EP0299027A1 - Kriechfeste legierung aus hochschmelzendem metall und verfahren zu ihrer herstellung. - Google Patents
Kriechfeste legierung aus hochschmelzendem metall und verfahren zu ihrer herstellung.Info
- Publication number
- EP0299027A1 EP0299027A1 EP88901002A EP88901002A EP0299027A1 EP 0299027 A1 EP0299027 A1 EP 0299027A1 EP 88901002 A EP88901002 A EP 88901002A EP 88901002 A EP88901002 A EP 88901002A EP 0299027 A1 EP0299027 A1 EP 0299027A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- creep
- sintered
- metals
- refractory metals
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
- C22C32/0031—Matrix based on refractory metals, W, Mo, Nb, Hf, Ta, Zr, Ti, V or alloys thereof
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
Definitions
- the invention relates to a sintered alloy of one or more of the refractory metals Mo, W, Nb, Ta, V, Cr with a stacked structure, which has excellent heat resistance combined with excellent creep resistance at high temperatures, and a process for its production.
- refractory metals are often used for molded parts that are designed to withstand high temperatures.
- TZM molybdenum alloy that typically contains about 0.5% by weight of titanium, 0.08% by weight of zirconium and 0.05% by weight of carbon.
- US Pat. No. 3,982,970 also describes a high-melting alloy of this type, where the base material is dispersion-hardened by heat treatment in a special atmosphere.
- a suitable atmosphere is one which contains particles of thorium oxide or aluminum oxide with a grain size of ⁇ 1 ⁇ m.
- D ⁇ -OS 34 41 851 Another alloy of high-melting metal of this type based on molybdenum is described in D ⁇ -OS 34 41 851. This alloy contains 0.2-1% by weight of oxides of the tri- or tetravalent metals as dispersed particles.
- Known alloys of high-melting metals of this type are e.g. B. tungsten and molybdenum alloys, which are usually doped with small amounts of aluminum and / or silicon and potassium. It is essential with these alloys made of high-melting metals that, first of all, potassium must always be present in the alloy so that a stacked wire structure is formed.
- the additional li doping elements such as aluminum and / or silicon ensure that the potassium does not completely diffuse out of the material during the sintering, while practically completely escaping even during the sintering.
- the doping elements aluminum, silicon and potassium can in principle be introduced in liquid form, in the form of their solutions, or in the form of dry powders.
- both methods of introduction are not without problems in the production of these alloys from refractory metals on an industrial scale.
- the introduction of the potassium can only be sensibly solved in the form of the potassium silicates.
- the potassium silicates have the disadvantage that they are hygroscopic and are therefore very difficult to distribute uniformly in the powder mixture.
- the wet introduction of the doping elements in the form of solutions is also not without disadvantages with regard to reproducible production, since the slight volatility of the solutions, again particularly in the case of potassium, sintering with high sintered densities, which would be very advantageous for the subsequent mechanical shaping , difficult.
- a further molybdenum alloy of this type is described in EU-A1 119438, in which the molybdenum is doped with about 0.005-0.75% by weight of the elements aluminum and / or silicon and potassium.
- This prior publication also mentions that by additionally doping this alloy with 0.3-3% by weight of at least one compound selected from the group of oxides, carbides, borides and nitrides of the elements La, Ce, Dy, Y, Th, Ti, Zr, Nb, Ta, Hf, V, Cr, Mo, W and Mg the high temperature properties of the alloy can be further improved.
- This prior publication also does not mention anything about a particularly advantageous grain size of the doping elements in the production of this alloy.
- the object of the present invention is to create an alloy with a stack structure of one or more high-melting metals, in which the use of potassium as a doping element is dispensed with, as a result of which good reproducible production of the alloy and in particular high densities during sintering are achieved.
- the alloy is said to have improved room temperature, warm and creep strength properties compared to the known alloys of high-melting metals with a stacked structure.
- the alloy contains 0.005-10% by weight of one or more compounds and / or one or more mixed phases of the compounds from the group of oxides, nitrides, carbides, borides, silicates or aluminates with a grain size ⁇ 1.5 ⁇ m, the additives being limited to compounds and / or mixed phases whose melting point is above 1500 ° C. Due to the known prior art, the use of potassium as a doping element for the production of alloys from high-melting metals with a stacked structure was absolutely necessary, so that the serious problems in production had to be accepted through the use of potassium.
