EP2617855B1 - Niedrig legierter Stahl und damit hergestellte Bauteile - Google Patents
Niedrig legierter Stahl und damit hergestellte Bauteile Download PDFInfo
- Publication number
- EP2617855B1 EP2617855B1 EP12198668.1A EP12198668A EP2617855B1 EP 2617855 B1 EP2617855 B1 EP 2617855B1 EP 12198668 A EP12198668 A EP 12198668A EP 2617855 B1 EP2617855 B1 EP 2617855B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- parts
- steels
- components
- boron
- 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.)
- Not-in-force
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
Definitions
- the invention relates to a low alloy steel with excellent processability, scale resistance and components made therefrom.
- Low alloy refers to steels in which no alloying element exceeds an average content of 5 percent by mass.
- Silicon steel of various composition is from the GB 2173216A known.
- the EP1961832A1 and the US 5846344A reveal highly elastic steels with one Carbon content up to 0.6%; and Si up to 2.5% and possibly some B - but they use expensive special elements such as Mn, Nb and V to obtain the desired elasticity.
- the well-known 42CrMoS4 IM steel has a composition of Chemical composition (% by weight) min Max C 0.38 0.45 Si 0.40 Mn 0.70 0.90 P 0,035 S 0,035 Cr 0.90 1.20 Not a word 0.15 0.30
- Carbon lowers the melting point and increases the hardness and tensile strength through the formation of Fe3C. In larger quantities it increased the brittleness and lowered the forging ability, weldability, elongation at break and notched impact strength. In particular, moldability is lowered when it is added in a large amount. Here, therefore, the addition must be low.
- Chromium lowers the critical cooling rate, increases wear resistance, heat resistance, scale resistance.
- the tensile strength is increased because chromium acts as a carbide former. From 12.2% by weight it increases the corrosion resistance (stainless steel), acts as a ferrite stabilizer. Unfortunately, it reduces impact energy and weldability, lowers heat and electrical conductivity. With chromium additives the best results of hardening or hardening are achieved.
- Molybdenum also increases hardenability and advantageously complements chromium.
- Mo improves the heat resistance as well as the tempering resistance, a property that is particularly important in tempering.
- Sulfur increases the machinability, but reduces the ductility and thus forgeability of the iron alloy.
- the well-known steel 42CrMo4 is extensively used. With the properties described, the materials are suitable for high and highest dynamic and static stability. Their application results from the required strength and toughness values, but always the dimensioning of the components must be taken into account.
- the mechanical workability of these steels, especially in hot and / or cold forming processes is excellent and they are therefore used extensively in vehicle construction, mechanical engineering, Oroßmotorenbau etc. For certain applications, however, they are not sufficiently resistant to scaling (thermally highly stressed parts) and do not have sufficient strength for lightweight steel components
- the required load increases the aluminum alloy used until then for cars is less and less grown.
- a two-part solution consisting of a heavy-duty piston upper part and the piston skirt.
- the material 42CrMo4 in tempered design is also frequently chosen.
- the strength of these components is between 870 and 1080 MPa.
- the heat resistance, alternating load resistance, thermal shock resistance and oxidation resistance of this tempering steel are just sufficient for the present conditions.
- the invention accordingly relates to low-alloy steel with the composition of claim 1.
- the steels according to the invention contain at least 92.00% by weight of iron, preferably at least 96.00% by weight of iron. It is favorable if impurities and unavoidable elements are present in concentrations of less than 0.10% by weight, preferably less than 0.05% by weight.
- a typical application is for components, in particular machine components, with a tensile strength of> 950-1250 [MPa], a yield strength of> 700 to about 770 [MPa]; an elongation at break> 10% and a scale resistance of about 600 ° C to about 650 ° C and more.
- Typical such components are engine components selected from the group consisting of pistons, also for internal combustion engines, crankshafts, connecting rods, steering parts, valve parts, conveyor belt parts, in particular for hot parts; but also power plant components; Fasteners for heat resistant areas, steam turbine parts, combustor parts for gas or oil burners; Exhaust systems and their parts.
