral crystal structure, and therefore they have incoherent interfaces with the surrounding ⁇ -aluminum matrix. Transformation of the metastable, semi-coherent Al 12 Mn particles into stable, incoherent Al 6 Mn particles signals the loss of their strengthening effect.
- the present invention capitalizes on the fact that the lattice of the metastable Al 12 Mn phase is similar to that of the Al 12 W phase (both are body centered cubic), and also on the fact that the lattice parameter of the Al 12 Mn phase (0.754 nm) is close to that of the Al 12 W phase (0.758 nm). For these two reasons, during precipitation from the super saturated solid solution, tungsten can dissolve into the Al 12 Mn phase to form Al 12 Mn 1-x W x co-precipitates. Similar to the Al 12 Mn particles, the Al 12 Mn 1-x W x particles have body centered cubic lattice structure and semi-coherent interfaces with the ⁇ -aluminum matrix.
- thermodynamic calculations show that dissolution of tungsten into Al 12 Mn lowers the Gibbs free energy of the thus-formed Al 12 Mn 1-x W x particles relative to the Gibbs free energy of Al 12 Mn. This makes the Al 12 Mn 1-x W x particles more resistant to coarsening when exposed to elevated temperature, and therefore less prone to transforming into the incoherent Al 6 Mn phase, than the Al 12 Mn particles.
- an aluminum die-casting alloy comprising the following:
- the aluminum die-casting alloy comprises 4 to 6 % by weight nickel.
- the aluminum die-casting alloy further comprises 2 to 4% by weight manganese.
- the aluminum die-casting alloy comprises 0.2 to 0.8 % by weight tungsten.
- the aluminum die-casting alloy comprises 0.2 to 0.8 % by weight molybdenum.
- the aluminum die-casting alloy comprises 0.1 to 0.3 % by weight zirconium.
- the aluminum die-casting alloy comprises 0.3 to 0.4 % by weight vanadium.
- the aluminum die-casting alloy includes substantially uniformly dispersed particles of Al 3 V x Zr 1-x , where x is a fraction of unity that depends on the ratio of Zr : V in the alloy.
- the particles having an equivalent diameter of less than about 50 nm, preferably less than about 30 nm, more preferably less than about 10 nm, particularly less than about 5 nm.
- the aluminum die-casting alloy includes particles of Al 3 Ni having an equivalent diameter of less than about 500 nm, preferably less than about 300 nm, particularly less than about 100 nm.
- the aluminum die-casting alloy includes substantially uniformly dispersed particles of Al 12 Mn 1-x W x , where x is a fraction of unity that depends on the ratio of W : Mn in the alloy, the particles having an equivalent diameter of less than about 500 nm, preferably less than about 300 nm, particularly less than 100 nm.
- the Al 12 Mn 1-x W x particles have a body centered cubic crystal structure.
- the Al 12 Mn 1-x W x particles are semi-coherent with the ⁇ -aluminum matrix.
- the aluminum die-casting alloy includes substantially uniformly dispersed particles of Al 12 Mn 1-x Mo x , where x is a fraction of unity that depends on the ratio of Mo : Mn in the alloy, the particles having an equivalent diameter of less than about 500 nm, preferably less than about 300 nm, particularly less than 100 nm.
- the Al 12 Mn 1-x Mo x particles have a body centered cubic crystal structure.
- the Al 12 Mn 1-x Mo x particles are semi-coherent with the ⁇ -aluminum matrix.
- the die casting alloy includes substantially uniformly dispersed particles of Al 12 Mn 1-x-y W x Mo y , where x and y are fractions of unity that depend on the ratio of W : Mo : Mn in the alloy, the particles having an equivalent diameter of less than about 500 nm, preferably less than about 300 nm, particularly less than 100 nm.
- the Al 12 Mn 1-x-y W x Mo y particles have a body centered cubic crystal structure.
- the Al 12 Mn 1-x-y W x Mo y particles are semi-coherent with the ⁇ -aluminum matrix.
- a high pressure die-cast component is made is made of the alloy according to the invention.
- the aluminum die-casting alloy is solidified in a metal water-cooled mold.
- a cast component is made from an aluminum die-casting alloy according to the invention, wherein the alloy is age-hardened by holding the solidified cast component at a temperature of 350°C to 450°C for 2 to 12 hours.
- the aluminum alloy comprises 5.5 to 6.0 % by weight nickel, 1.75 to 2.0 % by weight manganese, 0.1 to 0.3 % by weight of zirconium, 0.3 to 0.4 % by weight of vanadium and 0.3 to 0.4 % by weight tungsten.
