EP2450463B1 - Alliage d'aluminium - Google Patents

Alliage d'aluminium Download PDF

Info

Publication number
EP2450463B1
EP2450463B1 EP20110165256 EP11165256A EP2450463B1 EP 2450463 B1 EP2450463 B1 EP 2450463B1 EP 20110165256 EP20110165256 EP 20110165256 EP 11165256 A EP11165256 A EP 11165256A EP 2450463 B1 EP2450463 B1 EP 2450463B1
Authority
EP
European Patent Office
Prior art keywords
alloy
aluminium alloy
alloy according
alloys
aluminum
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.)
Active
Application number
EP20110165256
Other languages
German (de)
English (en)
Other versions
EP2450463A2 (fr
EP2450463A3 (fr
Inventor
Georg Dambauer
Peter Schumacher
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.)
Voecklabrucker Metallgiesserei Dambauer GmbH
Original Assignee
Vocklabrucker Metallgiesserei Dambauer GmbH
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 Vocklabrucker Metallgiesserei Dambauer GmbH filed Critical Vocklabrucker Metallgiesserei Dambauer GmbH
Publication of EP2450463A2 publication Critical patent/EP2450463A2/fr
Publication of EP2450463A3 publication Critical patent/EP2450463A3/fr
Application granted granted Critical
Publication of EP2450463B1 publication Critical patent/EP2450463B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent

