EP2641675A1 - Corps composite fritté comportant du carbure cimenté et des grains cBN - Google Patents

Corps composite fritté comportant du carbure cimenté et des grains cBN Download PDF

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Publication number
EP2641675A1
EP2641675A1 EP20120160972 EP12160972A EP2641675A1 EP 2641675 A1 EP2641675 A1 EP 2641675A1 EP 20120160972 EP20120160972 EP 20120160972 EP 12160972 A EP12160972 A EP 12160972A EP 2641675 A1 EP2641675 A1 EP 2641675A1
Authority
EP
European Patent Office
Prior art keywords
cbn
cemented carbide
sintered composite
composite body
depleted zone
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.)
Withdrawn
Application number
EP20120160972
Other languages
German (de)
English (en)
Inventor
Lei YIN
Alexander Hirsch
Yi Cui
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sandvik Intellectual Property AB
Original Assignee
Sandvik Intellectual Property AB
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sandvik Intellectual Property AB filed Critical Sandvik Intellectual Property AB
Priority to EP20120160972 priority Critical patent/EP2641675A1/fr
Priority to PCT/EP2013/054496 priority patent/WO2013139603A1/fr
Priority to US14/387,084 priority patent/US20150082963A1/en
Publication of EP2641675A1 publication Critical patent/EP2641675A1/fr
Withdrawn legal-status Critical Current

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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
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • 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
    • Y10T83/00—Cutting
    • Y10T83/929—Tool or tool with support
    • Y10T83/9319—Toothed blade or tooth therefor