- the aluminum alloy comprises 5.75 to 6.00 % by weight nickel, 3.75 to 4.25 % by weight manganese, 0.3 to 0.4 % by weight of vanadium, 0.1 to 0.2 % by weight zirconium, 0.25 to 0.30 % by weight tungsten, 0.25 to 0.30 by weight molybdenum and Al as remainder.
- the melt was poured into a water-cooled copper mold to produce disk-shaped castings that were then machined into ASTM standard sub-size tensile test specimens.
- the tensile test specimens were aged in an electric box furnace at 450°C for 10 hours and then divided into four groups each group containing six identical specimens.
- the elevated temperature yield strength of each group of specimens was measured by means of an Instron Universal Testing machine. Prior to performing the measurements, the tensile specimens were soaked in an electric box furnace at the following test temperatures for 100 hours; and during the test, each tensile specimen was soaked in the furnace of the Instron Universal Testing machine at the test temperature for an additional 30 minutes in order to allow the specimen to equilibrate at the test temperature.
- Group No. Temperature (oC) 1 25 2 300 3 350 4 400
- Figure 3 shows the change in the measured yield strength of the Al-6Ni-4Mn-0.8W-0.4V-0.1 Zr alloy of the present invention compared to that of 380-F and 356-T6 commercial aluminum-silicon alloys.
- the alloy of the present invention outperforms both commercial alloys at all temperatures above 150°C.
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- 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)
- Continuous Casting (AREA)
- Molds, Cores, And Manufacturing Methods Thereof (AREA)
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US15/127,120 US20170101703A1 (en) | 2014-03-26 | 2015-02-27 | Aluminum Die-Casting Alloys |
| PCT/EP2015/054180 WO2015144387A1 (fr) | 2014-03-26 | 2015-02-27 | Alliages d'aluminium pour le moulage sous pression |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US201461970586P | 2014-03-26 | 2014-03-26 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| EP2924137A1 true EP2924137A1 (fr) | 2015-09-30 |
Family
ID=50693529
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP14168188.2A Withdrawn EP2924137A1 (fr) | 2014-03-26 | 2014-05-13 | Alliages d'aluminium pour la coulée sous pression |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US20170101703A1 (fr) |
| EP (1) | EP2924137A1 (fr) |
| WO (1) | WO2015144387A1 (fr) |
Cited By (8)
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|---|---|---|---|---|
| CN105950922A (zh) * | 2016-06-07 | 2016-09-21 | 太仓市纯杰金属制品有限公司 | 一种抗氧化镍铝合金 |
| CN105970037A (zh) * | 2016-07-15 | 2016-09-28 | 南南铝业股份有限公司 | 人行天桥用铝合金及其制备方法 |
| CN106119637A (zh) * | 2016-08-04 | 2016-11-16 | 苏州优浦精密铸造有限公司 | 一种汽车用高强度铝合金材料 |
| CN107739857A (zh) * | 2017-10-04 | 2018-02-27 | 长沙仲善新能源科技有限公司 | 耐腐蚀铝合金材料的制备工艺及耐腐蚀铝合金材 |
| CN109778028A (zh) * | 2019-01-21 | 2019-05-21 | 宁波市鄞州迪信机械制造有限公司 | 一种缝纫机铝合金盖板 |
| WO2020028730A1 (fr) * | 2018-08-02 | 2020-02-06 | Tesla, Inc. | Alliages d'aluminium pour coulée sous pression |
| WO2020165542A1 (fr) | 2019-02-15 | 2020-08-20 | C-Tec Constellium Technology Center | Procédé de fabrication d'une pièce en alliage d'aluminium |
| US11421304B2 (en) | 2017-10-26 | 2022-08-23 | Tesla, Inc. | Casting aluminum alloys for high-performance applications |
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| JP7112275B2 (ja) * | 2018-07-26 | 2022-08-03 | 三菱重工業株式会社 | アルミニウム合金材料、アルミニウム合金材料の製造方法、キャスク用バスケット及びキャスク |
| US11408061B2 (en) * | 2019-10-01 | 2022-08-09 | Ford Global Technologies, Llc | High temperature, creep-resistant aluminum alloy microalloyed with manganese, molybdenum and tungsten |