Definitions

  • steels or cast iron have the advantage of very high strength and are also cheap base materials.
  • a disadvantage of steels or cast iron, however, is that a casting process is usually expensive, corrosion resistance can be low and, in principle, a higher production cost is given in comparison with aluminum alloys.
  • steels and cast iron also have a higher density, which adversely affects a weight of a vehicle component and is often undesirable in view of a comparatively higher fuel consumption.
  • alloys of the aluminum-silicon-magnesium alloy system are easy to cast, are relatively easy to machine mechanically and are generally resistant to corrosion, but often have low strength. Alloys of the aluminum-copper-titanium alloy system can achieve a high theoretical strength, but are often not resistant to corrosion and, as a rule, poorly cast.
  • EP 1 215 295 A1 discloses an aluminum casting alloy with 5 to 10% silicon.
  • EP 1136 581 discloses an aluminum alloy with 1.5-2.2 Fe.
  • alloys containing 7 to 17% by weight and up to 0.7% by weight of magnesium or wrought alloys containing less than 1% by weight of silicon and less than 1% by weight of magnesium are frequently used, depending on the component and component geometry.
  • alloys with the designations AlSi7Mg0.6 or AC72 or AlSi0.5Mg or AC04 are used for the production of vehicle components.
  • the AlSi7Mg0.6 casting alloy which consists essentially of about 7% silicon by weight, about 0.6% magnesium by weight, balance aluminum, has high strength, but an elongation at break is too low for some applications. In addition, points this alloy has only low heat resistance.
  • the wrought AlSi0.5Mg alloy which is sometimes used as a casting alloy and consists essentially of about 0.5 weight percent silicon, about 0.5 weight percent magnesium, balance aluminum, on the other hand, has a high elongation at break, but at the expense of strength , which is low and therefore unsatisfactory for many purposes.
  • the object of the invention is to provide an aluminum alloy, which has a high strength with high elongation at break and good heat resistance, without a corrosion resistance is insufficient.
  • an aluminum alloy containing (by weight) 0.3 to 1.5% cobalt 1.0 up to 2.5% nickel more than 0 up to 1.5% magnesium more than 0 up to 1.5% silicon optionally more than 0 up to 1.0% silver optionally more than 0 up to 0.20% titanium and / or boron optionally more than 0 up to 0.003% beryllium Remaining aluminum and production-related impurities, with a maximum iron content of up to 0.5%.
  • an aluminum alloy according to the invention has a high strength combined with a high elongation at break, a high heat resistance of the alloy and, moreover, that the alloy is extremely resistant to corrosion.
  • cobalt dissolves iron present in the aluminum in formed intermetallic cobalt-aluminum phases. This leads to a good ductility of the aluminum alloy because no or only small amounts of acicular aluminum-iron phases are present.
  • cobalt contributes to the increase in strength.
  • Cobalt is mandatory, in concentrations of 0.3 up to 1.5%. It is preferably provided that a cobalt content is 0.30 to 0.80%, particularly preferably 0.40 to 0.60%, in particular 0.45 to 0.55%.
  • the aluminum alloy according to the invention further contains nickel as a mandatory constituent, with a nickel content basically being 1.0 to 2.5%, but preferably being in a range of 1.0 to 2.0%.
  • Nickel contributes to increasing the strength of the aluminum alloy at both room temperature and high temperature, that is at more than 200 ° C, by forming an intermetallic aluminum-nickel phase.
  • a nickel content is 1.2 to 1.6%, in particular 1.4 to 1.5%.
  • Magnesium is mandatory in an aluminum alloy according to the invention with a content of more than 0 up to 1.5%.
  • Magnesium, in conjunction with the silicon also provided, serves to increase the strength in the heat-treated state, wherein a content of magnesium is oriented to a maximum solubility at an annealing temperature which is generally in the range of about 570 ° C. It is favorable if a magnesium content is 0.8 to 1.2%, in particular 1.0 to 1.1%.
  • Silicon is provided at levels of greater than 0 to 1.5%.
  • a content of silicon is to be considered in connection with a content of magnesium, so that the desired strength increase is achieved in the heat-treated state.
  • a silicon content is therefore tuned to a magnesium content, however, with respect to magnesium, an excess of silicon is used.
  • an excess of silicon is provided in the amount of about one-fourth of the iron content of the alloy in order to fully exploit the precipitation potential by the excess silicon or to prevent activity reduction by the existing iron, which is usually up to 0.2%, in particular 0.1 to 0.2%, and is introduced as an impurity of the aluminum used in the alloy.
  • a content of iron can be up to 0.5%. It is expedient if the aluminum alloy contains 0.20 to 0.80%, in particular 0.55 to 0.70%, silicon, in each case based on the preferred magnesium contents given above.
  • Another component which may be provided in an aluminum alloy according to the invention is silver, in a content of more than 0 up to 1.0%.
  • silver in comparison with copper as an alloying element, silver proves to be better in terms of corrosion resistance. It is favorable if a silver content is 0.05 to 0.70%, in particular 0.10 to 0.55%.
  • an aluminum alloy according to the invention may optionally also contain titanium and / or boron and also beryllium.
  • a titanium and / or boron content may be up to 0.20% in total, but is preferably in the range of 0.001 to 0.15%, more preferably in the range of 0.001 to less than 0.02%.
  • Titanium and boron act as grain refining elements and can be added in the production of the aluminum alloy, for example by a master alloy of the type AlTi5B1, which master alloy 5 weight percent titanium, 1 weight percent boron, balance aluminum.
  • Beryllium serves to suppress as far as possible the evaporation of magnesium during the production of an aluminum alloy.
  • a beryllium content can be up to 0.003%.
  • the alloy according to the invention is advantageously substantially copper-free and has a copper content of less than 0.005%, since copper can lead to disadvantageous, low-melting phases.
  • the reference alloys AlSi7Mg0,6 or AC72 and AlSi0.5Mg or AC04 were assumed, which have a high strength and a high elongation at break.
  • target criteria no or only small proportions of below the eutectic melting temperature melting phases, high eutectic temperatures and taking advantage of a full Mg 2 Si precipitation hardening were specified.
  • the starting point for the comparative investigations was the binary Al-Mg 2 Si cut in the ternary phase system aluminum-silicon-magnesium, since the eutectic temperature has a maximum in this range.
  • Four experimental alloys were defined in the hypoeutectic region.
  • trial alloys were defined which additionally contained cobalt or both cobalt and nickel.
  • the chemical compositions of the trial alloys are shown in Table 1 below.
  • Table 1 - chemical compositions of trial alloys attempt Composition (in weight percent) T6 heat treatment mg Si Co Ni al A1 1.1 0.65 0 0 rest No A2 1.1 0.65 0 0 rest Yes A3 1.1 0.65 0.45 0 rest No A4 1.1 0.65 0.45 0 rest Yes A5 1.1 0.65 0.45 1.45 rest No A6 1.1 0.65 0.45 1.45 rest Yes B1 3.7 2.1 0 0 rest No B2 3.7 2.1 0 0 rest Yes B3 3.7 2.1 0.45 0 rest No B4 3.7 2.1 0.45 0 rest Yes B5 3.7 2.1 0.45 1.45 rest No B6 3.7 2.1 0.45 1.45 rest Yes C1 6.2 3.6 0 0 rest No C2 6.2 3.6 0 0 rest Yes C3 6.2 3.6 0.45 0 rest No C4 6.2 3.6 0.45 0 rest Yes C5 6.2 3.6 0.45 1.45 rest No C6 6.2 3.6 0.45 1.45 rest Yes D1 8.8 5.1 0 0
  • Fig. 1 to 4 are mechanical property values of alloys, optionally after the T6 heat treatment as described above, for the alloys shown in Table 1, wherein Fig. 1 the tensile strengths R m shows, Fig. 2 the yield strengths R p0,2 , Fig. 3 the Brinell hardnesses and Fig. 4 finally, the elongations at break A 5 .
  • the lines 1 to 6 in Fig. 1 to 4 connect in each case those values which were obtained for the experiments A1, B1, C1, D1 to A6, B6, C6, D6, ie the numerically identically marked alloys.
  • Fig. 6 is a microsection of an alloy shown in Experiment A2. As can be seen, one recognizes a pure mixed crystal structure and occasionally iron-rich needles.
  • Fig. 7 is a microsection of an alloy shown in experiment A6. It is compared with Fig. 6 recognizable that changes the structure by adding cobalt and nickel. Cobalt- and / or nickel-rich phases form at the grain boundaries and therefore give the microstructure a little more stability, which can also be understood on the basis of the mechanical properties already discussed. Iron-rich precipitates in the form of oblong needles are unlike Fig. 6 no longer present, since iron dissolves in the cobalt-rich phase. This could be verified by scanning electron microscopy.
  • a major advantage of the alloys according to experiments A5 and A6, respectively, is that higher annealing temperatures of up to about 570 ° C can be used instead of the usual annealing temperatures of about 535 ° C for standard alloys such as AC72. Due to the higher annealing temperatures more precipitation-relevant elements can be solved in mixed crystal, which leads to an increase in the achievable maximum strength. This is in Fig. 8 illustrated.
  • Fig. 9 are corrosion measurements on an alloy A6Ag according to test A6, which additionally contained 0.45% silver, compared with a reference alloy AlSi7Mg0,6 or AC72 shown.
  • sample bodies were introduced into a test solution (0.6 g / l NaCl, diluted 1:10 in borate buffer at a pH of about 6.4) and subjected to a voltage.
  • As counter electrode was a Platinum electrode used.
  • the corrosion behavior is comparable, but the alloy A6Ag has advantages in the passivation range. That is, this alloy has lower corrosion rates for an existing surface defect than an AlSi7Mg0.6 reference alloy.
  • An alloy according to the invention has, as in Fig. 10 is apparent, a globulitic structure on. Such a globulitic structure is favorable in terms of dynamic properties of an alloy.
  • a main field of application of an alloy according to experiment A5 or A6 is in particular an application for an engine component, for example as a material for a cylinder head.
  • the alloy was tested A5 compared to a common cylinder head alloy, namely AlSi7Mg0.3Cu, containing about 7 weight percent silicon, about 0.3 weight percent magnesium, about 0.5 weight percent copper, balance aluminum, as reference alloy. It was found that an alloy according to experiment A5, which was subjected to a T6 heat treatment (outsourced to hardness maximum) or a T7 heat treatment (outsourced for 500 hours at 225 ° C), less in strength at elevated temperature, which was Fig. 11 to 13 for the T7 heat treatment. An alloy A5Ag according to experiment A5, but additionally with 0.45% silver, gave even better values in terms of heat resistance.
  • an alloy according to Experiment A6 which additionally contained 0.45% silver, exhibits better properties at higher temperatures compared to a conventional AlSi7Mg0.3Cu cylinder head alloy, and thus also lends more suitability for use purposes because the time-stability line has a larger slope, as shown in Table 2.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Soft Magnetic Materials (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Fuel-Injection Apparatus (AREA)
  • Conductive Materials (AREA)