- the properties of steels of the invention over known steels are 42CrMo4 42TBSi Tensile strength (Mpa) > 900 - 1100 1000-1200 Yield strength (Mpa) > 650 > 750 elongation > 12% > 10% scaling resistance up to 550 ° C up to approx. 650 ° C heat treatment QT QT workability: Good Good Reibschoir : Good analysis DIN EN 10083 DIN EN 10083 plus
- the costs for the steel according to the invention are approximately equal to those of 42CrMo4, but at the same time a considerable increase in the scale strength by 100-150 ° C. and more and yield strength occurs.
- the yield strength increases by about 100 MPa for the steels according to the invention, accompanied by a slight reduction in the elongation at break.
- the processing does not change and can be carried out with the usual tools and procedures.
- a typical steel according to the invention has a composition of: Chemical composition (% by weight) min Max C 0.38 0.45 Cr 0.9 1.2 Not a word 0 0.3 Mn 0.6 0.9 Ti 0.04 0.04 Si 4 4 B 0.005 0.005
- Titanium prevents intergranular corrosion due to TiC formation in iron alloys.
- the strong nitride former (titanium) serves u.a. to protect boron by reaction with nitrogen.
- titanium serves u.a. to protect boron by reaction with nitrogen.
- nitrogen is fixed with titanium, satisfactory hardenability occurs in the temperature range up to 1000 ° C when the steel contains about 5-20 ppm of boron.
- Ti is used to deoxidize the steel and to fix C and N as TiC and TiN, respectively.
- the Ti content must therefore be at least 0.02%.
- the upper limit of the Ti content is defined as 0.08%.
- Boron increases the yield strength and strength of the steel, even when added in the smallest amounts. It also acts as a neutron absorber and makes the steel suitable for nuclear power plant and similar applications.
- the addition of boron in an amount of up to 0.01% on austenitic steels also improves their high temperature resistance. Boron steels are high quality cold formed steels. The basic effect of boron in steel is shown in the improvement of hardenability, which is already evident at a very low concentration of 0.0010% boron. Even in the small amount up to 100 ppm, boron increases the hardenability more than other, more expensive elements that have to be used in much larger quantities
- An outstanding feature of boron steels is the improvement of hardenability through the addition of even minute amounts of boron between 3 and 15 ppm.
- the amount of boron is critical because an excessive amount of boron (> 30 ppm) can reduce toughness, lead to embrittlement and heat brittleness.
- the effect of boron on hardenability also depends on the amount of carbon in the steel, with the effect of boron increasing in inverse proportion to the percentage of carbon present.
- Boron may also be ineffective if its condition is altered by improper heat treatment. For example, a high austenitizing temperature must be avoided as well as temperature ranges in which certain boron precipitates occur.
- the hardenability of steel is largely due to the behavior of oxygen, carbon and nitrogen in steel. Boron reacts with oxygen to form bromide (B 2 O 3 ); with carbon to iron borcementite (Fe 3 (GB)) and iron boron carbide (Fe 23 (CB) 6 ) and with nitrogen to boron nitride (BN). Boron loss can be by oxygen.
- the hardenability of boron steel is also closely related to austenitic conditions and usually falls by heating above 1000 ° C. Boron steels must also be tempered at a lower temperature than other alloyed steels of the same hardenability.
- the steels according to the invention are used for many applications, such as wear-resistant material and as high-strength steel. Examples include punching tools, spades, knives, saw blades, safety supports in vehicles, etc.
- Boron steels are indicated when the base material meets the mechanical requirements (toughness, wear resistance, etc.), but the hardenability is insufficient for the intended section size. Instead of requiring a higher alloyed and thus expensive steel, a user may employ appropriate amounts of boron, thereby providing suitable hardenability.
- a 42TBSi cast steel billet is forged to a piston at 1150 ° C in a forging process.