- the present invention is based on the completely surprising finding, based on the known prior art, that the element potassium can be dispensed with when using very specific compounds as doping materials for producing high-strength and creep-resistant, sintered alloys from high-melting metals with a stacked structure.
- the alloy of high-melting metal according to the invention has heat strengths and creep strengths at high temperatures, which exceed those of the known alloys of high-melting metals with a stacked structure.
- the strength values at room temperature also correspond, at least approximately, to those of the known alloys made of refractory metals, but may even exceed them in some cases.
- a particularly advantageous alloy made of high-melting metal with a stacked structure according to the present invention contains 1-5% by weight of the oxides and / or mixed oxides with a respective grain size ⁇ 0.5 ⁇ m of one or more elements from the group La, Ce, Y, Th, Mg, Ca, Sr, Hf, Zr, Er, Ba, Pr, Cr.
- Another particularly advantageous alloy made of refractory metal with a stacked structure according to the present invention contains 1 - 5% by weight of at least one of the borides and / or the nitride, each with a grain size of 0.5 ⁇ m, from Hf.
- the oxides La 2 O 3 , CeO 2 , Y 2 O 3 , ThO 2 , MgO, CaO, the mixed oxides Sr (Hf, Zr) O 3 , ZrO 2 ; Er 2 O 3 , SrZrO 3 , Sr 4 Zr 3 O 10 , BaZrO 3 as well as La 0.84 Sr 0.16 CrO 3 and the borides HfB, HfB 2 and HfN were found to be within an alloy content of 1 - 5% by weight proven particularly suitable doping materials.
- Molybdenum, tungsten, chromium and their alloys are particularly suitable as high-melting metals for the production of the alloy according to the invention.
- the alloy of high-melting metal according to the invention can only be produced by powder metallurgy.
- the alloy according to the invention is produced from high-melting metal in a particularly advantageous manner by adding 0.005-10% by weight of one or more compounds and / or one or more mixed phases of the compounds from the group of hydroxides, oxides, to the powdery high-melting metal or metals.
- Nitrides, carbides, borides, silicates or aluminates with a grain size ⁇ 1.5 ⁇ m and with a melting point above 1500 oC are mixed in powder form and that the powder mixture is pressed and sintered in a known manner and the sintered body obtained with a degree of deformation of at least 85 % is mechanically formed in compliance with the necessary heat treatments and then subjected to a recrystallization annealing.
- the doping materials according to the invention can be introduced dry in the form of solid powders into the high-melting metal powder. It is only important that the doping materials are introduced in a correspondingly fine manner with the specified grain size as a discrete, that is to say non-agglomerated and non-aggregated powder. Such a powder can be obtained, for example, by spray drying finely precipitated compounds. The most uniform distribution possible is achieved by forced mixing.
- Another method to achieve the required fine grain of the doping materials in the finished alloy is the introduction of the doping materials in the form of compounds that can be decomposed at low temperatures, for example in the case of lanthanum as lanthanum hydroxide La (OH) 3 , lanthanum carbonate La 2 (CO 3 ) 3 .8H 2 O, lanthanum heptahydrate LaCl 3 .7H 2 O or lanthanum molybdate La 2 (MoO 4 ) 3 .
- the introduction can be achieved with the necessary fine grain.
- the doping materials have melting points that are well above 1500 ° C., the amount of doping materials introduced into the powder mixture remains almost completely in the finished sintered alloy.
- the doping materials have melting points that are close to the specified lower limit of 1500 ° C., part of the doping materials introduced into the powder mixture escapes due to the high vapor pressure during sintering in gaseous form and entrains inevitable impurities in the alloy, so that a positive cleaning effect occurs.
- the powder batches can be pressed on die presses or isostatic presses.
- the compacts are usually sintered under normal pressure and H 2 atmosphere.
- the sintering temperature is chosen depending on the alloy composition, but must as a rule be at least 200 ° below the melting point of the lowest melting component.
- the achievable sintered densities of the alloy according to the invention are then over 95% of the theoretical density.
- the alloy is mechanically deformed by at least 85%, e.g. B. by rolling or drawing.
- the mechanical reshaping takes place in individual stages, each reshaping stage advantageously resulting in a reshaping by approximately 10%.
- Heat treatments are inserted between the individual forming operations. It is essential that both the forming temperature and the temperature of the heat treatment are below the respective recrystallization temperature.
- the material is subjected to a recrystallization annealing, as a result of which the stacked structure is formed.
- Table 1 shows the comparison of the creep strengths of known alloys made of high-melting metals according to the prior art and alloys according to the invention made of high-melting metals.
