EP1422306A2 - Ti(C,N)-(Ti,Nb,W)(C,N)-Co pour uotils de coupe pour superfinition en tournage - Google Patents

Ti(C,N)-(Ti,Nb,W)(C,N)-Co pour uotils de coupe pour superfinition en tournage Download PDF

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Publication number
EP1422306A2
EP1422306A2 EP03445110A EP03445110A EP1422306A2 EP 1422306 A2 EP1422306 A2 EP 1422306A2 EP 03445110 A EP03445110 A EP 03445110A EP 03445110 A EP03445110 A EP 03445110A EP 1422306 A2 EP1422306 A2 EP 1422306A2
Authority
EP
European Patent Office
Prior art keywords
alloy
cores
undissolved
amount
hard
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
Application number
EP03445110A
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German (de)
English (en)
Other versions
EP1422306B1 (fr
EP1422306A3 (fr
Inventor
Marco Zwinkels
Gerold Weinl
Ulf Rolander
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
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Sandvik Intellectual Property AB
Sandvik AB
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Publication of EP1422306A3 publication Critical patent/EP1422306A3/fr
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    • 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
    • C22C29/04—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 carbonitrides
    • 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
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
    • 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

Definitions

  • the present invention relates to a sintered carbonitride alloy with Ti as the main component and a Ni-free binder phase which has improved properties particularly when used as cutting tool material in superfinishing turning operations particularly for superfinishing of steel and cast iron. More particularly, the present invention relates to a carbonitride-based alloy of specific composition, for which the amount of undissolved Ti(C,N) cores is optimized for maximal abrasive wear resistance, while the Co and Nb contents are simultaneously optimized to give the desired toughness and resistance to plastic deformation.
  • Titanium-based carbonitride alloys are produced by powder metallurgical methods and comprise carbonitride hard constituents embedded in a metallic binder phase.
  • the hard constituent grains generally have a complex structure with a core, most often surrounded by a rim of other composition.
  • group VIa elements normally both Mo and W are added to facilitate wetting between binder and hard constituents and to strengthen the binder by means of solution hardening.
  • Group IVa and/or Va elements e.g. Zr, Hf, V, Nb, and Ta, are also added in all commercial alloys available today.
  • the carbonitride forming elements are usually added as carbides, nitrides and/or carbonitrides.
  • the metallic binder may contain one or more of Ni, Co and Fe.
  • cermets Compared to WC-Co based materials, cermets have excellent chemical stability when in contact with hot steel, even if the cermet is uncoated, but have substantially lower strength. This makes them most suited for finishing operations, which generally are characterized by limited mechanical loads on the cutting edge and a high surface finish requirement on the finished component.
  • US 5,308,376 discloses a cermet in which at least 80 vol% of the hard phase constituents comprises core-rim structured particles having several, preferably at least two, different hard constituent types with respect to the composition of core and/or rim(s). These individual hard constituent types each consist of 10-80%, preferably 20-70% by volume of the total content of hard constituents.
  • EP-A-872 566 discloses a cermet in which particles of different core-rim ratios coexist.
  • particles forming the hard phase in the alloy have black core parts and peripheral parts which are located around the black core parts to appear grey.
  • Some particles have black core parts occupying areas of at least 30 % of the overall particles referred to as big cores and some have the black core parts occupying areas of less than 30 % of the overall particle area are referred to as small cores.
  • the amount of particles having big cores is 30-80 % of total number of particles with cores.
  • US 6,004,371 discloses a cermet comprising different microstructural components, namely cores which are remnants of and have a metal composition determined by the raw material powder, tungsten-rich cores formed during the sintering, outer rims with intermediate tungsten content formed during the sintering and a binder phase of a solid solution of at least titanium and tungsten in cobalt. Toughness and wear resistance are varied by adding WC, (Ti,W)C, and/or (Ti,W)(C,N) in varying amounts as raw materials.
  • abrasive wear resistance was maximized for a given level of toughness and resistance to plastic deformation by optimizing the amount of undissolved Ti(C,N) cores.
  • the amount of undissolved Ti(C,N) cores can be varied independently from other parameters, such as Nb and binder content. Hence, it has been possible to simultaneously optimize all three main cutting performance criteria, i.e. toughness, abrasive wear resistance and resistance to plastic deformation.
