EP2516687A1 - Pièce moulée en alliage d'aluminium au cuivre à haute résistance mécanique et au fluage à chaud - Google Patents
Pièce moulée en alliage d'aluminium au cuivre à haute résistance mécanique et au fluage à chaudInfo
- Publication number
- EP2516687A1 EP2516687A1 EP10799072A EP10799072A EP2516687A1 EP 2516687 A1 EP2516687 A1 EP 2516687A1 EP 10799072 A EP10799072 A EP 10799072A EP 10799072 A EP10799072 A EP 10799072A EP 2516687 A1 EP2516687 A1 EP 2516687A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- molded part
- part according
- content
- insert
- alloy
- 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.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 12
- JRBRVDCKNXZZGH-UHFFFAOYSA-N alumane;copper Chemical compound [AlH3].[Cu] JRBRVDCKNXZZGH-UHFFFAOYSA-N 0.000 title description 5
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 25
- 229910052802 copper Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 239000000203 mixture Substances 0.000 claims abstract description 7
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 239000000126 substance Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 229910045601 alloy Inorganic materials 0.000 claims description 52
- 239000000956 alloy Substances 0.000 claims description 52
- 239000011777 magnesium Substances 0.000 claims description 27
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 23
- 239000010949 copper Substances 0.000 claims description 12
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 10
- 239000010936 titanium Substances 0.000 claims description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 238000000465 moulding Methods 0.000 claims description 5
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 4
- 239000011572 manganese Substances 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 230000003068 static effect Effects 0.000 claims description 4
- 239000011701 zinc Substances 0.000 claims description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 239000007921 spray Substances 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 2
- 239000003232 water-soluble binding agent Substances 0.000 claims description 2
- 239000012943 hotmelt Substances 0.000 claims 1
- 238000002485 combustion reaction Methods 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 8
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 6
- 229910000676 Si alloy Inorganic materials 0.000 description 5
- 238000007711 solidification Methods 0.000 description 5
- 230000008023 solidification Effects 0.000 description 5
- 238000002679 ablation Methods 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- 229910052796 boron Inorganic materials 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 238000007528 sand casting Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 230000000670 limiting effect Effects 0.000 description 2
- 238000004064 recycling Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 241000251948 Dolophilodes major Species 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 239000000284 extract Substances 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 239000008188 pellet Substances 0.000 description 1
- 230000000750 progressive effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000010112 shell-mould casting Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
- C22F1/057—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 copper as the next major constituent
Definitions
- the invention relates to copper aluminum alloy castings subjected to high mechanical stresses and working, at least in some of their areas, at high temperatures, including cylinder heads supercharged diesel or gasoline engines.
- the alloys commonly used for the cylinder heads of automotive mass-produced vehicles are essentially silicon alloys (5 to 10% Si in general) often containing copper and magnesium in order to increase their mechanical characteristics, especially when hot. .
- the main types used are: AlSi7Mg, AlSi7CuMg, AlSi (5 to 8) Cu3Mg, AlSilOMg, AlSilOCuMg.
- These alloys are used with different methods of heat treatment: sometimes in the F-state without any treatment, sometimes in the T5 state with a simple income, sometimes in the T6 state with dissolution, quenching and drying. at the peak of hardening or slightly below, and often in the T7 state with dissolution, quenching and over-tempering or stabilization.
- copper alloys of the AlCu5 type are also sometimes used. added with elements promoting the heat resistance such as Ni, Co, Ti, V and Zr: there is particularly in this category AlCu5NiCoZr and AlCu4NiTi. These alloys are very resistant to heat, especially at 300 ° C where they clearly outperform the silicon aluminum mentioned above, but suffer from two serious weaknesses: their high cracks, combined with a bad shrinkage behavior, which makes them very difficult.
- Table 1 summarizes the characteristics at ambient temperature of these two sand-cast alloys heat-treated in the T7 state (Rp0.2 (or 0.2% TYS) being the elastic limit in MPa; Rm (or UTS) being the breaking strength in MPa, and A (or E) being elongation at break in%:
- AlCu5Mg alloys such as AlCu5MgTi (designated 204 following ⁇ ), and A206 and B206 (following ⁇ ), intended for rooms working at ambient or moderate temperature, do not meet these requirements, in particular at 300 ° C.
- the alloys AlCu4NiTi and AlCu5NiCoZr (203 following ⁇ ) mentioned above are too weak and fragile at room temperature.