- Table 2 shows the improved strengths and hardness values of alloys according to the invention made from refractory metals compared to alloys made from refractory metals according to the prior art and to unalloyed refractory metals.
- Forming temperatures of approx. 1400 o C, starting with gradations of approx. 10% each, are hammered round on rods with a diameter of approx. 3 mm. These bars were drawn at a temperature of about 800 ° C in several stages to 0.5 mm diameter wires. The wires obtained showed a final one
- Alloy 4 was produced in the same way as in Example 1. Instead of La (OH) 3 , 1% by weight of MgO with a grain size of 0.45 ⁇ m was mixed in and wire with a diameter of 0.5 mm was produced.
- Alloy 5 was produced by the same procedure as in Example 1. Instead of La (OH) 3 , 1% by weight of Al 2 O 3 with a grain size of 1.2 ⁇ m was mixed in and wire with a diameter of 0.5 mm was produced. In game 4
- Molybdenum metal powder with a grain size of 5 ⁇ m was mixed with 2% by weight
- a tungsten alloy according to the invention was produced as follows: 99% by weight of tungsten metal powder with a grain size of 4 ⁇ m was mixed with 1% by weight of La (OH) 3 powder with a grain size of 0.4 ⁇ m and cold isostatically squared with 3 MN Bars with a cross section of 2.5 cm pressed. The bars were then sintered under Hp protective gas at 2100 ° C. for 12 hours. The sintered bars were hammered round at temperatures of 1600 ° C, starting with gradations of about 10% each, on bars with a diameter of approx. 3 mm. After recrystallization annealing at approx. 2300 oC, these rods already showed a stacked structure with a diameter of approx. 3 mm.
- Example 5 Another tungsten alloy with 1.0 wt% CeO 2 was made in the same manner as Example 5. In contrast, only the sintering was carried out at a temperature of 2400 ° C. for 6 hours. The further processing into bars of approximately 3 mm in diameter was carried out analogously to Example 5.
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT0015887A AT386612B (de) | 1987-01-28 | 1987-01-28 | Kriechfeste legierung aus hochschmelzendem metall und verfahren zu ihrer herstellung |
AT158/87 | 1987-01-28 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0299027A1 true EP0299027A1 (de) | 1989-01-18 |
EP0299027B1 EP0299027B1 (de) | 1991-10-02 |
Family
ID=3483080
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP88901002A Expired - Lifetime EP0299027B1 (de) | 1987-01-28 | 1988-01-26 | Kriechfeste legierung aus hochschmelzendem metall und verfahren zu ihrer herstellung |
Country Status (6)
Country | Link |
---|---|
US (1) | US4950327A (de) |
EP (1) | EP0299027B1 (de) |
JP (1) | JP2609212B2 (de) |
AT (1) | AT386612B (de) |
DE (1) | DE3865259D1 (de) |
WO (1) | WO1988005830A1 (de) |
Families Citing this family (41)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AT389326B (de) * | 1987-11-09 | 1989-11-27 | Plansee Metallwerk | Verfahren zur herstellung von halbzeug aus gesinterten refraktaermetall-legierungen |
DE3835328C1 (de) * | 1988-10-17 | 1989-12-14 | Gesellschaft Fuer Wolfram-Industrie Mbh, 8220 Traunstein, De | |
ES2020131A6 (es) * | 1989-06-26 | 1991-07-16 | Cabot Corp | Procedimiento para la produccion de polvos de tantalo, niobio y sus aleaciones. |
JPH0747793B2 (ja) * | 1991-04-26 | 1995-05-24 | 株式会社クボタ | 酸化物分散強化耐熱焼結合金 |
AT395493B (de) * | 1991-05-06 | 1993-01-25 | Plansee Metallwerk | Stromzufuehrung |
AT399165B (de) * | 1992-05-14 | 1995-03-27 | Plansee Metallwerk | Legierung auf chrombasis |
AT401124B (de) * | 1994-07-05 | 1996-06-25 | Plansee Ag | Elektrischer leiter in lampen |