- This piston thus prepared is used in a conventional manner as a combustion chamber for a gas engine. After a burning period of several months, no scaling of the steel surface of the bulb was found in the firing range / ignition range. By contrast, an identical piston made of 42CrMoS4 already showed clear signs of scaling after 70% of this time.
- a forged steel billet of conventional 42CrMo4 (Sample 4) and a steel billet of steel according to the invention (42CrMo4 + 4% Si + 0.04 wt% Ti and 0.005 wt% B) (Sample 6) were transferred to an electric air circulation furnace and at 700 ° C annealed in the oven for 5 h.
- the controlled circulating air atmosphere with normal air in the oven always ensured the same amount of oxygen.
- Two more samples of conventional 42CrMo4 (Sample 4) and the steel of the invention (Sample 6) were annealed in the same furnace under the same conditions but at 750 ° C for 5 hours.
- the measured steel billets each came from cast, forged blocks, forged down to 45 mm diameter.
- the upper one of the 42CrMo4 steel after annealing at 700 ° C and ground down by the same conditions Annealed steel alloy according to the invention shows that the scale layer in the Si steel according to the invention is considerably thinner (8 micrometers compared to 30 micrometers) than in the conventional 42CrMo4 steel without addition of silicon - the Si steel material according to the invention thus scales up much slower / less.
- Fig. 2 shows the same steel billets in a 5h annealing in the same convection oven at 750 ° C
- the upper sample is the 42 CrMo4 steel and a compared to the treatment at 700 ° C thickened scale layer of max. 44 micrometers has formed, while the steel according to the invention a thin scale layer of max. 5 micrometers shows.
- the silicon steel according to the invention is attacked oxidatively much less at elevated temperatures of oxygen than conventional low-alloyed CrMo4 steel.
- the steels of the invention thus achieve a scale strength that could previously be achieved only with expensive additives.
- Fig. 3 is a compilation of the properties of 42CrMo4 steels with silicon alloy up to about 4% depending on the silicon content and the temperature of the thermal aging graphically.
- the abscissa indicates the Si content in% by weight of a basic alloy 42CrMo4, while the left-hand ordinate indicates the tensile strength UTS in MPa. On the right ordinate the notched impact strength (KU) is indicated.
- the properties also depend on the tempering temperature (low tempering / high tempering).
- the high tempering temperature at about 0.5 wt.% Si was 680 ° C while the low tempering temperature was 630 ° C. With an addition of about 2.5 Si, the high tempering temperature was 730 ° C and the low tempering temperature was 680 ° C. It can be clearly seen that with increasing Si content - depending on the tempering temperature - the tensile strength increases, while constriction and impact strength decrease.
- a higher tempering temperature deteriorates the impact value and constriction RoFa; whereas the RoFa constriction at low silicon content is higher for tempered steel than at low tempered steel - this RoFa ratio of Steel tempered with low temperature compared to RoFa of steel tempered with higher temperature reverses with increasing Si content; while the impact strength at higher silicon content becomes almost independent of the tempering temperature.
- the tensile strength increases with increasing tempering temperature and increasing Si content.
- the invention thus also relates to machine components or components with a tensile strength of 1000 [MPa] and more for varying mechanical loads up to a temperature of 630 ° C, formed from a thermally tempered steel alloy according to the invention.
- the invention also relates to engine and / or drive components of vehicles.
- inventive low-alloy tempered steels are now used advantageously.
- Use of steel alloys having a composition equal to that of tempered steels of the aforesaid kind has proven useful for producing highly stressed machine components, with their fatigue and thermal resistance properties sufficient for mechanical cycling in the limit of the materials used.