- the subject of the invention is therefore a molded part with high static resistance at ambient temperature and with high heat resistance and high creep resistance, in particular at 300 ° C. and above, cast in aluminum alloy of the following chemical composition , expressed in percentages by weight:
- Mn ⁇ 0.70%, preferably 0.20 - 0.50%
- Mg 0.05 - 0.20%, preferably 0.07 - 0.20%, and more preferably 0.08 - 0.20% and finally very preferably 0.09 - 0.13%
- Zn ⁇ 0.30%, preferably ⁇ 0.10% and more preferably ⁇ 0.03%
- Ni ⁇ 0.30%, preferably ⁇ 0.10% and more preferably ⁇ 0.03%
- V 0.05 - 0.30%, preferably 0.08 - 0.25%, and more preferably 0.10 - 0.20%
- Zr 0.05 - 0.25%, preferably 0.08 - 0.20%
- FIG. 1 represents a cluster of four shell-cast specimens from the Rio Tinto Alcan company with a 1 ⁇ 4 "diameter (6.35 mm).
- Figure 2 shows differential enthalpy analysis curves for AlCu4.7MnVZrTi alloys with magnesium content of 0%, 0.09% and 0.13%.
- Figure 3 shows creep test results at 300 ° C on AlCu4.7MnVZrTi treated T7 alloys and AlSi7Cu3.5MnVZrTi also treated T7 with variable magnesium content respectively from 0% to 0.13%. and from 0.1% to 0.15%. Description of the invention
- the invention is based on the finding by the applicant that it is possible to make very significant improvements to the characteristics mentioned above of the old alloy 224 (following ⁇ ), and thus to solve the problem posed, in particular by the addition of a limited amount of magnesium.
- the addition of a small amount of magnesium, of the order of 0.10 to 0.15%, makes it possible to considerably increase the yield strength and the resistance of the alloy not only at room temperature but also hot, especially at 250-300 ° C and above. It is at room temperature that the relative gain is the most important: as explained in the following examples and Tables 6, 7, 8, the elastic limit goes from about 190 MPa without magnesium to about 340 MPa with only 0.09% and then at over 390 MPa with 0.13%. If we consider the average results obtained with 0.09% and 0.13% magnesium, the gains observed on the yield strength and the resistance at ambient temperature are remarkable: respectively + 96% and + 29% in relative terms. However, the elongation is substantially reduced by half but still retains a suitable level of 6 to 8%.
- the gains brought by the addition of magnesium remain even if they decrease.
- the observed gains in yield strength and strength are respectively 35 and 13% in relative terms at 250 ° C, and 27 and 8% in relative terms at 300 ° C.
- the addition of magnesium remains beneficial at least up to 300 ° C., especially as the loss of elongation fades at these high temperatures.
- the addition of magnesium considerably improves the hot creep resistance, reducing by approximately 2, for example, the deformation observed after 300 h at 300 ° C. under a stress of 30 MPa.
- the addition of magnesium does not therefore affect the hot stability, contrary to the philosophy that led to the definition of alloys AlCu5NiCoZr (203 according to A A) and AlCu5MnVZr (224 according to A A) conventional which are lacking magnesium.
- the alloy according to the invention treated T7 can be compared with the AlSi7Cu3.5Mg0.15MnVZrTi also treated T7, which was also developed by the applicant and is its most creep-resistant knowledge of the series of aluminum silicon alloys considered in the previous table.
- the magnesium content can be increased beyond the area already experienced in the examples. If only very high strength and hardness are sought, with a reduced ductility requirement, a maximum level of 0.38% can be envisaged, knowing that the burn temperature will be lowered and the heat treatment will have to be adapted. The minimum to obtain a significant curing effect is of the order of 0.05%. A smaller range is from 0.07% to 0.30% and the preferred range, corresponding to the resistance-ductility-creep tradeoffs quantified in the examples while having an industrially acceptable width is 0.08-0.20%, or even 0.09-1.03%.
- Silicon It is generally harmful to ductility and can lower the burn temperature. On the other hand, it improves the foundry properties and in particular is likely, even at a low level, to reduce the feasibility, as described in the ASM Handbook, volume 15, edition 2008. A minimum level of 0.02% is necessary. A maximum level of 0.50% is conceivable for parts solidified very quickly or requiring little elongation, but we will generally prefer less than 0.20%, or even 0.06%.