US5590386A (en) * | 1995-07-26 | 1996-12-31 | Osram Sylvania Inc. | Method of making an alloy of tungsten and lanthana |
US5604321A (en) * | 1995-07-26 | 1997-02-18 | Osram Sylvania Inc. | Tungsten-lanthana alloy wire for a vibration resistant lamp filament |
US5868876A (en) * | 1996-05-17 | 1999-02-09 | The United States Of America As Represented By The United States Department Of Energy | High-strength, creep-resistant molybdenum alloy and process for producing the same |
DE19643156C1 (de) * | 1996-10-18 | 1998-02-19 | Siemens Ag | Verfahren zur Herstellung eines Chrom-Werkstoffs |
AT2017U1 (de) * | 1997-05-09 | 1998-03-25 | Plansee Ag | Verwendung einer molybdän-/wolfram-legierung in bauteilen für glasschmelzen |
FR2771755B1 (fr) * | 1997-11-28 | 1999-12-31 | Saint Gobain Rech | Alliage resistant a la corrosion, procede d'elaboration et article realise a partir de l'alliage |
US6102979A (en) * | 1998-08-28 | 2000-08-15 | The United States Of America As Represented By The United States Department Of Energy | Oxide strengthened molybdenum-rhenium alloy |
AT4408U1 (de) | 2000-05-18 | 2001-06-25 | Plansee Ag | Verfahren zur herstellung einer elektrischen lampe |
KR100375944B1 (ko) * | 2000-07-08 | 2003-03-10 | 한국과학기술원 | 기계적 합금화에 의한 산화물 분산강화 텅스텐 중합금의 제조방법 |
MXPA04007104A (es) * | 2002-01-23 | 2004-10-29 | Starck H C Inc | Productos laminados de pulvimetalurgia de metal refractario de tamano de grano estabilizado. |
JP2003293070A (ja) * | 2002-03-29 | 2003-10-15 | Japan Science & Technology Corp | 高強度・高靭性Mo合金加工材とその製造方法 |
US6830637B2 (en) * | 2002-05-31 | 2004-12-14 | Osram Sylvania Inc. | Large diameter tungsten-lanthana rod |
ATE354683T1 (de) * | 2002-09-04 | 2007-03-15 | Osram Sylvania Inc | Verfahren zur herstellung von sag-beständigen molybdän-lanthanoxid-legierungen |
JP2006517615A (ja) * | 2003-01-31 | 2006-07-27 | ハー ツェー シュタルク インコーポレイテッド | 耐火金属アニーリングバンド |
US20060151072A1 (en) * | 2003-04-23 | 2006-07-13 | James Daily | Molybdenum alloy x-ray targets having uniform grain structure |
US7544228B2 (en) * | 2003-05-20 | 2009-06-09 | Exxonmobil Research And Engineering Company | Large particle size and bimodal advanced erosion resistant oxide cermets |
US7074253B2 (en) * | 2003-05-20 | 2006-07-11 | Exxonmobil Research And Engineering Company | Advanced erosion resistant carbide cermets with superior high temperature corrosion resistance |
US7153338B2 (en) * | 2003-05-20 | 2006-12-26 | Exxonmobil Research And Engineering Company | Advanced erosion resistant oxide cermets |
US7175687B2 (en) * | 2003-05-20 | 2007-02-13 | Exxonmobil Research And Engineering Company | Advanced erosion-corrosion resistant boride cermets |
US7175686B2 (en) * | 2003-05-20 | 2007-02-13 | Exxonmobil Research And Engineering Company | Erosion-corrosion resistant nitride cermets |
JP4603841B2 (ja) * | 2004-09-29 | 2010-12-22 | 株式会社アライドマテリアル | 耐酸化性を有するタングステン合金とその製造方法 |
US20080203920A1 (en) * | 2005-05-19 | 2008-08-28 | Koninklijke Philips Electronics, N.V. | Lamp Having Molybdenum Alloy Lamp Components |
US7731776B2 (en) * | 2005-12-02 | 2010-06-08 | Exxonmobil Research And Engineering Company | Bimodal and multimodal dense boride cermets with superior erosion performance |
US8059785B2 (en) * | 2007-09-06 | 2011-11-15 | Varian Medical Systems, Inc. | X-ray target assembly and methods for manufacturing same |
US20090068055A1 (en) * | 2007-09-07 | 2009-03-12 | Bloom Energy Corporation | Processing of powders of a refractory metal based alloy for high densification |
CA2705769A1 (en) * | 2007-11-20 | 2009-05-28 | Exxonmobil Research And Engineering Company | Bimodal and multimodal dense boride cermets with low melting point binder |