Definitions

  • the present invention relates to a sintered composite body comprising cemented carbide and cBN grains, wherein the cBN grains are dispersed a cemented carbide matrix and wherein the mean cBN grain size is 1-20 ⁇ m and the cBN content is 0.3-4 wt%.
  • Cemented carbide components are used in a wide range of applications, especially in components subjected to extreme wear under abrasive conditions.
  • it is a commonly used material in several important components, from drilling bits to general wear parts.
  • the most important features of such components are a combination of high surface hardness and high toughness.
  • Cubic boron nitride is a superhard material surpassed only by diamond in hardness, which is widely used in demanding applications such as machining tools.
  • cBN is generally crystallographic stable at temperatures below 1400°C.
  • a problem with a material with increased wear resistance is that also the wear resistance during grinding is increased. Grinding is a common final treatment during production, aimed to achieve a desired shape and surface finish of a product, for example a cutting tool or a saw tooth. Due to an improved wear resistance this step can be costly and also demanding for certain geometries.
  • the present invention relates to a sintered composite body comprising cemented carbide and cBN grains, wherein the cBN grains are dispersed in a cemented carbide matrix , wherein said body comprises a cBN depleted zone 2 extending from the surface of the body and 50-400 ⁇ m, preferably 100-300 ⁇ m, towards the core of the body and the mean cBN grain size outside the depleted zone is 1-20 ⁇ m, preferably 1-10 ⁇ m, more preferably 2-8 ⁇ m, and the cBN content outside the depleted zone is 0.3-4 wt%, preferably 0.3-2 wt%, more preferably 0.5-1 wt%.
  • the cemented carbide matrix comprises hard constitutes in a metallic binder phase.
  • the binder phase can comprise one or more selected from the group of Co, Ni and Fe and the hard constitutes can comprise WC.
  • the cemented carbide can further comprise hard constitutes selected from borides, carbides, nitrides or carbonitrides of metals from groups 4, 5 or 6 of the periodic table, preferably tungsten, titanium, tantalium, niobium, chromium and/or vanadium.
  • the manufacturing of the sintered composite body typically comprises mixing and milling powders of the cemented carbide and cBN, pressing bodies of the powder to a desired shape and finally to sinter the pressed bodies to form dense bodies comprising cBN grains in a cemented carbide matrix.
  • the binder phase liquidize and enclose the hard constitutes and the cBN grains.
  • the depleted zone forms during the sintering step, which is disclosed in more detail below.
  • the milling, mixing and pressing steps can be performed with conventional methods as known in the art.
  • the cBN grain size does typically not change during the mixing, milling and pressing steps.
  • the surface of the cBN grain can be coated with a thin layer of a metal element, for example a thin Ti coating, to increase the wetting performance of the grain surface during the sintering step.
  • the body of the present invention can be of any shape, for example in the shape of a saw tooth, a drilling button or a wire drawing nib.
  • the core in the body is located inside the body.
  • the shape and extension of the core depends on the shape of the body.
  • the core in a spherical body the core can be a central point, in a body extended in on direction, the core can be extended, and in a ring shaped body, the core can be ring shaped or cylindrically shaped.
  • the cBN depleted zone is hereby meant an area that in SEM analyze at 750x magnification does show that the cBN grains, that normally appear as black spots or small areas in an otherwise continuous matrix of cemented carbide, are missing or depleted.
  • the depleted zone is essentially free of cBN grains and it extends from the surface of the body and down below the surface towards the core of the body. The area where the cBN grains are not depleted extends outside the depleted zone for example towards and through the core of the body.
  • One advantage with the sintered composite body according to the present invention is that the grinding of the surface of the body, i.e. grinding of the depleted zone, is more easy to perform due to that the hard particles of cBN are missing in the outer surface area of the material.
  • the depleted zone is less wear resistant than the cBN containing material in the core of the body.
  • Another advantage with the sintered composite body according to the present invention is that joining of the body to another body or material can be improved.
  • the strength of the weld i.e. the melt region
  • cBN grains are not preferred in a weld due to that cBN grains have a thermal mismatch with the cemented carbide matrix.
  • An advantage with an absence of cBN grains in the weld is that it leads to an absence of stresses due to said thermal mismatch.
  • the wettability of materials in the weld could be improved if no cBN is present.
  • cBN as a brittle phase is not present in the joint area. All of these facts lead to an improved joining strength if no cBN is present in the joint.
  • absence of cBN in the welding zone makes it possible to use existing production process parameters for welding and plating, thus reducing the production costs.
  • the extension of the depleted zone is 50-200 ⁇ m, preferably 100-200 ⁇ m. This is preferred in applications focusing on achieving a good surface finish and/or a small radius after surface or cutting edge grinding operations.
  • the extension of the depleted zone is 200-400 ⁇ m, preferably 200-300 ⁇ m. This is preferred in applications requiring high toughness to withstand initial impact. If such a body withstands the initial impact, it thereby has an increased chance to wear with a stable wear rate.
  • the cemented carbide comprises 6-16 wt% binder phase. In one embodiment of the present invention the binder phase comprises Co. In one embodiment of the present invention the cemented carbide comprises 10-14 wt% Co.
  • the cemented carbide comprises WC. In one embodiment of the present invention, the cemented carbide comprises 80-94 wt% WC. In one embodiment of the present invention the mean WC grain size is 0.5 to 8 ⁇ m, preferably 0.5 to 4 ⁇ m, most preferably 0.8 to 1.2 ⁇ m, as measured with linear intercept method in the sintered material.
  • the present invention relates to a wear part comprising the sintered composite body according to above.
  • of the present invention relates to saw tooth comprising the sintered composite body according as disclosed above.
  • the present invention further relates to the use of the sintered composite body in oil or gas applications, for example as a drilling button or an insert for a drilling head.
  • the present invention further relates to the use of the sintered composite body in wire drawing applications, for example as a wire drawing nib.
  • the composite body according to the present invention can be sintered in a sintering process in accordance with the settings as indicated below.
  • the sintering temperature is preferably 1250- 1360 °C, preferably 1300-1360 °C. At a too low sintering temperature, the material will not sinter. It is important to reach the melting point of the binder. A too high sintering temperature results in that the cBN grains decomposes into hBN, which is a less hard phase of BN.
  • the sintering temperature is preferably chosen to achieve full densified bodies and a gradient zone of a preferable depth.
  • the sintering can be performed in vacuum. Vacuum sintering is a standard process of production for many cemented carbide manufacturers.
  • the sintering can be performed using HIP (hot isostatic pressing).
  • HIP hot isostatic pressing
  • Sintering using a HIP is advantageous in that it leads to higher densities of the materials. It also enables a lower sintering temperature compared to what is possible at vacuum sintering, maintaining full densification of the material.
  • the sintering can for example be performed in a gas comprising Ar and/or N 2 .
  • the temperature is hold at a sintering temp during a dwelling time of preferably 10-80 minutes.
  • a too long sintering time can result in undesired grain growth of the cemented carbide.
  • a too short sintering time can result in not completely sintered material at the centre of a body.
  • the sintering time is suitably adjusted with regards to batch size, sintering equipment, cemented carbide composition, size of bodies, etc. to achieve dense sintered bodies with a preferable gradient depth.
  • cBN grain sizes Two cBN grain sizes were analyzed: 2-4 my and 4-8 my respectively.
  • the cBN grains were, as delivered from the manufacturer, coated with a thin coating of Ti.
  • the given size of the cBN grains is the size specified by the manufacturer.
  • the dry powder was pressed to a body of a bar with rectangular cross-section. As-pressed dimensions were about 25.5x8x6.5 mm.
  • the extension of the depleted zone is also dependent on the sintering pressure.
  • the sample A sintered at 5mbar had a smaller width of the depleted zone compared to the sample D sintered at 50 bar.
  • the sample F sintered at atmosphere pressure had a smaller width of the depleted zone compared to the sample G sintered at 50 bar.
  • Table 5 (sintering gas) Sample cBN grain size ( ⁇ m) Pressure (bar) Gas Temperature (°C) Time (min) Depleted zone ( ⁇ m) D 2-4 50 Ar 1360 70 280 G 2-4 50 N 2 1360 70 275
  • the sintering gas Ar or N2 did not have any clear diverging effect on the width of the depleted zone.
  • the depleted zone for sample D and G had about the same width of the depleted zone.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Ceramic Products (AREA)
  • Powder Metallurgy (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
EP20120160972 2012-03-23 2012-03-23 Corps composite fritté comportant du carbure cimenté et des grains cBN Withdrawn EP2641675A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP20120160972 EP2641675A1 (fr) 2012-03-23 2012-03-23 Corps composite fritté comportant du carbure cimenté et des grains cBN
PCT/EP2013/054496 WO2013139603A1 (fr) 2012-03-23 2013-03-06 Corps composite fritté comprenant du carbure cémenté et des grains de nitrure de bore cubique
US14/387,084 US20150082963A1 (en) 2012-03-23 2013-03-06 Sintered composite body comprising cemented carbide and cbn grains