- Iron it is harmful to the ductility, but decreases against the çriquange, as also described in ASM Handbook, volume 15, edition 2008. Moreover limiting it to a very low level obviously increases the cost of the piece. A minimum level of 0.02% is therefore advantageous. A maximum level of 0.30% is conceivable for parts solidified very quickly or not requiring much elongation, but one will generally prefer less than 0.20% for large automotive series, or even 0.12% or even 0.06% for highly stressed parts.
- the Applicant has carried out work on alloy B206 for which it considers that the results which are transferable to the alloy according to the invention and show that a lowering of copper from 5.0% to 4.0% allows to gain significantly in elongation at the cost of a loss of resistance, but that it remains higher than 400 MPa. In view of some cylinder heads, it is even conceivable to accept a slightly larger drop in resistance to favor elongation and reduce copper up to 3.5%.
- Manganese this element must not exceed 0.70% otherwise the risk of forming coarse intermetallic phases. Since it generally improves the mechanical properties, especially when hot, a range of 0.20 to 0.50% similar to that of 206 type alloys is preferred.
- Zinc this element is an impurity which, at high content, can decrease the mechanical properties and make the liquid bath more oxidizable. It may be envisaged to tolerate up to 0.30% in order to facilitate the use of recycle metal, but less than 0.10% and better still less than 0.03% is preferred for high performance parts.
- Nickel it generally contributes to the mechanical strength when hot but considerably reduces elongation. As the hot resistance is ensured in the invention by the addition of other elements, copper, magnesium, vanadium and zirconium, nickel is considered here as an impurity, which is limited to a maximum of 0.30% for the purpose of facilitate the use of recycling metal, and preferably at 0.10% and even better at 0.03% for high performance parts.
- Vanadium This peritectic element in particular improves the resistance to creep when hot. Applicant has observed that in another alloy base containing silicon, the creep resistance was greatly improved between 0 and 0.05%, then improved more gradually from 0.05% to 0.17% and was above 0.17%. % stable at an excellent level. Limiting the maximum level of vanadium to 0.15% as in the old 224 does not therefore seem desirable. In the alloy according to the invention, a level of 0.05 to 0.30% is provided, which can be tightened to narrower subdomains of 0.08 - 0.25% and preferably 0.10 - 0.20%.
- this peritectic element also improves in particular the resistance to hot creep, and its effect is additive to that of vanadium. A content of 0.05 - 0.25% and preferably 0.08 - 0.20% is retained.
- Titanium This peritectic element has two different effects: on the one hand, it is often used as a refining element of the grain, often in combination with an addition of parent alloy or salt adding titanium and boron. However, there are other refining practices consisting of adding only products introducing titanium and boron, or even only boron, and in the latter case the presence of titanium is not favorable. On the other hand, titanium contributes to good resistance to creep hot, although less strongly than vanadium and zirconium, as the applicant has observed. A maximum content of 0.35% has therefore been retained, but an addition of 0.05 to 0.25% and even more preferably of 0.10 to 0.20% is preferred.
- the other elements are to be considered as impurities.
- the burning temperature of the various compositions was first determined by performing differential enthalpic analyzes (AED) on pellets machined in the cast specimens. The rate of rise in temperature was 20 ° C / minute. The AED curves are shown in FIG. 2. The burning temperatures observed corresponding to the melting peaks obviously depend on the magnesium content as shown in Table 5:
- the burn temperature gradually shifts to lower temperatures when the Mg content increases from 0% to 0.09% and then to 0.13%.
- the blanks intended for the creep tests were subjected, prior to this heat treatment, to hot isostatic compaction at 1000 bar at 485 ° C. for 2 hours in order to eliminate any microporosity which could seriously affect the tests given the small diameter of the specimen.
- Static mechanical characteristics were measured at room temperature and at 250 ° C and 300 ° C. In the latter two cases, the specimens were preheated for 100 hours at the temperature before being tracted.
- Creep tests were conducted at 300 ° C under the following conditions:
- test pieces with a diameter of 4 mm in the working zone were first preheated for 100 h at 300 ° C. in a separate oven, then placed on the creep machine and stabilized again for 1 ⁇ 2 hour. at 300 ° C before putting them under a constant load of 30 MPa.
- The% strain is then recorded continuously for 300 hours at 300 ° C.
- the main criterion used for the interpretation of the tests is the deformation obtained after 300 h.
- Table 9 summarizes the results: Table 9: Creep at 300 ° C. under 30 MPa
- a part may then be molded from the advantageous alloy defined above, this part may in particular be a cylinder head or an insert of a cylinder head or of another part requiring a high static mechanical resistance at room temperature and at room temperature. hot and high resistance to creep when hot, in particular at 300 ° C.