- the description of the invention is merely exemplary and variations familiar to those skilled in the art are also within the scope of the invention as defined by the claims.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PL12198668T PL2617855T3 (pl) | 2012-01-19 | 2012-12-20 | Stal niskostopowa i wykonane z niej elementy konstrukcyjne |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102012100444 | 2012-01-19 | ||
DE102012111679A DE102012111679A1 (de) | 2012-01-19 | 2012-11-30 | Niedrig legierter Stahl und damit hergestellte Bauteile |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2617855A2 EP2617855A2 (de) | 2013-07-24 |
EP2617855A3 EP2617855A3 (de) | 2013-09-11 |
EP2617855B1 true EP2617855B1 (de) | 2016-09-28 |
Family
ID=58360410
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP12198668.1A Not-in-force EP2617855B1 (de) | 2012-01-19 | 2012-12-20 | Niedrig legierter Stahl und damit hergestellte Bauteile |
Country Status (6)
Country | Link |
---|---|
US (1) | US10041157B2 (es) |
EP (1) | EP2617855B1 (es) |
BR (1) | BR102013001355B1 (es) |
DE (1) | DE102012111679A1 (es) |
LT (1) | LT2617855T (es) |
MX (1) | MX356197B (es) |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102014010600A1 (de) | 2014-07-18 | 2016-01-21 | DST Defence Service Tracks GmbH | Legierung zur Herstellung eines dünnwandigen Stahlbauteils |
DE102015105448A1 (de) | 2015-04-09 | 2016-10-13 | Gesenkschmiede Schneider Gmbh | Legierter Stahl und damit hergestellte Bauteile |
EP3333277B1 (en) | 2015-08-05 | 2019-04-24 | Sidenor Investigación y Desarrollo, S.A. | High-strength low-alloy steel with high resistance to high-temperature oxidation |
CN109182650A (zh) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | 一种汽车曲轴用钢42CrMoH的生产方法 |
DE102022108997A1 (de) * | 2022-04-13 | 2023-10-19 | Ks Kolbenschmidt Gmbh | Kolbenrohling, kolben und verfahren |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE19549094A1 (de) * | 1995-10-17 | 1997-04-24 | Hyundai Motor Co Ltd | Hochfeste legierte Stahlzusammensetzung für Spiralfedern |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US1401925A (en) * | 1920-06-14 | 1921-12-27 | George W Sargent | Alloy steel |
CA1233644A (en) * | 1985-04-01 | 1988-03-08 | Glenn E. Hoffman | Method of producing ferro alloys |
JPS62112753A (ja) * | 1985-11-12 | 1987-05-23 | Toyota Motor Corp | 高強度鋳鋼製品の製造方法 |
JP2932943B2 (ja) * | 1993-11-04 | 1999-08-09 | 株式会社神戸製鋼所 | 高耐食性高強度ばね用鋼材 |
US5776267A (en) | 1995-10-27 | 1998-07-07 | Kabushiki Kaisha Kobe Seiko Sho | Spring steel with excellent resistance to hydrogen embrittlement and fatigue |
JP4044460B2 (ja) * | 2003-02-28 | 2008-02-06 | 大同特殊鋼株式会社 | 冷間成形ばね用鋼 |
WO2005106059A1 (ja) * | 2004-04-28 | 2005-11-10 | Jfe Steel Corporation | 機械構造用部品およびその製造方法 |
JP4027956B2 (ja) * | 2006-01-23 | 2007-12-26 | 株式会社神戸製鋼所 | 耐脆性破壊特性に優れた高強度ばね鋼およびその製造方法 |
KR100797895B1 (ko) * | 2006-12-22 | 2008-01-24 | 성진경 | 표면 (100) 면 형성 방법, 이를 이용한 무방향성 전기강판의 제조 방법 및 이를 이용하여 제조된 무방향성 전기강판 |
DE102007006875A1 (de) * | 2007-02-07 | 2008-08-14 | Benteler Stahl/Rohr Gmbh | Verwendung einer Stahllegierung als Werkstoff zur Herstellung von dynamisch belasteten Rohrbauteilen und Rohrbauteil |
JP4163239B1 (ja) * | 2007-05-25 | 2008-10-08 | 株式会社神戸製鋼所 | 疲労特性に優れた高清浄度ばね用鋼および高清浄度ばね |
EP2313535B8 (en) * | 2008-07-24 | 2021-09-29 | CRS Holdings, LLC | High strength, high toughness steel alloy |
JP5334769B2 (ja) * | 2009-09-10 | 2013-11-06 | 独立行政法人物質・材料研究機構 | 高強度ボルト |
JP5711539B2 (ja) * | 2011-01-06 | 2015-05-07 | 中央発條株式会社 | 腐食疲労強度に優れるばね |
-
2012
- 2012-11-30 DE DE102012111679A patent/DE102012111679A1/de not_active Withdrawn
- 2012-12-20 LT LTEP12198668.1T patent/LT2617855T/lt unknown
- 2012-12-20 EP EP12198668.1A patent/EP2617855B1/de not_active Not-in-force
-
2013
- 2013-01-16 MX MX2013000620A patent/MX356197B/es active IP Right Grant
- 2013-01-18 US US13/744,828 patent/US10041157B2/en not_active Expired - Fee Related
- 2013-01-18 BR BR102013001355-2A patent/BR102013001355B1/pt not_active IP Right Cessation
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE19549094A1 (de) * | 1995-10-17 | 1997-04-24 | Hyundai Motor Co Ltd | Hochfeste legierte Stahlzusammensetzung für Spiralfedern |
Also Published As
Publication number | Publication date |
---|---|
US10041157B2 (en) | 2018-08-07 |
BR102013001355A2 (pt) | 2014-12-02 |
US20130189146A1 (en) | 2013-07-25 |
BR102013001355B1 (pt) | 2019-02-26 |
