EP2516687A1 - Formteil aus kupferaluminiumlegierung mit hoher mechanischer festigkeit und hoher kriechbeständigkeit - Google Patents

Formteil aus kupferaluminiumlegierung mit hoher mechanischer festigkeit und hoher kriechbeständigkeit

Info

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
Application number
EP10799072A
Other languages
English (en)
French (fr)
Other versions
EP2516687B1 (de
Inventor
Michel Garat
James Frederick Major
Danny Jean
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.)
Rio Tinto Alcan International Ltd
Original Assignee
Rio Tinto Alcan International Ltd
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 Rio Tinto Alcan International Ltd filed Critical Rio Tinto Alcan International Ltd
Priority to PL10799072T priority Critical patent/PL2516687T3/pl
Publication of EP2516687A1 publication Critical patent/EP2516687A1/de
Application granted granted Critical
Publication of EP2516687B1 publication Critical patent/EP2516687B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/12Alloys based on aluminium with copper as the next major constituent
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002Castings of light metals
    • B22D21/007Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/12Alloys based on aluminium with copper as the next major constituent
    • C22C21/14Alloys based on aluminium with copper as the next major constituent with silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/12Alloys based on aluminium with copper as the next major constituent
    • C22C21/16Alloys based on aluminium with copper as the next major constituent with magnesium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057Changing 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)
EP10799072.3A 2009-12-22 2010-12-07 Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen Active EP2516687B1 (de)

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 (de) 2012-10-31
EP2516687B1 EP2516687B1 (de) 2016-08-10

Family

ID=42122814

Family Applications (1)

Application Number Title Priority Date Filing Date
EP10799072.3A Active EP2516687B1 (de) 2009-12-22 2010-12-07 Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen

Country Status (11)

Country Link
US (1) US20120258010A1 (de)
EP (1) EP2516687B1 (de)
JP (1) JP5758402B2 (de)
KR (1) KR101757013B1 (de)
BR (1) BR112012016917A2 (de)
CA (1) CA2812236C (de)
ES (1) ES2601809T3 (de)
FR (1) FR2954355B1 (de)
MX (1) MX2012006988A (de)
PL (1) PL2516687T3 (de)
WO (1) WO2011083209A1 (de)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
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)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2011083209A1 *

Also Published As

Publication number Publication date
CA2812236A1 (fr) 2011-07-14
CA2812236C (fr) 2018-03-27
FR2954355B1 (fr) 2012-02-24
PL2516687T3 (pl) 2017-07-31
ES2601809T3 (es) 2017-02-16
US20120258010A1 (en) 2012-10-11
KR20120114316A (ko) 2012-10-16
BR112012016917A2 (pt) 2016-04-12
EP2516687B1 (de) 2016-08-10
JP2013515169A (ja) 2013-05-02
WO2011083209A1 (fr) 2011-07-14
JP5758402B2 (ja) 2015-08-05
MX2012006988A (es) 2012-07-03
KR101757013B1 (ko) 2017-07-11
FR2954355A1 (fr) 2011-06-24

Similar Documents

Publication Publication Date Title
EP2516687B1 (de) Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen
CA2489349C (fr) Piece moulee en alliage d'aluminium a haute resistance a chaud
WO2010012875A1 (fr) Pièce moulée en alliage d'aluminium à hautes résistances à la fatigue et au fluage à chaud
FR2857378A1 (fr) Piece moulee en alliage d'aluminium a haute resistance a chaud
FR2818288A1 (fr) PROCEDE DE FABRICATION D'UNE PIECE DE SECURITE EN ALLIAGE Al-Si
FR2489846A1 (fr) Alliages d'aluminium de grande resistance mecanique et a l'usure et leur procede de fabrication
JP2005264301A (ja) 鋳造アルミニウム合金とアルミニウム合金鋳物およびその製造方法
EP3011068A1 (de) Bogenrückenstrukturelement aus einer aluminium-kupfer-lithium-legierung
WO2014162069A1 (fr) Tôles minces en alliage d'aluminium-cuivre-lithium pour la fabrication de fuselages d'avion
CN109280829B (zh) 一种高强度铸造Mg-Zn-Cu-Zr合金及其制备方法
WO2000043559A1 (fr) Produit en alliage aluminium-silicium hypereutectique pour mise en forme a l'etat semi-solide
EP1815036A2 (de) Aluminiumlegierung für komponenten mit hoher mechanischer festigkeit bei heissverfahren
JP4390762B2 (ja) デファレンシャルギアケース及びその製造方法
JPH11246925A (ja) 高靱性アルミニウム合金鋳物およびその製造方法
JP5607960B2 (ja) 疲労強度特性に優れた耐熱マグネシウム合金およびエンジン用耐熱部品
FR2859484A1 (fr) Piece moulee en alliage d'aluminium a haute resistance a chaud
EP3250722B1 (de) Verfahren zur gewinnung eines teils mit siliciumarmer aluminiumlegierung
FR2857376A1 (fr) ALLIAGE DE AlMgSi
JP5482627B2 (ja) 鋳造用アルミニウム合金及び鋳造用アルミニウム合金製鋳物
BE466004A (de)
BE617167A (de)
BE466003A (de)

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: 20120614

AK Designated contracting states

Kind code of ref document: A1

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

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20150804

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20160303

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

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

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 819131

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160815

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: FRENCH

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602010035443

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: RO

Ref legal event code: EPE

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

Ref country code: NO

Ref legal event code: T2

Effective date: 20160810

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161210

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2601809

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20170216

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161111

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161212

REG Reference to a national code

Ref country code: SK

Ref legal event code: T3

Ref document number: E 22501

Country of ref document: SK

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602010035443

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161110

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20170511

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20161207

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20161231

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20161231

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 8

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20101207

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160810

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 819131

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160810

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SK

Payment date: 20211124

Year of fee payment: 12

Ref country code: TR

Payment date: 20211207

Year of fee payment: 12

Ref country code: SE

Payment date: 20211126

Year of fee payment: 12

Ref country code: RO

Payment date: 20211203

Year of fee payment: 12

Ref country code: CZ

Payment date: 20211125

Year of fee payment: 12

Ref country code: AT

Payment date: 20211129

Year of fee payment: 12

Ref country code: GB

Payment date: 20211118

Year of fee payment: 12

Ref country code: NO

Payment date: 20211209

Year of fee payment: 12

Ref country code: IE

Payment date: 20211123

Year of fee payment: 12

Ref country code: FR

Payment date: 20211125

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20211129

Year of fee payment: 12

Ref country code: BE

Payment date: 20211203

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: PL

Payment date: 20211129

Year of fee payment: 12

Ref country code: NL

Payment date: 20211203

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20220104

Year of fee payment: 12

REG Reference to a national code

Ref country code: NO

Ref legal event code: MMEP

REG Reference to a national code

Ref country code: SK

Ref legal event code: MM4A

Ref document number: E 22501

Country of ref document: SK

Effective date: 20221207

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

Ref country code: CZ

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20230101

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 819131

Country of ref document: AT

Kind code of ref document: T

Effective date: 20221207

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20221207

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20221231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20230101

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221208

Ref country code: NO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221231

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221231

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221231

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20240126

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221207

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20231114

Year of fee payment: 14

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221208

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221208