- the part is advantageously treated T7, even if a T6 treatment is also possible.
- Ablation molding is particularly suitable for molding high-tread alloys. Initially, it is sand casting that does not much upset the withdrawal, and then after removal of the mold the end of the solidification is carried out without rigid mold at all. In addition to providing a high solidification rate, the process also leads to high temperature gradients because the spray is generally progressive, starting on selected areas and advancing towards the end points of solidification where it is possible to attach. the weights. This advantageously also favors the use of alloys with low feed capacity of the shrink, such as copper aluminum alloys, including the alloy according to the invention.
- the invention also relates to a method for molding a part from the alloy according to the invention, in particular an insert or a cylinder head, comprising the steps of:
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Cylinder Crankcases Of Internal Combustion Engines (AREA)
- Supercharger (AREA)
Abstract
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PL10799072T PL2516687T3 (pl) | 2009-12-22 | 2010-12-07 | Odlew ze stopu aluminium z miedzią, posiadający dużą wytrzymałość mechaniczną i trwałość w próbie pełzania na gorąco |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR0906218A FR2954355B1 (fr) | 2009-12-22 | 2009-12-22 | Piece moulee en alliage d'aluminium au cuivre a haute resistance mecanique et au fluage a chaud |
PCT/FR2010/000812 WO2011083209A1 (fr) | 2009-12-22 | 2010-12-07 | Pièce moulée en alliage d'aluminium au cuivre à haute résistance mécanique et au fluage à chaud |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2516687A1 true EP2516687A1 (fr) | 2012-10-31 |
EP2516687B1 EP2516687B1 (fr) | 2016-08-10 |
Family
ID=42122814
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP10799072.3A Active EP2516687B1 (fr) | 2009-12-22 | 2010-12-07 | Pièce moulée en alliage d'aluminium au cuivre à haute résistance mécanique et au fluage à chaud |
Country Status (11)
Country | Link |
---|---|
US (1) | US20120258010A1 (fr) |
EP (1) | EP2516687B1 (fr) |
JP (1) | JP5758402B2 (fr) |
KR (1) | KR101757013B1 (fr) |
BR (1) | BR112012016917A2 (fr) |
CA (1) | CA2812236C (fr) |
ES (1) | ES2601809T3 (fr) |
FR (1) | FR2954355B1 (fr) |
MX (1) | MX2012006988A (fr) |
PL (1) | PL2516687T3 (fr) |
WO (1) | WO2011083209A1 (fr) |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10266933B2 (en) * | 2012-08-27 | 2019-04-23 | Spirit Aerosystems, Inc. | Aluminum-copper alloys with improved strength |
FR3007423B1 (fr) * | 2013-06-21 | 2015-06-05 | Constellium France | Element de structure extrados en alliage aluminium cuivre lithium |
US9643651B2 (en) | 2015-08-28 | 2017-05-09 | Honda Motor Co., Ltd. | Casting, hollow interconnecting member for connecting vehicular frame members, and vehicular frame assembly including hollow interconnecting member |
DE102016200535A1 (de) * | 2016-01-18 | 2017-07-20 | Bayerische Motoren Werke Aktiengesellschaft | Verfahren zum Herstellen einer Aluminium-Gusslegierung |
CN107419148A (zh) * | 2017-05-05 | 2017-12-01 | 安徽彩晶光电有限公司 | 用于液晶电视支架的复合铝合金 |
CN112281034A (zh) * | 2020-10-16 | 2021-01-29 | 中国航发北京航空材料研究院 | 一种铸造铝合金及其制备方法 |
US20220170138A1 (en) * | 2020-12-02 | 2022-06-02 | GM Global Technology Operations LLC | Aluminum alloy for casting and additive manufacturing of engine components for high temperature applications |
CN114058917A (zh) * | 2021-10-29 | 2022-02-18 | 安徽省恒泰动力科技有限公司 | 应用于汽车发动机缸体的铝合金及其制备方法 |
