WO1998016665A1 - Method of making cemented carbide with binder phase enriched surface zone - Google Patents

Method of making cemented carbide with binder phase enriched surface zone Download PDF

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Publication number
WO1998016665A1
WO1998016665A1 PCT/SE1997/001690 SE9701690W WO9816665A1 WO 1998016665 A1 WO1998016665 A1 WO 1998016665A1 SE 9701690 W SE9701690 W SE 9701690W WO 9816665 A1 WO9816665 A1 WO 9816665A1
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WO
WIPO (PCT)
Prior art keywords
binder phase
atom
nitrogen
phase
surface zone
Prior art date
Application number
PCT/SE1997/001690
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French (fr)
Inventor
Per Lindskog
Per Gustafson
Original Assignee
Sandvik Ab (Publ)
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Filing date
Publication date
Application filed by Sandvik Ab (Publ) filed Critical Sandvik Ab (Publ)
Priority to US09/242,683 priority Critical patent/US6299992B1/en
Priority to AT97945149T priority patent/ATE231930T1/en
Priority to DE69718805T priority patent/DE69718805T2/en
Priority to EP97945149A priority patent/EP0931171B1/en
Priority to JP51825998A priority patent/JP3934160B2/en
Publication of WO1998016665A1 publication Critical patent/WO1998016665A1/en

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    • 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
    • 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
    • B22F3/10—Sintering only
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • B22F3/101—Changing atmosphere
    • 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
    • B22F2201/00—Treatment under specific atmosphere
    • B22F2201/02—Nitrogen
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • 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
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12014—All metal or with adjacent metals having metal particles
    • Y10T428/12028—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, etc.]
    • Y10T428/12049—Nonmetal component
    • Y10T428/12056—Entirely inorganic