Claims (16)

  1. Alliage d'aluminium, contenant (en pourcentages en poids)
    de 0,3 à 1,5 % de cobalt,
    de 1,0 à 2,5 % de nickel,
    de plus de 0 à 1,5 % de magnésium,
    de plus de 0 à 1,5 % de silicium,
    en option, de plus de 0 à 1,0 % d'argent,
    en option, de plus de 0 à 0,20 % de titane et/ou de bore, en option, de plus de 0 à 0,003 % de béryllium
    un reste d'aluminium et des impuretés dues à la fabrication, une teneur en fer s'élevant au maximum à jusqu'à 0,5 %.
  2. Alliage d'aluminium selon la revendication 1, contenant de 0,30 à 0,80 % de cobalt.
  3. Alliage d'aluminium selon la revendication 1, contenant de 0,40 à 0,60 % de cobalt.
  4. Alliage d'aluminium selon la revendication 1, contenant de 045 à 0,55 % de cobalt.
  5. Alliage d'aluminium selon la revendication 1, contenant de 1,0 à 2,0 % de nickel.
  6. Alliage d'aluminium selon la revendication 1, contenant de 1,2 à 1,6 % de nickel.
  7. Alliage d'aluminium selon la revendication 1, contenant de 1,4 à 1,5 % de nickel.
  8. Alliage d'aluminium selon la revendication 1, contenant de 0,80 à 1,20 % de magnésium.
  9. Alliage d'aluminium selon la revendication 1, contenant de de 1,0 à 1,1 % de magnésium.
  10. Alliage d'aluminium selon la revendication 1, contenant de 0,20 à 0,80 % de silicium.
  11. Alliage d'aluminium selon la revendication 1, contenant de 0,55 à 0,70 % de silicium.
  12. Alliage d'aluminium selon la revendication 1, contenant de 0,05 à 0,70 % d'argent.
  13. Alliage d'aluminium selon la revendication 1, contenant de 0,10 à 0,55 % d'argent.
  14. Alliage d'aluminium selon la revendication 1, contenant de 0,001 à 0,15 % de titane et/ou de bore.
  15. Alliage d'aluminium selon la revendication 1, contenant de 0,001 à moins de 0,02 % de titane et/ou de bore.
  16. Alliage d'aluminium selon la revendication 1 qui est conçu en étant sensiblement exempt de cuivre.
EP20110165256 2010-07-02 2011-05-09 Alliage d'aluminium Active EP2450463B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
AT11222010A AT509343B1 (de) 2010-07-02 2010-07-02 Aluminiumlegierung