CN114293077B (zh) * | 2021-12-29 | 2022-09-30 | 北京理工大学 | 一种用于航空航天结构件的高强铝铜合金及制备方法 |
CN116005022B (zh) * | 2023-02-08 | 2024-06-07 | 内蒙古蒙泰集团有限公司 | 一种高性能铸造铝硅合金及其制备方法 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
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US165A (en) * | 1837-04-17 | Mode of propelling boats ost castals or rivers | ||
GB516423A (en) * | 1937-04-30 | 1940-01-02 | Edgar Hutton Dix Jr | Improvements in or relating to the heat treatment of aluminium base alloys |
US3857165A (en) * | 1973-05-04 | 1974-12-31 | Aluminum Co Of America | Welding aluminum |
US4610733A (en) * | 1984-12-18 | 1986-09-09 | Aluminum Company Of America | High strength weldable aluminum base alloy product and method of making same |
JPH0759731B2 (ja) * | 1986-12-10 | 1995-06-28 | 石川島播磨重工業株式会社 | 鋳造用A▲l▼−Cu−Mg系高力アルミニウム合金及びその製造方法 |
FR2690927B1 (fr) * | 1992-05-06 | 1995-06-16 | Pechiney Aluminium | Alliages de moulage a base d'aluminium ayant une bonne resistance au fluage a chaud. |
JPH06262719A (ja) * | 1993-03-11 | 1994-09-20 | Nippon Steel Corp | 成形加工性、耐食性および焼付硬化性に優れたアルミニウム合金合わせ板 |
JPH0754088A (ja) * | 1993-08-13 | 1995-02-28 | Nippon Steel Corp | 成形加工性,耐食性および焼付硬化性に優れたアルミニウム合金合わせ板 |
JPH1017975A (ja) * | 1996-06-27 | 1998-01-20 | Kyushu Mitsui Alum Kogyo Kk | 鋳物用アルミニウム合金 |
JPH11302764A (ja) * | 1998-04-17 | 1999-11-02 | Kobe Steel Ltd | 高温特性に優れたアルミニウム合金 |
US6368427B1 (en) * | 1999-09-10 | 2002-04-09 | Geoffrey K. Sigworth | Method for grain refinement of high strength aluminum casting alloys |
CN1112455C (zh) * | 2001-07-26 | 2003-06-25 | 华南理工大学 | 高强韧和低热裂倾向的铸造铝基合金材料 |
US20070102071A1 (en) * | 2005-11-09 | 2007-05-10 | Bac Of Virginia, Llc | High strength, high toughness, weldable, ballistic quality, castable aluminum alloy, heat treatment for same and articles produced from same |
US20080041499A1 (en) * | 2006-08-16 | 2008-02-21 | Alotech Ltd. Llc | Solidification microstructure of aggregate molded shaped castings |
-
2009
- 2009-12-22 FR FR0906218A patent/FR2954355B1/fr not_active Expired - Fee Related
-
2010
- 2010-12-07 PL PL10799072T patent/PL2516687T3/pl unknown
- 2010-12-07 ES ES10799072.3T patent/ES2601809T3/es active Active
- 2010-12-07 KR KR1020127019244A patent/KR101757013B1/ko active IP Right Grant
- 2010-12-07 JP JP2012545367A patent/JP5758402B2/ja not_active Expired - Fee Related
- 2010-12-07 EP EP10799072.3A patent/EP2516687B1/fr active Active
- 2010-12-07 US US13/516,799 patent/US20120258010A1/en not_active Abandoned
- 2010-12-07 CA CA2812236A patent/CA2812236C/fr active Active
- 2010-12-07 MX MX2012006988A patent/MX2012006988A/es active IP Right Grant
- 2010-12-07 BR BR112012016917A patent/BR112012016917A2/pt not_active Application Discontinuation
- 2010-12-07 WO PCT/FR2010/000812 patent/WO2011083209A1/fr active Application Filing
Non-Patent Citations (1)
Title |
---|
See references of WO2011083209A1 * |
Also Published As
Publication number | Publication date |
---|---|
FR2954355A1 (fr) | 2011-06-24 |
KR20120114316A (ko) | 2012-10-16 |
BR112012016917A2 (pt) | 2016-04-12 |
WO2011083209A1 (fr) | 2011-07-14 |
CA2812236C (fr) | 2018-03-27 |
KR101757013B1 (ko) | 2017-07-11 |
PL2516687T3 (pl) | 2017-07-31 |
ES2601809T3 (es) | 2017-02-16 |
MX2012006988A (es) | 2012-07-03 |
US20120258010A1 (en) | 2012-10-11 |
JP2013515169A (ja) | 2013-05-02 |
CA2812236A1 (fr) | 2011-07-14 |
FR2954355B1 (fr) | 2012-02-24 |
JP5758402B2 (ja) | 2015-08-05 |
EP2516687B1 (fr) | 2016-08-10 |
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