Definitions

  • the present invention relates to coated cemented carbide inserts with unique edge security in sticky work piece materials such as stainless steel, achieved with a binder phase enriched surface zone extending over the edge.
  • Coated cemented carbide inserts with binder phase enriched surface zone are today used to a great extent for machining of steel and stainless materials. Thanks to the binder phase enriched surface zone, an extension of the application area for the cutting material has been obtained.
  • Methods or processes to make cemented carbide containing WC, cubic phase (gamma-phase) and binder phase with binder phase enriched surface zones are known through a number of patents and patent application. According to e.g. US Patents 4,277,283 and 4,610,931 nitrogen containing additions are used and sintering takes place in vacuum whereas according to US Patent 4,548,786 the nitrogen is added in gas phase. Hereby in both cases a binder phase enriched surface zone essentially free of cubic phase is obtained. US Patent 4,830,930 describes a binder phase enrichment obtained through decarburization after the sintering whereby a binder phase enrichment is obtained which also contains cubic phase.
  • the thickness of the binder phase enriched zone decreases towards sharp corners, such as the cutting edge of a cutting insert, and that a brittle binder phase depleted zone, enriched in cubic phase, is present in the edge area and often limits the use of binder phase enriched cemented carbides especially in work piece materials with high demands on edge toughness .
  • edges of a cutting insert has to be edge rounded to a certain radius of the order of 50-100 ⁇ or less in order to be useful.
  • the edge rounding is generally made after sintering by an edge rounding operation. In this operation the thin outermost binder phase enriched zone is completely removed and the hard, brittle area is exposed. As a result a hard but brittle edge is obtained resulting in an increased risk for problems with brittleness in the edge particularly in applications demanding high edge toughness.
  • EP-A-0569696 A method of maintaining the binder phase enriched zone in the edge portion of a cemented carbide insert is disclosed in EP-A-0569696. According to this application this effect is obtained if Zr and/or Hf is present in the cemented carbide .
  • the thickness of the binder phase enriched surface zone can be maintained over the edge also in cemented carbide free of Hf and Zr if certain conditions are fulfilled particularly with regard to the titanium and nitrogen content within the cubic phase as well as the overall carbon content.
  • a favourable influence on the edge toughness in sticky materials such as austenitic stainless steel can thereby be obtained.
  • the binder phase enriched zones according to this application often becomes to deep and difficult to control. It is an therefore an object of the present invention to provide a method of making a cemented carbide insert allowing a better control of the thickness of the binder phase enriched zone.
  • a cemented carbide insert comprising a cemented carbide substrate and a coating.
  • the substrate contains WC and cubic carbonitride phase in a binder phase based of Co and/or Ni and has a binder phase enriched surface zone essentially free of cubic phase.
  • the binder phase enriched surface zone prevails over the edge.
  • an insert according to the invention has improved edge toughness and is particularly useful for machining of sticky work piece materials such as stainless steel. (Although the cubic phase is essentially a carbonitride phase the material is herein referred to as a cemented carbide . )
  • Fig. 1 shows in 80OX the binder phase enriched zone under a cutting edge rounded to a 50 ⁇ m radius in a coated cemented carbide according to the invention. It has now surprisingly been found that by performing part of the sintering under nitrogen pressure the thickness of the binder phase enriched surface zone can be controlled with gradient prevailing in the vicinity of the edge.
  • the invention thus, relates to a method of making cutting inserts comprising a cemented carbide substrate consisting of a binder phase of Co and/or Ni , WC and a cubic carbonitride phase with a binder phase enriched surface zone essentially free of cubic phase and a coating.
  • Ta and/or Nb is/are added as carbides whereas Ti is added as TiC, TiCN and/or TiN in such proportions that the nitrogen content of the carbonitride phase expressed as x in the formula, (Ti,Nb,Ta) (N ⁇ C _ x ) shall be >0.2, preferably 0.3-0.4.
  • the powder mixture is mixed with pressing agent and possibly carbon such that the carbon content is 0-0.15, preferably 0.05-0.15, weight-%, above the stoichiometric content and the mixture is milled and dried to obtain a powder material. Next, the powder material is compacted and sintered.
