EP1364732B1 - Hartmetallbauteil mit gradiertem Aufbau - Google Patents
Hartmetallbauteil mit gradiertem Aufbau Download PDFInfo
- Publication number
- EP1364732B1 EP1364732B1 EP03008539A EP03008539A EP1364732B1 EP 1364732 B1 EP1364732 B1 EP 1364732B1 EP 03008539 A EP03008539 A EP 03008539A EP 03008539 A EP03008539 A EP 03008539A EP 1364732 B1 EP1364732 B1 EP 1364732B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- structural part
- production
- part according
- dispersion
- carbide
- 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.)
- Expired - Lifetime
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- 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
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
-
- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Definitions
- the invention relates to a powder metallurgically produced component made of a hard metal alloy with a binder content of 0.1 to 20 wt.%, Which contains at least one grain growth inhibiting additive and a process for its preparation.
- hard metal is meant a composite material consisting essentially of a carbide component and a binder.
- carbide components are the carbides or mixed carbides of the metals W, Ti, Zr, Hf, V, Nb, Ta, Mo and Cr.
- Typical binder metals are Co, Ni and Fe.
- additives of other hard materials, such as carbonitrides, are used.
- the properties of hard metals are determined by the ratio of carbide content to binder content, chemical composition, carbide grain size and carbide grain size distribution. This opens up many possibilities to adapt the properties of carbide to the respective field of application.
- increasing binder content improves fracture toughness and flexural strength while reducing hardness, stiffness and compressive strength.
- a reduction in the carbide grain size leads to an increase in hardness, compressive and flexural strength, with reduced impact and fracture toughness.
- carbide powders in the particle size range 0.2 ⁇ m to 15 ⁇ m are used today for the production of carbide components.
- grain growth inhibitors are added.
- the most effective grain growth inhibiting additives are vanadium carbide, chromium carbide, titanium carbide, tantalum carbide and niobium carbide.
- two or more additives are used, such as mixtures of VC and Cr 3 C 2 or TaC, NbC and TiC.
- the grain growth inhibiting additive can thereby already be finely distributed in the main component before or during the carburization.
- the effectiveness is also present when the grain growth inhibitor is added to the hard metal powder or individual constituents of the hard metal powder before, during or after the grinding.
- Hard metal components can be locally loaded very differently. Therefore, early solutions have been known or implemented, based on a composite material of two or more hard metal alloys. That's how it describes US 5,543,235 a cemented carbide material composite produced by powder metallurgy composite pressing, wherein the individual material regions differ by their composition or microstructure.
- a rotating composite tool which is composed of two hard metal alloys, is also in the PCT / US00 / 33644 described. The preparation is also preferably via composite presses.
- Another process technique for producing a hard metal composite body is based on U.S. 5,594,931 out.
- a slurry is applied, which consists of a powder mixture, a solvent, a binder and a plasticizer.
- the composite green compact produced in this way is compacted by sintering.
- a disadvantage of the material composites described here is that in the areas of the composite body, where materials meet with different properties, stress concentrations arise. Furthermore, it has to be considered that every material component has its own sintering behavior. This can cause a distortion of the component during sintering.
- compositionally graded structure is meant that the composition changes gradually over a range of grades.
- coated carbide graded versions are in the area of the layer, in the transition area Layer / base material and in the neighboring base material has long been known. This grading is achieved, for example, by the addition of carbonitrides.
- the metallic carbide or nitride forming elements diffuse towards the center of the carbide body. This achieves a binder enrichment in the region of the edge zone and a graded transition to the matrix composition.
- indexable inserts with a binder-rich edge zone, adjacent to the hard material layer have long been used for steel cutting.
- the grading is limited to a small, near-surface area.
- binder metals such as cobalt
- a method is for example in the EP 0 871 556 described.
- a composite consisting of at least two areas differing in binder content is produced by composite pressing.
- the temperature should be adjusted so that the binder metal diffuses from the higher binder content composite region to the lower binder content composite region.
- the disadvantage is that the sintering temperature is set very accurately, so as not to achieve a complete concentration balance and thus loss of different material properties.
- the composite pressing is associated with higher production costs, as is the case in the production of a monolithic green body.
- This object is achieved by a method for producing a component from a hard metal alloy according to claim 1.
