EP1751320A1 - Verschleissteil aus einem diamanthaltigen verbundwerkstoff - Google Patents
Verschleissteil aus einem diamanthaltigen verbundwerkstoffInfo
- Publication number
- EP1751320A1 EP1751320A1 EP05743117A EP05743117A EP1751320A1 EP 1751320 A1 EP1751320 A1 EP 1751320A1 EP 05743117 A EP05743117 A EP 05743117A EP 05743117 A EP05743117 A EP 05743117A EP 1751320 A1 EP1751320 A1 EP 1751320A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- part according
- wearing part
- alloy
- metallic
- diamond
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
-
- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1005—Pretreatment of the non-metallic additives
- C22C1/1015—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform
- C22C1/1021—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform the preform being ceramic
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
- C22C2026/006—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes with additional metal compounds being carbides
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/30—Self-sustaining carbon mass or layer with impregnant or other layer
Definitions
- the invention relates to a wear part made of a diamond-containing composite material and a method for its production.
- a wearing part is a component that is subject to high wear and tear.
- materials such as hardened steels, high-speed steels, stones, hard metals and hard materials.
- diamond-containing composites or material composites are becoming increasingly interesting.
- No. 4,124,401 describes a polycrystalline diamond material in which the individual diamond grains are held together by silicon carbide and a metal carbide or metal silicide. Although materials according to US Pat. No. 4,124,401 are very hard, they can only be machined in a very complex manner.
- EP 0 116 403 discloses a diamond-containing composite material which consists of 80 to 90% by volume of diamond and 10 to 20% by volume of Ni and Si-containing phase, Ni as Ni or Ni silicide and Si as Si, SiC or Ni silicide is present. There are no other phase components between the diamond grains. In order to achieve a sufficient bond between the individual diamond grains, sintering temperatures> 1400 ° C are required. Since diamond is no longer stable at these temperatures under normal pressure conditions, correspondingly high pressures are required according to the pressure-temperature diagram in order to prevent the diamond from decomposing. The systems required for this are expensive. In addition, the diamond composite material produced in this way has very low fracture toughness and poor machinability.
- WO 99/12866 describes a method for producing a diamond-silicon carbide composite material. It is manufactured by infiltration of a diamond skeleton with silicon or one Silicon alloy. Due to the high melting point of silicon and the resulting high infiltration temperature, diamond is converted to a large extent into graphite and subsequently into silicon carbide. Due to the high brittleness, the mechanical workability of this material is extremely problematic and complex.
- US 4,902,652 describes a method for producing a sintered diamond material.
- An element from the group of transition metals from groups 4a, 5a and 6a, boron and silicon is deposited on diamond powder by means of physical coating processes.
- the coated diamond grains are then connected to one another by means of a solid phase sintering process. It is disadvantageous that the resulting product has a high porosity, low fracture toughness and poor machinability.
- No. 5,045,972 describes a composite material in which, in addition to diamond grains with a size of 1 to 50 ⁇ m, there is a metallic matrix consisting of aluminum, magnesium, copper, silver or their alloys.
- the disadvantage here is that the metallic matrix is poorly bonded to the diamond grains, so that the mechanical integrity is not given to a sufficient degree.
- US 5,783,316 describes a method in which diamond grains are coated with W, Zr, Re, Cr or titanium, the coated grains are compacted in a wide sequence and the porous body is e.g. is infiltrated with Cu, Ag or Cu-Ag melts.
- the high coating costs and insufficient wear resistance limit the field of use of composite materials produced in this way.
- the object of the present invention is thus to provide a wearing part made of a diamond-containing composite material which has a high Has wear resistance and can be produced comparatively inexpensively by a sufficient formability.
- a metallic alloy is understood to mean a single-phase or multi-phase material which, in addition to metallic structural components, can also contain intermetallic, semi-metallic or ceramic structural components.
- An intermetallic alloy is a material that mainly consists of an intermetallic phase.
- the high bond strength between the diamond grains and the metallic / intermetallic alloy increases the fracture toughness due to the carbide phase that forms between them.
- the transition elements of the IIIb, IVb, Vb, Vlb groups of the periodic table, lanthanides, B and Si are suitable as carbide-forming elements. Disregarding the radioactive and very expensive elements, these are Si, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, B, Sc, Y and lanthanides.