EP2194564B1 (de) | 2008-12-04 | 2013-05-22 | Varian Medical Systems, Inc. | Röntgentarget-Anordnung und Herstellungsverfahren dafür |
WO2010141463A1 (en) * | 2009-06-04 | 2010-12-09 | First Solar, Inc. | Dopant-containing contact material |
US20140147327A1 (en) * | 2011-07-29 | 2014-05-29 | Tohoku University | Method for manufacturing alloy containing transition metal carbide, tungsten alloy containing transition metal carbide, and alloy manufactured by said method |
AT14143U1 (de) * | 2013-09-02 | 2015-05-15 | Plansee Se | Pulvermetallurgisches Bauteil |
DE102015111993A1 (de) * | 2015-07-23 | 2017-01-26 | Schott Ag | Formdorn mit Diffusionsschicht zur Glasformung |
AT15596U1 (de) * | 2017-02-28 | 2018-03-15 | Plansee Composite Mat Gmbh | Sputtertarget und Verfahren zur Herstellung eines Sputtertargets |
WO2020196879A1 (ja) | 2019-03-27 | 2020-10-01 | 日立金属株式会社 | 合金組成物および合金組成物の製造方法、並びに金型 |
CN117897243A (zh) | 2021-11-26 | 2024-04-16 | 株式会社博迈立铖 | 复合材料和复合材料的制造方法以及模具 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2628926A (en) * | 1949-06-21 | 1953-02-17 | Westinghouse Electric Corp | Manufacture of machinable molybdenum |
US3285736A (en) * | 1964-08-27 | 1966-11-15 | Gen Electric | Powder metallurgical alloy |
US3457051A (en) * | 1965-01-04 | 1969-07-22 | Du Pont | Metallic refractory compositions |
GB1298944A (en) * | 1969-08-26 | 1972-12-06 | Int Nickel Ltd | Powder-metallurgical products and the production thereof |
US3982970A (en) * | 1972-01-24 | 1976-09-28 | United Kingdom Atomic Energy Authority | Ductility of molybdenum and its alloys |
US3954421A (en) * | 1972-04-10 | 1976-05-04 | Westinghouse Electric Corporation | Alloys for high creep applications |
JPS5741336A (en) * | 1980-08-27 | 1982-03-08 | Hitachi Ltd | Manufacture of thorium-tungsten |
EP0074679B1 (de) * | 1981-09-03 | 1985-03-20 | BBC Aktiengesellschaft Brown, Boveri & Cie. | Verfahren zur Herstellung eines Werkstückes aus einer warmfesten Legierung |
US4514234A (en) * | 1983-02-10 | 1985-04-30 | Tokyo Shibaura Denki Kabushiki Kaisha | Molybdenum board and process of manufacturing the same |
JPH0617556B2 (ja) * | 1983-02-10 | 1994-03-09 | 株式会社東芝 | モリブデン材の製造方法 |
JPS59177345A (ja) * | 1983-03-29 | 1984-10-08 | Toshiba Corp | 構造材用モリブデン |
US4599214A (en) * | 1983-08-17 | 1986-07-08 | Exxon Research And Engineering Co. | Dispersion strengthened extruded metal products substantially free of texture |
JPS60197839A (ja) * | 1984-03-22 | 1985-10-07 | Toshiba Corp | セラミツクス焼結用治具及びその製造方法 |
DE3441851A1 (de) * | 1984-11-15 | 1986-06-05 | Murex Ltd., Rainham, Essex | Molybdaenlegierung |
-
1987
- 1987-01-28 AT AT0015887A patent/AT386612B/de not_active IP Right Cessation
-
1988
- 1988-01-26 DE DE8888901002T patent/DE3865259D1/de not_active Expired - Lifetime
- 1988-01-26 JP JP63501265A patent/JP2609212B2/ja not_active Expired - Lifetime
- 1988-01-26 EP EP88901002A patent/EP0299027B1/de not_active Expired - Lifetime
- 1988-01-26 US US07/264,959 patent/US4950327A/en not_active Expired - Lifetime
- 1988-01-26 WO PCT/AT1988/000002 patent/WO1988005830A1/de active IP Right Grant
Non-Patent Citations (1)
Title |
---|
See references of WO8805830A1 * |
Also Published As
Publication number | Publication date |
---|---|
EP0299027B1 (de) | 1991-10-02 |
US4950327A (en) | 1990-08-21 |
AT386612B (de) | 1988-09-26 |
DE3865259D1 (de) | 1991-11-07 |
ATA15887A (de) | 1988-02-15 |
JP2609212B2 (ja) | 1997-05-14 |
JPH01502680A (ja) | 1989-09-14 |
WO1988005830A1 (en) | 1988-08-11 |
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