- the graded concentration course of the grain growth inhibiting additive leads to a graded course of the carbide grain size. Subsequently, the mechanical properties also show a graded course. This is advantageous, for example, where a high level of wear resistance and bending strength at the surface and at the same time a high level of toughness in the core is required, for example in the case of forming tools or tools for diamond production.
- the concentration profile of the grain growth-inhibiting additive is adjusted so that in the region of the edge zone, the concentration values are higher and these decrease towards the center of the component, the edge zone is fine-grained, with a graded transition to the coarse-grained center.
- ком ⁇ онент with excellent wear resistance and bending strength in the region of the edge zone, combined with a high toughness of the center can be produced. These have improved tool life.
- a high fracture toughness in the region of the edge zone may be advantageous. This is achieved by a reduced content of grain growth inhibiting additive in the region of the edge zone.
- Advantageous grain growth inhibiting additives are vanadium and chromium compounds, the maximum concentration being 2% by weight. Higher levels lead to embrittlement effects.
- a particularly advantageous process is the superficial application of a dispersion or solution on a green body.
- the dispersion contains the grain growth inhibiting additive in very finely divided form.
- the green compact can be in the as-pressed state. If the green compact contains waxing or plasticizing agent additives, it can also be present in the dewaxed or partially dewaxed state, in accordance with an advantageous embodiment of the present invention.
- the application of the dispersion or solution can be done for example by dipping, spraying or brushing. Subsequently, the dispersion or solution penetrates into the interior of the green body along open pore channels.
- the reaction time and the content of the dispersion or solution of grain growth inhibiting additive essentially determine the amount introduced or the penetration depth.
- the carbide component of the green body has a mean particle size of less than 2 microns.
- Fig. 1 shows the vanadium content over the sample cross-section.
- Fig.2 In addition to the vanadium content, the carbide grain size is indicated.
- Figure 3 and Fig. 5 each show the hardness profile over the sample cross-section.
- Fig. 4 schematically shows the cross section of a drawing tool.
- Fig. 1 and Fig. 2 refer to Example 1, Fig. 3 on example 2, Fig. 4 and Fig. 5 on example 3.
- the greenlings were subjected to a usual eviscerating process.
- the green compacts were immersed for 5 seconds in the above-described dispersion and then dried in air at 50 ° C.
- Fig. 1 shows that the vanadium content in the region of the edge zone is 0.24% by weight and this value gradually decreases inwards over the cross section of the sample.
- the vanadium content at a distance of 3.8 mm from the sample edge is 0.08 wt.%.
- the corresponding vanadium concentrations were below the detection limit of the microprobe.
- the graded vanadium distribution leads to a graded grain stabilization effect, as does the WC grain size values in Fig. 2 document. As the average grain size increases from the edge zone towards the center, the corresponding hardness values decrease, as in FIG Fig. 3 is shown.
- a cemented carbide approach with 89.5 wt.% WC having an average grain size of 0.8 micron, 0.5 wt.% Cr 3 C 2, balance Co was prepared according to the usual method in the hard metal industry.
- the greenlings were subjected to a usual eviscerating process.
- a dispersion of distilled water and V 2 O 5 was prepared, the solid content being 2% by weight and the average V 2 O 5 particle size being less than 50 nm.
- the green compacts were immersed for 5 seconds in the above-described dispersion and then dried in air at 50 ° C.
- samples were sintered with reference green sheets that were not aftertreated at a temperature of 1400 ° C under vacuum.
- the analysis of the samples was carried out by electron beam microprobe, the microstructural and mechanical characterization by a light microscopic examination or hardness test.
- the samples according to the invention again show a graded vanadium concentration course, with a marginal zone value of 0.21 wt.% V and a center value of 0.03 wt.% V.
- the corresponding hardness values are 1698 HV30 or 1648 HV30.
- the hardness curve is in Figure 3 played.
- the reference sample shows a uniform hardness profile over the cross section with an average value of 1605 HV30.
- the samples according to the invention and the reference samples were also subjected to a bending test.
- the mean value of ten measurements is 3950 MPa for the samples according to the invention and 3500 MPa for the comparative samples.