- the carbidic phase preferably arises from a reaction of the carbide-forming element with diamond.
- a thickness of this carbidic phase in the nanometer range or a degree of coverage of> 60 percent is sufficient.
- the degree of coverage is to be understood as the proportion of the diamond grain surface which is enveloped by the carbidic phase. According to these premises, this corresponds to a volume content of the carbidic phase of> 0.001%. If an upper limit of 12 vol.% Is exceeded, the fracture toughness decreases below a critical value and inexpensive processing is no longer possible.
- the carbide-forming element or elements are also present in the metallic / intermetallic alloy in dissolved or precipitated form and, on their own or together with other alloying elements, cause the metallic / intermetallic alloy to solidify.
- a minimum hardness of the metallic / intermetallic alloy at room temperature of> 250 HV, preferably> 400 HV, must be set.
- the selection of the carbide-forming element depends on the matrix metal of the metallic / intermetallic alloy, the manufacturing process and the geometry of the wear part.
- Suitable matrix metals for the metallic alloy are Al, Fe, Co, Ni, Cu, Zn, Ag, Pb and Sn, the first six elements mentioned being particularly suitable.
- the carbide-forming elements and optionally further alloy elements are dissolved in the metallic alloy or in this, for example in the form of precipitates or intermetallic
- the alloy composition should be chosen so that the liquidus temperature is ⁇ 1400 ° C and the solidus temperature is preferably ⁇ 1200 ° C. This enables a correspondingly low one Processing temperature, for example infiltration or hot pressing temperature. It is thus possible to carry out processing at comparatively low gas pressures of ⁇ 1 kbar, preferably ⁇ 50 bar, in accordance with the pressure / temperature phase diagram for graphite / diamond. Compared to conventional polycrystalline diamond (PCD), this means significantly reduced manufacturing costs.
- PCD polycrystalline diamond
- the usual strength-increasing mechanisms in particular mixed crystal and precipitation hardening, can be used.
- the precipitation-hardened Al alloys such as Al-Mg-Si-Cu, Al-Cu-Ti, Al-Si-Cu and Al-Si-Mg, are particularly suitable
- Al-Si alloys hardenable Cu alloys, and here again preferably alloys with the addition of Si and further Cr and / or Zr, hypereutectic Ag-Si alloys, as well as Fe, Co and Ni alloys, to name their liquidus or solidus temperature Addition of Si and / or B is reduced to the values specified in claim 1.
- Excellent wear resistance can be achieved with diamond contents of 40% by volume.
- the upper limit of the diamond content of 90% by volume represents a barrier to cost-effective production.
- a sufficient fracture toughness of the diamond composite material would no longer be guaranteed at higher diamond contents.
- carbidic phase and metallic / intermetallic alloy are 0.1 to 10% by volume and 10 to 30% by volume.
- Trials have shown that diamond powder comes in a wide range
- Grain size spectrum can be processed.
- cheaper synthetic diamonds can also be processed.
- Good processing results were also achieved with the common coated diamond grades. This means that the cheapest variety can be used.
- a particularly advantageous wear resistance can be achieved when using diamond powder with a grain size of 20 to 200 ⁇ m.
- Wear parts can be found in a wide variety of applications.
- the first excellent results were achieved with water jet nozzles, drill bit inserts, saw teeth and drill tips. Due to its excellent thermal conductivity, especially when using a metallic phase based on Cu, Al or Ag, the material according to the invention is also particularly suitable for applications in which wear is associated with heat development. Only brake discs for airplanes, rail vehicles, automobiles and motorcycles are mentioned here as examples.
- a wide variety of processes can be used for the production. It is thus possible to compact diamond powder coated with a carbide-forming element with metal powder under temperature and pressure. This can be done, for example, in hot presses or hot isostatic presses. Infiltration has proven to be particularly advantageous.
- a precursor or intermediate is produced which can contain a binder in addition to diamond powder. Binders which pyrolyze to a high degree under the influence of temperature are particularly advantageous. advantageous
- Binder contents are 1 to 20% by weight.
- Diamond powder and binder are mixed in conventional mixers or mills.
- the shaping then takes place, this being supported by pouring into a mold or by pressure, for example by pressing or metal powder injection molding.