  • nitrogen gas may be supplied to the furnace at 0-500 mbar, preferably 10-40 mbar, in order to prevent denitrification prior to pore closure at temperatures above 1200°C.
  • Sintering is performed at a temperature of 1380-1520°C, in a protective atmosphere consisting essentially of nitrogen, the nitrogen pressure adjusted to impede gradient growth, with a period of sintering in an atmosphere without nitrogen, the time of this period adjusted to obtain the gradient zone depth desired.
  • the nitrogen pressure required to impede gradient growth depends on composition of the carbide body, sintering temperature and on the furnace used.
  • the time required in atmosphere without nitrogen addition depends on sintering temperature and furnace used.
  • Cooling can be performed according to standard practice or as disclosed in US 5,484,468. After conventional post sintering treatments including edgerounding a hard, wear resistant coating according to above is applied by CVD- , PVD- or MT-CVD-technique .
  • the present invention also relates to a cutting insert comprising a cemented carbide substrate with a binder phase enriched surface zone and a coating, said substrate consisting of a binder phase of Co and/or Ni , WC and a cubic carbonitride of W , Ti and at least one of the metals Ta, Nb, Mo, V, or Cr with a binder phase enriched surface zone being essentially free of cubic phase .
  • the cemented carbide contains 6-14 atom- %, most preferably 8-11 atom-%, binder phase, 3-8 atom- %, most preferably 4-6 atom-%, of Ti and at least one of Ta and Nb and rest WC .
  • the average WC grain size shall be between 1.0 and 4 ⁇ m, preferably between 1.5 and 3 ⁇ m.
  • the Ti/ (Ta+Nb) atomic ratio in the carbonitride phase shall be >2 , preferably >3 , with a nitrogen content expressed as x in the formula, (Ti,Nb,Ta) (N x ,C ⁇ _ x ) shall be >0.2, preferably between 0.3 and 0.4.
  • the depth of the binder phase enriched surface zone close to the edge increases with increased titanium and nitrogen content within the cubic phase and with increased overall carbon content.
  • the maximum nitrogen content that can be used in practice is mainly limited by the increased tendency for A and B type of porosity with increased nitrogen content. However, the maximum nitrogen content can be extended over the above stated limit if the sintering is performed in an inert atmosphere under high pressure.
  • the maximum carbon content that can be used in practice is mainly limited by an increased tendency for carbon precipitation in the binder phase enriched surface zone, reduced coating adhesion and reduced deformation resistance.
  • the carbon content shall correspond to a C-porosity better than CO8, preferably COO just below carbon saturation.
  • the thickness of the binder phase enriched surface zone shall be 1. below a flat surface 15-45 ⁇ m, preferably 25-35 ⁇ m
  • the gradient zone depth close to the edge depends on the geometry, a blunt, 90 degrees or more, geometry giving deeper gradient zones .
  • Inserts according to the invention shall preferably have a coating of TiC, TiCN and/or TiN with a total coating thickness of 3-10 ⁇ m, most preferably 4-8 ⁇ m, possibly in combination with an AI2O3 coating with a thickness of 1-4 ⁇ m, most preferably 1.5-3 ⁇ m.
  • Other coatings known in the art can also be used such as single or multiple layers of at least one carbide, nitride, carbonitride, oxide or boride of at least one metal of the groups I b, VB and VIB of the periodic table and/or aluminium oxide by known CVD- , PVD- or MT- CVD-methods .
  • the structure in the surface of the cutting inserts consisted of a 30 ⁇ m thick binder phase enriched zone below the flat flank face with a minimum if 25 ⁇ m close to the edge .
  • the structure in the surface of the cutting inserts consisted of a 33 ⁇ m thick binder phase enriched zone below the flat flank face with a minimum if 23 ⁇ m close to the edge .
  • CNMG120408 were pressed.
  • the inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1200°C, and after that with a protective gas of 40 mbar nitrogen up to 1380°C the furnace was then evacuated and filled with argon to 40 mbar heated to sintering temperature, 1450°C, and held there for 1 hour and then cooled.
  • the structure in the surface of the cutting inserts consisted of a 46 ⁇ m thick binder phase enriched zone below the flat flank face with a minimum if 30 ⁇ m close to the edge .
  • the structure in the surface of the cutting inserts consisted of a 40 ⁇ m thick binder phase enriched zone below the flat flank face with a minimum if 26 ⁇ m close to the edge .
  • Examples 1 and 2 show that it is possible to control the depth of the gradient zone without loosing the desired gradient in the vicinity of the edge as in example 5.
  • Examples 3 and 4 show that the gradient zone may grow excessively without nitrogen addition under a part of the sintering.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Powder Metallurgy (AREA)
  • Ceramic Products (AREA)
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Abstract