- a hard metal batch with 93.4 wt.% WC with an average particle size of 2.0 .mu.m, 0.2 wt.% TiC, 0.4 wt.% TaC / NbC, remainder Co was prepared according to the methods customary in the hard metal industry. Cylindrical green compacts were produced by isostatic pressing with a compacting pressure of 100 MPa, which were formed by mechanical machining into a hard metal drawing tool. The greenlings were subjected to a usual eviscerating process. In turn, a dispersion of distilled water and V 2 O 5 was prepared, wherein the solids content was 2 wt.%, With a particle size of dispersed V 2 O 5 particles of less than 50 nm.
- Fig. 4 shows the area where the characterization was done by electron microprobe and hardness testing.
- the vanadium content in the edge zone is 0.18 wt.%, At a distance of 2 mm from the sample edge only 0.11 wt.%.
- Fig. 5 shows the gradual hardness curve.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT0024502U AT5837U1 (de) | 2002-04-17 | 2002-04-17 | Hartmetallbauteil mit gradiertem aufbau |
AT2452002U | 2002-04-17 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP1364732A2 EP1364732A2 (de) | 2003-11-26 |
EP1364732A3 EP1364732A3 (de) | 2005-12-21 |
EP1364732B1 true EP1364732B1 (de) | 2008-03-05 |
Family
ID=3485393
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP03008539A Expired - Lifetime EP1364732B1 (de) | 2002-04-17 | 2003-04-14 | Hartmetallbauteil mit gradiertem Aufbau |
Country Status (7)
Country | Link |
---|---|
US (2) | US20040009088A1 (he) |
EP (1) | EP1364732B1 (he) |
JP (1) | JP2003328067A (he) |
CN (1) | CN100482836C (he) |
AT (2) | AT5837U1 (he) |
DE (1) | DE50309292D1 (he) |
IL (1) | IL155430A (he) |
Families Citing this family (30)
Publication number | Priority date | Publication date | Assignee | Title |
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US7385889B2 (en) * | 2003-03-03 | 2008-06-10 | Samsung Electronics Co., Ltd. | Method and apparatus for managing disc defect using temporary DFL and temporary DDS including drive and disc information disc with temporary DFL and temporary DDS |
JP4313587B2 (ja) * | 2003-03-03 | 2009-08-12 | 株式会社タンガロイ | 超硬合金及び被覆超硬合金部材並びにそれらの製造方法 |
US7506109B2 (en) * | 2003-05-09 | 2009-03-17 | Lg Electronics Inc. | Recording medium having data structure for managing at least a data area of the recording medium and recording and reproducing methods and apparatuses |
PT1548136E (pt) * | 2003-12-15 | 2008-06-12 | Sandvik Intellectual Property | Ferramenta de carboneto cementado e método para a sua produção |
EP1697551B1 (en) * | 2003-12-15 | 2015-07-22 | Sandvik Intellectual Property AB | Cemented carbide tools for mining and construction applications and method of making the same |
US7634582B2 (en) * | 2003-12-19 | 2009-12-15 | Intel Corporation | Method and architecture for optical networking between server and storage area networks |
DE102004034312A1 (de) * | 2004-07-15 | 2006-02-02 | Mtu Aero Engines Gmbh | Dichtungsanordnung und Verfahren zur Herstellung eines Dichtkörpers für eine Dichtungsanordnung |
DE04090325T1 (de) * | 2004-08-24 | 2006-06-22 | Tungaloy Corporation, Kawasaki | Hartmetall, beschichtetes Hartmetallteil und Verfahren zu dessen Herstellung |
CN100419105C (zh) * | 2005-02-04 | 2008-09-17 | 李北 | 一种金属陶瓷材料及其成型工艺 |