Publications (3)

Publication Number Publication Date
EP2450463A2 EP2450463A2 (fr) 2012-05-09
EP2450463A3 EP2450463A3 (fr) 2013-05-29
EP2450463B1 true EP2450463B1 (fr) 2014-08-27

Family

ID=44352398

Family Applications (1)

Application Number Title Priority Date Filing Date
EP20110165256 Active EP2450463B1 (fr) 2010-07-02 2011-05-09 Alliage d'aluminium

Country Status (2)

Country Link
EP (1) EP2450463B1 (fr)
AT (1) AT509343B1 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN118064771B (zh) * 2024-04-24 2024-07-09 湖南卓创精材科技股份有限公司 一种提高反射率的铝镁合金材料、制备方法和应用

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2286886A1 (fr) * 1974-10-04 1976-04-30 Pechiney Aluminium Conducteurs electriques en alliages d'aluminium et procedes d'obtention
ATE188259T1 (de) * 1996-04-10 2000-01-15 Alusuisse Lonza Services Ag Bauteil
EP1136581B1 (fr) * 2000-03-23 2005-11-02 Furukawa-Sky Aluminum Corp. Procédé de fabrication de Matériau pour ailettes d'échangeur de chaleur pour brassage
JP3504917B2 (ja) * 2000-10-11 2004-03-08 日本碍子株式会社 自動車エンジンの可動部品およびケーシング部材用のアルミニウム−ベリリウム−シリコン系合金
DE10062547A1 (de) * 2000-12-15 2002-06-20 Daimler Chrysler Ag Aushärtbare Aluminium-Gusslegierung und Bauteil
AT412726B (de) * 2003-11-10 2005-06-27 Arc Leichtmetallkompetenzzentrum Ranshofen Gmbh Aluminiumlegierung, bauteil aus dieser und verfahren zur herstellung des bauteiles
DE102005037738B4 (de) * 2005-08-10 2009-03-05 Daimler Ag Aluminium-Gusslegierung mit hoher dynamischer Festigkeit und Wärmeleitfähigkeit
CN101121255A (zh) * 2006-09-07 2008-02-13 广东科信达科技有限公司 一种铝基金属结合剂金刚石工具及其制备方法

Also Published As

Publication number Publication date
AT509343B1 (de) 2011-08-15
AT509343A4 (de) 2011-08-15
EP2450463A2 (fr) 2012-05-09
EP2450463A3 (fr) 2013-05-29