- the intermediate substance is subsequently heated to a temperature at which the binder at least partially pyrolyzes.
- the pyrolysis of the binder can also take place during the heating up in the infiltration process.
- the infiltration process can be pressure-free or pressure-supported. The latter can be done in a sinter-hip system or by means of squeeze casting.
- the liquidus temperature of the respective infiltrate alloy (alloy that infiltrates into the porous body) is not higher than 1400 ° C, advantageously not higher than 1200 ° C, since otherwise excessive amounts of diamond will decompose.
- An infiltrate with a eutectic composition is particularly suitable for infiltration.
- Synthetic diamond powder with an average grain size of 90 ⁇ m was made into a plate by means of die pressing at a pressure of 200 MPa
- the pore content of the plate was approximately 20% by volume.
- this plate was covered with a piece of the infiltrate alloy, which had already melted in an upstream process and whose liquidus and solidus temperature was determined by means of thermal analysis.
- the compositions of the infiltrate alloys are shown in Table 1.
- the porous diamond body and the infiltrate alloy were first heated in a sinter-hip system under vacuum to a temperature of 70 ° C above the liquidus temperature of the respective infiltrate alloy. After a holding time of 10 minutes, an argon gas pressure of 40 bar was set. After a further holding time of 5 minutes, the sample was cooled to room temperature by switching off the heating and under Ar gas flooding and subjected to a further one-hour heat treatment at 200 ° C. under the respective non-variance temperature.
- a carbidic phase enveloping the diamond grains was formed in all of the variants examined.
- the diamond composites according to the invention were subjected to a sandblasting test and with hard metal with a Co content of 2% by weight. compared.
- the removal rates based on the reference hard metal are shown in Table 1.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Ceramic Engineering (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT0038604U AT7492U1 (de) | 2004-06-01 | 2004-06-01 | Verschleissteil aus einem diamanthaltigen verbundwerkstoff |
PCT/AT2005/000184 WO2005118901A1 (de) | 2004-06-01 | 2005-05-30 | Verschleissteil aus einem diamanthaltigen verbundwerkstoff |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1751320A1 true EP1751320A1 (de) | 2007-02-14 |
EP1751320B1 EP1751320B1 (de) | 2010-01-27 |
Family
ID=34140140
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP05743117A Not-in-force EP1751320B1 (de) | 2004-06-01 | 2005-05-30 | Verschleissteil aus einem diamanthaltigen verbundwerkstoff |
Country Status (10)
Country | Link |
---|---|
US (1) | US7879129B2 (de) |
EP (1) | EP1751320B1 (de) |
JP (1) | JP2008502794A (de) |
KR (1) | KR20070026550A (de) |
CN (1) | CN1961090B (de) |
AT (2) | AT7492U1 (de) |
DE (1) | DE502005008950D1 (de) |
IL (1) | IL179677A (de) |
WO (1) | WO2005118901A1 (de) |
ZA (1) | ZA200609866B (de) |
Families Citing this family (40)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US7488537B2 (en) | 2004-09-01 | 2009-02-10 | Radtke Robert P | Ceramic impregnated superabrasives |
EP2099944B1 (de) * | 2006-11-21 | 2012-07-11 | Element Six (Production) (Pty) Ltd. | Verfahren zum herstellen eines materials, das diamant und eine intermetallische verbindung enthält |