WO2009111749A1 (en) * | 2008-03-07 | 2009-09-11 | University Of Utah | Thermal degradation and crack resistant functionally graded cemented tungsten carbide and polycrystalline diamond |
SE532704C2 (sv) * | 2008-03-31 | 2010-03-23 | Atlas Copco Secoroc Ab | Förfarande för att öka segheten av stift för ett bergborrverktyg. |
DE102008040094A1 (de) | 2008-07-02 | 2009-01-29 | Basf Se | Verfahren zur Herstellung eines oxidischen geometrischen Formkörpers |
DE102008040093A1 (de) | 2008-07-02 | 2008-12-18 | Basf Se | Verfahren zur Herstellung eines ringähnlichen oxidischen Formkörpers |
EP2184122A1 (en) | 2008-11-11 | 2010-05-12 | Sandvik Intellectual Property AB | Cemented carbide body and method |
CN101429618B (zh) * | 2008-11-21 | 2012-10-31 | 嘉应学院 | 型内熔化扩散形成梯度耐磨材料及其制造方法 |
AT13536U1 (de) * | 2013-05-07 | 2014-02-15 | Plansee Se | Verfahren zur Herstellung eines Formkörpers und damit herstellbarer Formkörper |
KR102231553B1 (ko) * | 2013-05-31 | 2021-03-23 | 산드빅 인터렉츄얼 프로퍼티 에이비 | 초경합금의 신규 제조 방법 및 그로부터 획득되는 제품 |
IN2013CH04500A (he) | 2013-10-04 | 2015-04-10 | Kennametal India Ltd | |
CN104404283B (zh) * | 2014-12-15 | 2017-01-04 | 中南大学 | 一种直接添加难熔金属制备梯度硬质合金的方法 |
CN104988372B (zh) * | 2015-08-06 | 2017-04-26 | 广东工业大学 | 一种表面软化的梯度硬质合金及其制备方法 |
RU2746537C2 (ru) * | 2016-09-28 | 2021-04-15 | Сандвик Интеллекчуал Проперти Аб | Вставка долота для бурения |
CN108480624B (zh) * | 2018-04-13 | 2019-09-13 | 昆明理工大学 | 一种粉末递增压制装置及压制方法 |
EP3653743A1 (en) * | 2018-11-14 | 2020-05-20 | Sandvik Mining and Construction Tools AB | Binder redistribution within a cemented carbide mining insert |
WO2020127684A1 (en) * | 2018-12-20 | 2020-06-25 | Ab Sandvik Coromant | Coated cutting tool |
ES2912991T3 (es) * | 2019-07-10 | 2022-05-30 | Sandvik Mining And Construction Tools Ab | Cuerpo de carburo cementado con gradiente y método de fabricación del mismo |
CN111069610A (zh) * | 2019-12-20 | 2020-04-28 | 株洲硬质合金集团有限公司 | 一种梯度结构硬质合金球齿及其制备方法 |
EP3909707A1 (en) * | 2020-05-14 | 2021-11-17 | Sandvik Mining and Construction Tools AB | Method of treating a cemented carbide mining insert |
DE102020120576A1 (de) * | 2020-08-04 | 2022-02-10 | Hauni Maschinenbau Gmbh | Hartmetallmesser für Strangschnitt und Messerhalter |
JP6957828B1 (ja) * | 2020-10-30 | 2021-11-02 | 住友電工ハードメタル株式会社 | 超硬合金及びそれを備える切削工具 |
CN114737097B (zh) * | 2022-04-27 | 2022-12-09 | 山东大学 | 一种三层梯度结构硬质合金及其制备方法 |
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US4101703A (en) * | 1972-02-04 | 1978-07-18 | Schwarzkopf Development Corporation | Coated cemented carbide elements |
US4610931A (en) * | 1981-03-27 | 1986-09-09 | Kennametal Inc. | Preferentially binder enriched cemented carbide bodies and method of manufacture |
EP0111600A1 (en) | 1982-12-13 | 1984-06-27 | Reed Rock Bit Company | Improvements in or relating to cutting tools |
DE3574738D1 (de) * | 1984-11-13 | 1990-01-18 | Santrade Ltd | Gesinterte hartmetallegierung zum gesteinsbohren und zum schneiden von mineralien. |
SE456428B (sv) | 1986-05-12 | 1988-10-03 | Santrade Ltd | Hardmetallkropp for bergborrning med bindefasgradient och sett att framstella densamma |
US5116416A (en) | 1988-03-11 | 1992-05-26 | Vermont American Corporation | Boron-treated hard metal |
JP3046336B2 (ja) * | 1990-09-17 | 2000-05-29 | 東芝タンガロイ株式会社 | 傾斜組成組識の焼結合金及びその製造方法 |
JP3080983B2 (ja) | 1990-11-21 | 2000-08-28 | 東芝タンガロイ株式会社 | 傾斜組成組織の硬質焼結合金及びその製造方法 |
SE500049C2 (sv) | 1991-02-05 | 1994-03-28 | Sandvik Ab | Hårdmetallkropp med ökad seghet för mineralavverkning samt sätt att framställa denna |