Similar Documents

Publication Publication Date Title
DE102016118729B4 (de) Aluminiumlegierung, geeignet für Hochdruckgießen
EP3314031B1 (fr) Bande almg facilement déformable et très résistante et son procédé de fabrication
EP2653579B1 (fr) Alliage d'aluminium
DE60123065T2 (de) Titanlegierung und wärmebehandlungsverfahren für grossdimensionale, halbfertige materialien aus dieser legierung
EP2735621B1 (fr) Alliage à coulée sous pression en aluminium
DE69325804T2 (de) Hochfeste-al-li-legierung mit niedriger dichte und hoher zähigkeit bei hohen temperaturen
DE112008000587T5 (de) Schmiedestücke aus einer Aluminiumlegierung und Verfahren zu deren Herstellung
EP3176275B2 (fr) Alliage de coulée sous pression de silicium/aluminium. procédé de fabrication d'un composant coulé sous pression en alliage et composants de carrosserie comprenant un tel composant coulé sous pression
DE102016219711B4 (de) Aluminiumlegierung zum Druckgießen und Verfahren zu ihrer Hitzebehandlung
DE112016005830B4 (de) Metalldichtung und Verfahren zu ihrer Herstellung
EP2013371A2 (fr) Alliage de cuivre multi-matière et son utilisation
EP3024958B1 (fr) Alliage d'aluminium de fondèrie résistant a haute temperature et pièce de fonderie pour moteurs a combustion interne utilisant cet alliage
WO2005045080A1 (fr) Alliage d'alminium
EP1589122B1 (fr) Revêtement comprenant des phases NiAl-beta
DE1483228B2 (de) Aluminiumlegierung mit hoher zeitstandfestigkeit
EP2703508B1 (fr) Alliages d'aluminium résistant à la corrosion intercristalline
DE10231437A1 (de) Geschmiedetes Aluminium-Magnesium-Legierungserzeugnis
EP2450463B1 (fr) Alliage d'aluminium
EP1748088B1 (fr) Procédé de fabrication de produit semi-fini ou de composant pour des applications de châssis ou de structure automobiles
DE102006027844B4 (de) Kupferlegierung auf der Basis von Kupfer und Zinn
EP1229141A1 (fr) Alliage d'aluminium de fonderie
EP3670691B1 (fr) Alliage de magnesium et son procédé de fabrication
EP3781719B1 (fr) Alliage de cuivre, zinc, nickel et manganèse
EP3992319A1 (fr) Produit d'alliage fabriqué à partir d'alliage de cuivre-zinc sans plomb et son procédé de fabrication
DE1292412B (de) Verfahren zur Waermebehandlung von Titanlegierungen

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

AK Designated contracting states

Kind code of ref document: A2

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

AX Request for extension of the european patent

Extension state: BA ME

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: VOECKLABRUCKER METALLGIESSEREI DAMBAUER GMBH

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A3

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

AX Request for extension of the european patent

Extension state: BA ME

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 21/08 20060101ALI20130419BHEP

Ipc: C22C 21/02 20060101AFI20130419BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

17P Request for examination filed

Effective date: 20130924

RBV Designated contracting states (corrected)

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

INTG Intention to grant announced

Effective date: 20131104

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20140415

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

RIN1 Information on inventor provided before grant (corrected)

Inventor name: SCHUMACHER, PETER

Inventor name: DAMBAUER, GEORG

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 684592

Country of ref document: AT

Kind code of ref document: T

Effective date: 20140915

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502011004170

Country of ref document: DE

Effective date: 20141009

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: KELLER AND PARTNER PATENTANWAELTE AG, CH

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20140827

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

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: 20141229

Ref country code: SE

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: 20140827

Ref country code: NO

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: 20141127

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: 20141128

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: 20140827

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: 20141127

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: 20140827

Ref country code: ES

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: 20140827

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

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: 20140827

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: 20140827

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: 20140827

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: 20141227

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: 20140827

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20140827

REG Reference to a national code

Ref country code: CH

Ref legal event code: PCAR

Free format text: NEW ADDRESS: EIGERSTRASSE 2 POSTFACH, 3000 BERN 14 (CH)

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

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: 20140827

Ref country code: RO

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: 20140827

Ref country code: CZ

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: 20140827

Ref country code: IT

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: 20140827

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: 20140827

Ref country code: SK

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: 20140827

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502011004170

Country of ref document: DE

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

Ref country code: PL

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: 20140827

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: 20150528

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: 20140827

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: 20140827

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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

Ref country code: IE

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

Effective date: 20150509

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 6

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: 20140827

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: 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: 20140827

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: 20110509

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 684592

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160509

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

Ref country code: TR

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: 20140827

Ref country code: AT

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

Effective date: 20160509

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: 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: 20140827

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: 20140827

REG Reference to a national code

Ref country code: CH

Ref legal event code: PFA

Owner name: VOECKLABRUCKER METALLGIESSEREI DAMBAUER GMBH, AT

Free format text: FORMER OWNER: VOECKLABRUCKER METALLGIESSEREI DAMBAUER GMBH, AT

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

Ref country code: LU

Payment date: 20230519

Year of fee payment: 13

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

Ref country code: FR

Payment date: 20230526

Year of fee payment: 13

Ref country code: DE

Payment date: 20230519

Year of fee payment: 13

Ref country code: CH

Payment date: 20230605

Year of fee payment: 13

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

Ref country code: BE

Payment date: 20230519

Year of fee payment: 13

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

Ref country code: GB

Payment date: 20230524

Year of fee payment: 13