WO2008096314A2 (en) * | 2007-02-05 | 2008-08-14 | Element Six (Production) (Pty) Ltd | Polycrystalline diamond (pcd) materials |
DE102007024170A1 (de) * | 2007-05-24 | 2008-11-27 | Andreas Stihl Ag & Co. Kg | Handgeführtes Arbeitsgerät und Verfahren zur Herstellung einer Bremseinrichtung eines handgeführten Arbeitsgeräts |
US20100199573A1 (en) * | 2007-08-31 | 2010-08-12 | Charles Stephan Montross | Ultrahard diamond composites |
SE532992C2 (sv) * | 2007-11-08 | 2010-06-08 | Alfa Laval Corp Ab | Förfarande för framställning av en diamantkomposit, grönkropp, diamantkomposit samt användning av diamantkompositen |
CN101925430B (zh) * | 2008-01-22 | 2012-05-23 | 圣戈班磨料磨具有限公司 | 具有偏置齿槽的圆形锯片 |
KR101721818B1 (ko) * | 2008-07-17 | 2017-03-30 | 덴카 주식회사 | 알루미늄-다이아몬드계 복합체 및 그 제조 방법 |
US8568205B2 (en) | 2008-08-08 | 2013-10-29 | Saint-Gobain Abrasives, Inc. | Abrasive tools having a continuous metal phase for bonding an abrasive component to a carrier |
GB0816837D0 (en) * | 2008-09-15 | 2008-10-22 | Element Six Holding Gmbh | A Hard-Metal |
GB0816836D0 (en) * | 2008-09-15 | 2008-10-22 | Element Six Holding Gmbh | Steel wear part with hard facing |
US9139893B2 (en) * | 2008-12-22 | 2015-09-22 | Baker Hughes Incorporated | Methods of forming bodies for earth boring drilling tools comprising molding and sintering techniques |
US9097067B2 (en) * | 2009-02-12 | 2015-08-04 | Saint-Gobain Abrasives, Inc. | Abrasive tip for abrasive tool and method for forming and replacing thereof |
US8393939B2 (en) * | 2009-03-31 | 2013-03-12 | Saint-Gobain Abrasives, Inc. | Dust collection for an abrasive tool |
US8763617B2 (en) * | 2009-06-24 | 2014-07-01 | Saint-Gobain Abrasives, Inc. | Material removal systems and methods utilizing foam |
US8505654B2 (en) * | 2009-10-09 | 2013-08-13 | Element Six Limited | Polycrystalline diamond |
RU2562556C2 (ru) | 2009-12-31 | 2015-09-10 | Сэнт-Гобэн Эбрейзивс, Инк. | Абразивное изделие |
EP2593274B1 (de) | 2010-07-12 | 2017-03-29 | Saint-Gobain Abrasives, Inc. | Schleifartikel zur formung von industriematerialien |
US8651203B2 (en) * | 2011-02-17 | 2014-02-18 | Baker Hughes Incorporated | Polycrystalline compacts including metallic alloy compositions in interstitial spaces between grains of hard material, cutting elements and earth-boring tools including such polycrystalline compacts, and related methods |
US9868099B2 (en) | 2011-04-21 | 2018-01-16 | Baker Hughes Incorporated | Methods for forming polycrystalline materials including providing material with superabrasive grains prior to HPHT processing |
US20130098691A1 (en) | 2011-10-25 | 2013-04-25 | Longyear Tm, Inc. | High-strength, high-hardness binders and drilling tools formed using the same |
CN103821456A (zh) * | 2014-02-28 | 2014-05-28 | 郑州神利达钻采设备有限公司 | 填坑式烧结金刚石钻头及其制造方法 |
CN105014554B (zh) * | 2015-05-25 | 2017-08-15 | 江苏锋泰工具有限公司 | 轻质高效金刚石磨轮的制备方法 |
CN104875131A (zh) * | 2015-05-28 | 2015-09-02 | 江苏耐尔特钻石有限公司 | 一种金刚石磨盘 |
WO2017011415A1 (en) * | 2015-07-16 | 2017-01-19 | Schlumberger Technology Corporation | Infiltrated cutting tools and related methods |
CN105312556B (zh) * | 2015-11-27 | 2016-08-24 | 泉州天智合金材料科技有限公司 | 一种金刚石工具用超细高抗弯强度合金粉末 |
US10287824B2 (en) | 2016-03-04 | 2019-05-14 | Baker Hughes Incorporated | Methods of forming polycrystalline diamond |
CN106041089B (zh) * | 2016-06-29 | 2018-05-22 | 沈阳昌普超硬精密工具有限公司 | 漫渗燃烧Ti-Al-Cu-Sn-Ni微孔金刚石砂轮的制造方法 |
US11396688B2 (en) | 2017-05-12 | 2022-07-26 | Baker Hughes Holdings Llc | Cutting elements, and related structures and earth-boring tools |