US5431239A (en) * | 1993-04-08 | 1995-07-11 | Tibbitts; Gordon A. | Stud design for drill bit cutting element |
US5494635A (en) * | 1993-05-20 | 1996-02-27 | Valenite Inc. | Stratified enriched zones formed by the gas phase carburization and the slow cooling of cemented carbide substrates, and methods of manufacture |
US6073518A (en) * | 1996-09-24 | 2000-06-13 | Baker Hughes Incorporated | Bit manufacturing method |
US5543235A (en) | 1994-04-26 | 1996-08-06 | Sintermet | Multiple grade cemented carbide articles and a method of making the same |
US5945167A (en) * | 1994-10-27 | 1999-08-31 | Honda Giken Kogyo Kabushiki Kaisha | Method of manufacturing composite material |
US5762843A (en) | 1994-12-23 | 1998-06-09 | Kennametal Inc. | Method of making composite cermet articles |
US5594931A (en) * | 1995-05-09 | 1997-01-14 | Newcomer Products, Inc. | Layered composite carbide product and method of manufacture |
US5623723A (en) * | 1995-08-11 | 1997-04-22 | Greenfield; Mark S. | Hard composite and method of making the same |
US6495115B1 (en) * | 1995-09-12 | 2002-12-17 | Omg Americas, Inc. | Method to produce a transition metal carbide from a partially reduced transition metal compound |
SE513740C2 (sv) * | 1995-12-22 | 2000-10-30 | Sandvik Ab | Slitstark hårmetallkropp främst för användning vid bergborrning och mineralbrytning |
JPH10138027A (ja) * | 1996-11-11 | 1998-05-26 | Shinko Kobelco Tool Kk | ドリル用超硬合金および該合金を用いたプリント基板穿孔用ドリル |
DE19752289C1 (de) | 1997-11-26 | 1999-04-22 | Hartmetall Beteiligungs Gmbh | Gesinterter Hartmetall-Formkörper |
WO2000038864A1 (en) * | 1998-12-23 | 2000-07-06 | De Beers Industrial Diamond Division (Proprietary) Limited | Abrasive body |
US6511265B1 (en) | 1999-12-14 | 2003-01-28 | Ati Properties, Inc. | Composite rotary tool and tool fabrication method |
DE10135790B4 (de) * | 2001-07-23 | 2005-07-14 | Kennametal Inc. | Feinkörniges Sinterhartmetall und seine Verwendung |
US6869460B1 (en) * | 2003-09-22 | 2005-03-22 | Valenite, Llc | Cemented carbide article having binder gradient and process for producing the same |
-
2002
- 2002-04-17 AT AT0024502U patent/AT5837U1/de not_active IP Right Cessation
-
2003
- 2003-04-10 JP JP2003106153A patent/JP2003328067A/ja not_active Withdrawn
- 2003-04-14 EP EP03008539A patent/EP1364732B1/de not_active Expired - Lifetime
- 2003-04-14 DE DE50309292T patent/DE50309292D1/de not_active Expired - Lifetime
- 2003-04-14 IL IL155430A patent/IL155430A/he unknown
- 2003-04-14 AT AT03008539T patent/ATE387978T1/de not_active IP Right Cessation
- 2003-04-17 CN CNB031472184A patent/CN100482836C/zh not_active Expired - Lifetime
- 2003-04-17 US US10/417,487 patent/US20040009088A1/en not_active Abandoned
-
2007
- 2007-10-09 US US11/869,127 patent/US7537726B2/en not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
---|---|
CN1480543A (zh) | 2004-03-10 |
IL155430A0 (en) | 2003-11-23 |
CN100482836C (zh) | 2009-04-29 |
EP1364732A2 (de) | 2003-11-26 |
DE50309292D1 (de) | 2008-04-17 |
US20080075621A1 (en) | 2008-03-27 |
JP2003328067A (ja) | 2003-11-19 |
ATE387978T1 (de) | 2008-03-15 |
AT5837U1 (de) | 2002-12-27 |
US20040009088A1 (en) | 2004-01-15 |
EP1364732A3 (de) | 2005-12-21 |
US7537726B2 (en) | 2009-05-26 |
IL155430A (he) | 2009-05-04 |
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