DE102012111679A1 (de) | 2013-07-25 |
MX2013000620A (es) | 2013-07-18 |
EP2617855A2 (de) | 2013-07-24 |
MX356197B (es) | 2018-05-18 |
LT2617855T (lt) | 2017-03-27 |
EP2617855A3 (de) | 2013-09-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2446064B1 (de) | Verfahren zum herstellen eines warmpressgehärteten bauteils und verwendung eines stahlprodukts für die herstellung eines warmpressgehärteten bauteils | |
EP1905857B1 (de) | Hochfester Stahl und Verwendungen eines solchen Stahls | |
DE60021670T2 (de) | Verfahren zur Herstellung eines Werkzeugstahles sowie Werkzeug | |
EP2059623A1 (de) | Nichtrostender austenitischer stahlformguss, verfahren zu dessen herstellung, und seine verwendung | |
EP2617855B1 (de) | Niedrig legierter Stahl und damit hergestellte Bauteile | |
DE2621297A1 (de) | Hochleistungs-turbomaschinenlaufrad | |
DE1533239B1 (de) | Verwendung eines stahles fuer tellerventile | |
DE112019006482T5 (de) | Karbonitrierte lagerkomponente | |
EP2111475B1 (de) | Bauteile aus ultrahochkohlenstoffhaltigen stählen mit reduzierter dichte und hoher zunderbeständigkeit | |
DE60024495T2 (de) | Stahl mit ausgezeichneter Schmiedbarkeit und Bearbeitbarkeit | |
DE2830850B2 (de) | Verwendung eines Einsatzstahls | |
DE112016002489T5 (de) | Hitzebeständiger austenitischer gussstahl | |
DE112019006504T5 (de) | Stahlmaterial als ausgangsmaterial für karbonitrierte lagerkomponente | |
DE102015220299A1 (de) | Lagerstahl mit verbesserter Dauerhaltbarkeit und Verfahren zur Herstellung desselbigen | |
DE102008032024B4 (de) | Dichtereduzierte UHC-Stähle | |
DE10019042A1 (de) | Stickstofflegierter, sprühkompaktierter Stahl, Verfahren zu seiner Herstellung und Verbundwerkstoff hergestellt aus dem Stahl | |
DE2800444A1 (de) | Legierter stahl | |
DE60027355T2 (de) | Selbstschmierendes Kolbenringmaterial für Verbrennungsmotoren und Kolbenring | |
EP2414552B1 (de) | Kugelzapfen aus bainitischen stählen für pkw und leichte lkw | |
DE19836360B4 (de) | Kolbenringmaterial mit hervorragender Bearbeitbarkeit und Resistenz gegen Fressen sowie Kolbenring hieraus | |
DE3522115A1 (de) | Hitzebestaendiger 12-cr-stahl und daraus gefertigte turbinenteile | |
DE19920324B4 (de) | Verwendung eines Stahls mit ausgezeichneter Bruchspaltbarkeit und Dauerfestigkeit in Pleuelstangen | |
DE69917444T2 (de) | Wärmebehandlungsfähiger Werkzeugstahl mit hervorragender Bearbeitbarkeit und Kaltumformbarkeit; Matrizen aus diesem Stahl | |
DE19531260C5 (de) | Verfahren zur Herstellung eines Warmarbeitsstahls | |
EP3325683B1 (de) | Legierter stahl und damit hergestellte bauteile |
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 |
|
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 38/22 20060101ALI20130808BHEP Ipc: C22C 38/02 20060101AFI20130808BHEP Ipc: C22C 38/18 20060101ALI20130808BHEP |
|
17P | Request for examination filed |
Effective date: 20131217 |
|
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 |
|
17Q | First examination report despatched |
Effective date: 20150629 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R079 Ref document number: 502012008357 Country of ref document: DE Free format text: PREVIOUS MAIN CLASS: C22C0038020000 Ipc: C22C0038280000 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 38/28 20060101AFI20160630BHEP Ipc: C22C 38/34 20060101ALI20160630BHEP Ipc: C22C 38/22 20060101ALI20160630BHEP Ipc: C22C 38/32 20060101ALI20160630BHEP |
|
INTG | Intention to grant announced |
Effective date: 20160721 |
|
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 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 832827 Country of ref document: AT Kind code of ref document: T Effective date: 20161015 |
|
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: 502012008357 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 5 |
|
REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Ref document number: 2617855 Country of ref document: PT Date of ref document: 20170102 Kind code of ref document: T Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 20161222 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20160928 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: 20161228 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: 20160928 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20160928 |
|