US11292750B2 (en) | 2017-05-12 | 2022-04-05 | Baker Hughes Holdings Llc | Cutting elements and structures |
CN108119138A (zh) * | 2017-11-17 | 2018-06-05 | 湖州南浔昊骏金属制品厂 | 一种耐磨煤截齿 |
EP3757240A4 (de) * | 2018-02-21 | 2021-11-17 | Sumitomo Electric Industries, Ltd. | Verbundmaterial und verfahren zur herstellung eines verbundmaterials |
US11536091B2 (en) | 2018-05-30 | 2022-12-27 | Baker Hughes Holding LLC | Cutting elements, and related earth-boring tools and methods |
CN109777352B (zh) * | 2019-02-25 | 2020-06-30 | 清华大学 | 超耐磨二维复合材料及其制备方法 |
JPWO2021192916A1 (de) * | 2020-03-24 | 2021-09-30 | ||
CN111451501B (zh) * | 2020-04-03 | 2021-12-21 | 季华实验室 | 一种基于共晶反应的激光增材制造钨零件的制备方法 |
CN112483030B (zh) * | 2020-10-23 | 2022-09-13 | 重庆宏工工程机械股份有限公司 | 一种便于冷却的取芯钻筒 |
WO2024026289A1 (en) * | 2022-07-26 | 2024-02-01 | Baker Hughes Oilfield Operations Llc | Cutting elements including binder materials having modulated morphologies, earth-boring tools including such cutting elements, and related methods of making and using same |
CN115283671B (zh) * | 2022-08-11 | 2023-09-29 | 中科粉研(河南)超硬材料有限公司 | 一种CuNiSn合金-镀钛金刚石磨具复合材料及其制备方法和应用 |
CN115896526A (zh) * | 2022-11-25 | 2023-04-04 | 国网山东省电力公司电力科学研究院 | 一种调控纳米多孔金形貌的分段控制脱合金法、纳米多孔金及应用 |
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DE69433253T2 (de) * | 1993-06-30 | 2004-08-12 | The University Of Sydney, Sydney | Herstellungsverfahren für evakuierte Verglasung |
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IL134575A (en) * | 1997-09-05 | 2004-07-25 | Skeleton Technologies Ag | Method of manufacturing a diamond-silicon carbide-silicon composite and a composite produced by this method |
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SE0301117L (sv) * | 2003-04-14 | 2004-10-15 | Skeleton Technologies Ag | Metod att tillverka en diamantkomposit |
-
2004
- 2004-06-01 AT AT0038604U patent/AT7492U1/de not_active IP Right Cessation
-
2005
- 2005-05-30 CN CN2005800177725A patent/CN1961090B/zh not_active Expired - Fee Related
- 2005-05-30 KR KR1020067025265A patent/KR20070026550A/ko not_active Application Discontinuation
- 2005-05-30 DE DE502005008950T patent/DE502005008950D1/de active Active
- 2005-05-30 AT AT05743117T patent/ATE456683T1/de active
- 2005-05-30 JP JP2007513592A patent/JP2008502794A/ja active Pending
- 2005-05-30 EP EP05743117A patent/EP1751320B1/de not_active Not-in-force
- 2005-05-30 WO PCT/AT2005/000184 patent/WO2005118901A1/de not_active Application Discontinuation
-
2006
- 2006-11-27 ZA ZA200609866A patent/ZA200609866B/xx unknown
- 2006-11-28 IL IL179677A patent/IL179677A/en not_active IP Right Cessation
- 2006-12-01 US US11/607,602 patent/US7879129B2/en not_active Expired - Fee Related
Non-Patent Citations (1)
Title |
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See references of WO2005118901A1 * |
Also Published As
Publication number | Publication date |
---|---|
DE502005008950D1 (de) | 2010-03-18 |
ZA200609866B (en) | 2009-05-27 |
CN1961090A (zh) | 2007-05-09 |
AT7492U1 (de) | 2005-04-25 |
JP2008502794A (ja) | 2008-01-31 |
KR20070026550A (ko) | 2007-03-08 |
US7879129B2 (en) | 2011-02-01 |
US20070092727A1 (en) | 2007-04-26 |
WO2005118901A1 (de) | 2005-12-15 |
IL179677A0 (en) | 2007-05-15 |
EP1751320B1 (de) | 2010-01-27 |
ATE456683T1 (de) | 2010-02-15 |
CN1961090B (zh) | 2010-12-08 |
IL179677A (en) | 2012-03-29 |
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