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20120160972 EP2641675A1 (fr) 2012-03-23 2012-03-23 Corps composite fritté comportant du carbure cimenté et des grains cBN

Publications (1)

Publication Number Publication Date
EP2641675A1 true EP2641675A1 (fr) 2013-09-25

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EP20120160972 Withdrawn EP2641675A1 (fr) 2012-03-23 2012-03-23 Corps composite fritté comportant du carbure cimenté et des grains cBN

Country Status (3)

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US (1) US20150082963A1 (fr)
EP (1) EP2641675A1 (fr)
WO (1) WO2013139603A1 (fr)

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0256829A2 (fr) 1986-08-11 1988-02-24 De Beers Industrial Diamond Division (Proprietary) Limited Matériau abrasif et résistant à l'usure
EP2433727A1 (fr) * 2010-09-24 2012-03-28 Sandvik Intellectual Property AB Procédé de production d'un corps composite fritté

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5226404A (en) * 1989-09-22 1993-07-13 Mitsubishi Metal Corporation Cutting apparatus

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0256829A2 (fr) 1986-08-11 1988-02-24 De Beers Industrial Diamond Division (Proprietary) Limited Matériau abrasif et résistant à l'usure
EP2433727A1 (fr) * 2010-09-24 2012-03-28 Sandvik Intellectual Property AB Procédé de production d'un corps composite fritté

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Publication number Publication date
WO2013139603A1 (fr) 2013-09-26
US20150082963A1 (en) 2015-03-26

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