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: 20161229 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: 20160928 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: 20160928 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: 20160928 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2609123 Country of ref document: ES Kind code of ref document: T3 Effective date: 20170418 |
|
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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160928 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: 20160928 |
|
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: 20170128 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: 20161228 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 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: 20160928 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 502012008357 Country of ref document: DE |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20170118 Year of fee payment: 5 |
|
REG | Reference to a national code |
Ref country code: HU Ref legal event code: AG4A Ref document number: E031319 Country of ref document: HU |
|
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: 20160928 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
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 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20161228 |
|
26N | No opposition filed |
Effective date: 20170629 |
|
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: 20160928 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: T3 Ref document number: E 24145 Country of ref document: SK |
|
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: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161220 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161228 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161220 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: 20160928 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 6 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20161231 |
|
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: 20160928 |
|
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: 20160928 |
|
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: 20160928 |
|
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: 20160928 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20181221 Year of fee payment: 8 Ref country code: HU Payment date: 20181206 Year of fee payment: 7 Ref country code: CZ Payment date: 20181210 Year of fee payment: 7 Ref country code: FI Payment date: 20181213 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MM01 Ref document number: 832827 Country of ref document: AT Kind code of ref document: T Effective date: 20171220 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PT Payment date: 20191217 Year of fee payment: 8 Ref country code: LT Payment date: 20191210 Year of fee payment: 8 Ref country code: DE Payment date: 20191217 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20191219 Year of fee payment: 8 Ref country code: IT Payment date: 20191216 Year of fee payment: 8 Ref country code: PL Payment date: 20191210 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20200122 Year of fee payment: 8 |
|
REG | Reference to a national code |
Ref country code: FI Ref legal event code: MAE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20191220 Ref country code: CZ Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20191220 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: MM4A Ref document number: E 24145 Country of ref document: SK Effective date: 20191220 |
|
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: 20191220 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20191221 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 502012008357 Country of ref document: DE |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20210621 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MM4D Effective date: 20201220 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201231 Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201220 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210701 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201220 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20220412 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20201220 |
|
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: 20201221 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20201220 |