  • Fig. 1 shows the microstructure of an alloy according to the invention in which
  • the present invention provides a titanium based carbonitride alloy containing Ti, Nb, W, C, N and Co, which is particularly useful for superfinishing operations.
  • a titanium based carbonitride alloy containing Ti, Nb, W, C, N and Co, which is particularly useful for superfinishing operations.
  • the structure When observed in back scattering mode in a scanning electron microscope the structure has black cores of Ti(C,N), A, a grey complex carbonitride phase, B, sometimes surrounding the A-cores and an almost white Co binder phase, C, as depicted in Fig. 1.
  • the abrasive wear resistance could be maximized for a given level of toughness and resistance to plastic deformation by optimizing the amount of undissolved Ti(C,N)-cores (A).
  • a large amount of undissolved cores is favourable for the abrasive wear resistance.
  • the maximum amount of these cores is limited by the demand for sufficient toughness for a specific application since toughness decreases at high levels of undissolved cores. This amount must therefore be kept between 26 and 37 vol% of the hard constituents, preferably 27 and 35 vol%, most preferably 28 and 32 vol%, the balance being one or more complex carbonitride phases containing Ti, Nb and W.
  • composition of the Ti(C,N)-cores can be more closely defined as TiC x N 1-x .
  • the C/(C+N) atomic ratio, x, in these cores should be in the range 0.46-0.70, preferably 0.52-0.64, most preferably 0.55-0.61.
  • the overall C/(C+N) ratio in the sintered alloy should be in the range 0.50-0.75.
  • the average grain size of the undissolved cores, A should be 0.1-2 ⁇ m and the average grain size of the hard phase including the undissolved cores 0.5-3 ⁇ m.
  • the Nb and Co contents should be chosen properly to give the desired properties for an envisioned application area.
  • the W content should be 3 to 8 at%, preferably less than 4 at%, to avoid an unacceptably high porosity level.
  • the body of the present invention For cutting operations requiring extremely high wear resistance it is advantageous to coat the body of the present invention with a thin wear resistant coating using PVD, CVD, MTCVD or similar techniques. It should be noted that the composition of the insert is such that any of the coatings and coating techniques used today for WC-Co based materials or cermets may be directly applied, though of course the choice of coating will also influence the deformation resistance and toughness of the material.
  • a method of manufacturing a sintered titanium-based carbonitride alloy in which hard constituent powders of TiC x N 1-x , wherein x is 0.46-0.70, preferably 0.52-0.64, most preferably 0.55-0.61, NbC and WC, are mixed with powder of Co to a composition as defined above and pressed into bodies of desired shape. Sintering is performed in a N 2 -CO-Ar atmosphere at a temperature of 1370-1500 C for 1.5-2h, preferably using the technique described in EP-A-1052297.
  • the amount of Ti(C,N) powder should be 50-70 wt-%, its grain size 1-3 ⁇ m and the sintering temperature and sintering time have to be chosen adequately. It is within the purview of the skilled artisan to determine by experiments the conditions necessary to obtain the desired microstructure according to this specification.
  • the powder was spray dried and pressed into TNMG160408-PF inserts.
  • the green bodies were dewaxed in H 2 and subsequently sintered in a N 2 -CO-Ar atmosphere for 1.5 h at 1480 °C according to EP-A-1052297, which was followed by suitable edge treatment.
  • Polished cross sections of inserts were prepared by standard metallographic techniques and characterized using scanning electron microscopy.
  • Fig. 1 shows a scanning electron micrograph of such a cross section, taken in back scattering mode. As indicated in Fig. 1, the black particles (A) are the undissolved Ti(C,N) cores and the light grey areas (C) are the binder phase.
  • the remaining grey particles (B) are the part of the hard constituents consisting of carbonitrides containing Ti, Nb and W. Using image analysis, the amount of undissolved Ti(C,N) cores was determined to be 29.4 vol% of the hard constituents.
  • Inserts of a prior art composition were manufactured and characterized in the same manner as described in Example 1.
  • the composition of Alloy B is (at %) Ti 39.4, W 3.9, Ta 3.7, Co 6.2 with a N/(N+C) ratio of 0.38. Characterization was carried out in the same manner as described in Example 1. Using image analysis, the amount of undissolved Ti(C,N) cores was determined to be 36.2% of the hard constituents.
  • Alloy C of the same nominal composition as Alloy A was produced and characterized in an identical manner except for the sintering temperature which was 1510 °C. Using image analysis, the amount of undissolved Ti(C,N) cores was determined to be 25.0 vol% of the hard constituents.
  • Plastic deformation resistance for Alloys A and C was determined in a test with facing towards centre in a tube blank, with the following cutting data:

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Adornments (AREA)
  • Physical Vapour Deposition (AREA)
  • Powder Metallurgy (AREA)
  • Turning (AREA)
EP03445110A 2002-11-19 2003-10-10 Ti(C,N)-(Ti,Nb,W)(C,N)-Co pour outils de coupe pour superfinition en tournage Expired - Lifetime EP1422306B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0203407A SE526180C3 (sv) 2002-11-19 2002-11-19 Ti (C,N) - (Ti,Nb,W) (C,N) -Co-legering för svarvskärtillämpningar för lätt finbearbetning
SE0203407 2002-11-19

Publications (3)

Publication Number Publication Date
EP1422306A2 true EP1422306A2 (fr) 2004-05-26
EP1422306A3 EP1422306A3 (fr) 2006-04-12
EP1422306B1 EP1422306B1 (fr) 2009-05-20

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EP03445110A Expired - Lifetime EP1422306B1 (fr) 2002-11-19 2003-10-10 Ti(C,N)-(Ti,Nb,W)(C,N)-Co pour outils de coupe pour superfinition en tournage

Country Status (6)

Country Link
EP (1) EP1422306B1 (fr)
JP (1) JP2004169186A (fr)
KR (1) KR20040044157A (fr)
AT (1) ATE431858T1 (fr)
DE (1) DE60327682D1 (fr)
SE (1) SE526180C3 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101251599B1 (ko) * 2009-12-30 2013-04-08 한국야금 주식회사 절삭공구용 소결체 및 이의 제조방법

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1052297A1 (fr) * 1999-05-03 2000-11-15 Sandvik Aktiebolag Procédé de fabrication une alliage de Ti(C,N)-(Ti,Ta,W)(C,N)-Co pour outil de coupe
EP1052300A1 (fr) * 1999-05-03 2000-11-15 Sandvik Aktiebolag Alliage Ti(C,N) - (Ti,Ta,W) (C,N) - Co pour des applications exigeant une tenacité supérieure dans les outils de coupe

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61147823A (ja) * 1984-12-21 1986-07-05 Mitsubishi Metal Corp 高強度窒素含有超硬合金の製造方法
JPH02205654A (ja) * 1989-02-01 1990-08-15 Nippon Carbide Ind Co Inc 硬質合金
JP3199407B2 (ja) * 1991-09-26 2001-08-20 京セラ株式会社 ＴｉＣＮ基サーメット
JPH0641671A (ja) * 1992-05-26 1994-02-15 Kyocera Corp ウイスカー強化サーメット
JP3198680B2 (ja) * 1992-11-16 2001-08-13 三菱マテリアル株式会社 耐摩耗性のすぐれたＴｉ系炭窒化物基サーメット製切削工具
JPH11124649A (ja) * 1997-10-21 1999-05-11 Toshiba Tungaloy Co Ltd 炭化タングステン系超硬合金製金型用部品

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1052297A1 (fr) * 1999-05-03 2000-11-15 Sandvik Aktiebolag Procédé de fabrication une alliage de Ti(C,N)-(Ti,Ta,W)(C,N)-Co pour outil de coupe
EP1052300A1 (fr) * 1999-05-03 2000-11-15 Sandvik Aktiebolag Alliage Ti(C,N) - (Ti,Ta,W) (C,N) - Co pour des applications exigeant une tenacité supérieure dans les outils de coupe

Also Published As

Publication number Publication date
EP1422306B1 (fr) 2009-05-20
SE0203407L (sv) 2004-05-20
SE526180C3 (sv) 2005-08-03
JP2004169186A (ja) 2004-06-17
EP1422306A3 (fr) 2006-04-12
KR20040044157A (ko) 2004-05-27
ATE431858T1 (de) 2009-06-15
SE0203407D0 (sv) 2002-11-19
SE526180C2 (sv) 2005-07-19
DE60327682D1 (de) 2009-07-02

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