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| CN116240432B (zh) * | 2023-02-08 | 2024-05-28 | 上海交通大学 | 一种免热处理压铸铝合金、制备方法及应用 |
| CN116287890B (zh) * | 2023-03-29 | 2024-01-16 | 深圳市鑫申新材料科技有限公司 | 一种高强韧、高焊接性能、免热处理高压铸造铝合金及其性能、制备方法 |
| CN118685670B (zh) * | 2024-08-29 | 2024-12-17 | 山东海化集团有限公司 | 一种免热处理高强韧压铸铝合金材料及其制备方法 |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63219543A (ja) * | 1987-03-10 | 1988-09-13 | Showa Alum Corp | 発色用アルミニウム合金 |
| JPH01132733A (ja) * | 1987-11-17 | 1989-05-25 | Kasei Naoetsu:Kk | 防振アルミニウム合金 |
| US20040261916A1 (en) * | 2001-12-21 | 2004-12-30 | Lin Jen C. | Dispersion hardenable Al-Ni-Mn casting alloys for automotive and aerospace structural components |
| WO2011124590A1 (fr) | 2010-04-07 | 2011-10-13 | Rheinfelden Alloys Gmbh & Co. Kg | Alliage d'aluminium pour la coulée sous pression |
-
2014
- 2014-05-13 EP EP14168188.2A patent/EP2924137A1/fr not_active Withdrawn
-
2015
- 2015-02-27 US US15/127,120 patent/US20170101703A1/en not_active Abandoned
- 2015-02-27 WO PCT/EP2015/054180 patent/WO2015144387A1/fr not_active Ceased
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| JPS63219543A (ja) * | 1987-03-10 | 1988-09-13 | Showa Alum Corp | 発色用アルミニウム合金 |
| JPH01132733A (ja) * | 1987-11-17 | 1989-05-25 | Kasei Naoetsu:Kk | 防振アルミニウム合金 |
| US20040261916A1 (en) * | 2001-12-21 | 2004-12-30 | Lin Jen C. | Dispersion hardenable Al-Ni-Mn casting alloys for automotive and aerospace structural components |
| WO2011124590A1 (fr) | 2010-04-07 | 2011-10-13 | Rheinfelden Alloys Gmbh & Co. Kg | Alliage d'aluminium pour la coulée sous pression |
| EP2653578A1 (fr) * | 2010-04-07 | 2013-10-23 | Rheinfelden Alloys GmbH & Co. KG | Alliage d'aluminium pour la coulée sous pression |
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| KAUFMAN, J.G.; ROOY, E.L.: "Aluminum Alloy Castings: Properties, Processes, and Applications", AFS, 2004 |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105950922A (zh) * | 2016-06-07 | 2016-09-21 | 太仓市纯杰金属制品有限公司 | 一种抗氧化镍铝合金 |
| CN105970037A (zh) * | 2016-07-15 | 2016-09-28 | 南南铝业股份有限公司 | 人行天桥用铝合金及其制备方法 |
| CN106119637A (zh) * | 2016-08-04 | 2016-11-16 | 苏州优浦精密铸造有限公司 | 一种汽车用高强度铝合金材料 |
| CN107739857A (zh) * | 2017-10-04 | 2018-02-27 | 长沙仲善新能源科技有限公司 | 耐腐蚀铝合金材料的制备工艺及耐腐蚀铝合金材 |
| US11421304B2 (en) | 2017-10-26 | 2022-08-23 | Tesla, Inc. | Casting aluminum alloys for high-performance applications |
| WO2020028730A1 (fr) * | 2018-08-02 | 2020-02-06 | Tesla, Inc. | Alliages d'aluminium pour coulée sous pression |
| CN112567059A (zh) * | 2018-08-02 | 2021-03-26 | 特斯拉公司 | 用于压铸的铝合金 |
| US12378642B2 (en) | 2018-08-02 | 2025-08-05 | Tesla, Inc. | Aluminum alloys for die casting |
| CN109778028A (zh) * | 2019-01-21 | 2019-05-21 | 宁波市鄞州迪信机械制造有限公司 | 一种缝纫机铝合金盖板 |
| WO2020165542A1 (fr) | 2019-02-15 | 2020-08-20 | C-Tec Constellium Technology Center | Procédé de fabrication d'une pièce en alliage d'aluminium |
| FR3092777A1 (fr) | 2019-02-15 | 2020-08-21 | C-Tec Constellium Technology Center | Procédé de fabrication d'une pièce en alliage d'aluminium |
| EP3924124B1 (fr) * | 2019-02-15 | 2023-11-15 | C-Tec Constellium Technology Center | Procédé de fabrication d'une pièce en alliage d'aluminium |
| US12528125B2 (en) | 2019-02-15 | 2026-01-20 | C-Tec Constellium Technology Center | Method for manufacturing an aluminum alloy part |
Also Published As
| Publication number | Publication date |
|---|---|
| US20170101703A1 (en) | 2017-04-13 |
| WO2015144387A1 (fr) | 2015-10-01 |
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