The present invention relates to method of making a cemented carbide insert, comprising a cemented carbide substrate and a coating. The substrate contains WC and cubic carbonitride phase in a binder phase based of Co and/or Ni and has a binder phase enriched surface zone essentially free of cubic phase. The binder phase enriched surface zone prevails over the edge. By sintering in an atmosphere essentially consisting of nitrogen the thickness of the binder phase enriched zone can be controlled.

Description

Method of making cemented carbide with binder phase enriched surface zone
The present invention relates to coated cemented carbide inserts with unique edge security in sticky work piece materials such as stainless steel, achieved with a binder phase enriched surface zone extending over the edge.
Coated cemented carbide inserts with binder phase enriched surface zone are today used to a great extent for machining of steel and stainless materials. Thanks to the binder phase enriched surface zone, an extension of the application area for the cutting material has been obtained. Methods or processes to make cemented carbide containing WC, cubic phase (gamma-phase) and binder phase with binder phase enriched surface zones are known through a number of patents and patent application. According to e.g. US Patents 4,277,283 and 4,610,931 nitrogen containing additions are used and sintering takes place in vacuum whereas according to US Patent 4,548,786 the nitrogen is added in gas phase. Hereby in both cases a binder phase enriched surface zone essentially free of cubic phase is obtained. US Patent 4,830,930 describes a binder phase enrichment obtained through decarburization after the sintering whereby a binder phase enrichment is obtained which also contains cubic phase.
It is well known in the art that the thickness of the binder phase enriched zone decreases towards sharp corners, such as the cutting edge of a cutting insert, and that a brittle binder phase depleted zone, enriched in cubic phase, is present in the edge area and often limits the use of binder phase enriched cemented carbides especially in work piece materials with high demands on edge toughness .
However, the edges of a cutting insert has to be edge rounded to a certain radius of the order of 50-100 μ or less in order to be useful. The edge rounding is generally made after sintering by an edge rounding operation. In this operation the thin outermost binder phase enriched zone is completely removed and the hard, brittle area is exposed. As a result a hard but brittle edge is obtained resulting in an increased risk for problems with brittleness in the edge particularly in applications demanding high edge toughness.
One method of reducing this drawback of binder phase enriched sintered cemented carbides is described in US 5,484,468. This method is, however, not sufficient in very difficult work piece materials such as austenitic stainless steel and may result in an unwanted decrease in the deformation resistance.
A method of maintaining the binder phase enriched zone in the edge portion of a cemented carbide insert is disclosed in EP-A-0569696. According to this application this effect is obtained if Zr and/or Hf is present in the cemented carbide .
According to Swedish Patent application SE 9501383-5 the thickness of the binder phase enriched surface zone can be maintained over the edge also in cemented carbide free of Hf and Zr if certain conditions are fulfilled particularly with regard to the titanium and nitrogen content within the cubic phase as well as the overall carbon content. A favourable influence on the edge toughness in sticky materials such as austenitic stainless steel can thereby be obtained. However, the binder phase enriched zones according to this application often becomes to deep and difficult to control. It is an therefore an object of the present invention to provide a method of making a cemented carbide insert allowing a better control of the thickness of the binder phase enriched zone. According to the presently claimed invention there is provided a cemented carbide insert, comprising a cemented carbide substrate and a coating. The substrate contains WC and cubic carbonitride phase in a binder phase based of Co and/or Ni and has a binder phase enriched surface zone essentially free of cubic phase.
The binder phase enriched surface zone prevails over the edge. As a result an insert according to the invention has improved edge toughness and is particularly useful for machining of sticky work piece materials such as stainless steel. (Although the cubic phase is essentially a carbonitride phase the material is herein referred to as a cemented carbide . )
Fig. 1 shows in 80OX the binder phase enriched zone under a cutting edge rounded to a 50 μm radius in a coated cemented carbide according to the invention. It has now surprisingly been found that by performing part of the sintering under nitrogen pressure the thickness of the binder phase enriched surface zone can be controlled with gradient prevailing in the vicinity of the edge.
The invention, thus, relates to a method of making cutting inserts comprising a cemented carbide substrate consisting of a binder phase of Co and/or Ni , WC and a cubic carbonitride phase with a binder phase enriched surface zone essentially free of cubic phase and a coating. A powder mixture containing WC, 6-14 atom-%, preferably 8-11 atom-% binder phase and 3-8 atom-%, preferably 4-6 atom-% of Ti and at least one of Ta and Nb such that the Ti/ (Ta+Nb) atomic ratio is >2 , preferably >3. Ta and/or Nb is/are added as carbides whereas Ti is added as TiC, TiCN and/or TiN in such proportions that the nitrogen content of the carbonitride phase expressed as x in the formula, (Ti,Nb,Ta) (Nχ C _x) shall be >0.2, preferably 0.3-0.4. The powder mixture is mixed with pressing agent and possibly carbon such that the carbon content is 0-0.15, preferably 0.05-0.15, weight-%, above the stoichiometric content and the mixture is milled and dried to obtain a powder material. Next, the powder material is compacted and sintered. During heating to sintering nitrogen gas may be supplied to the furnace at 0-500 mbar, preferably 10-40 mbar, in order to prevent denitrification prior to pore closure at temperatures above 1200°C. Sintering is performed at a temperature of 1380-1520°C, in a protective atmosphere consisting essentially of nitrogen, the nitrogen pressure adjusted to impede gradient growth, with a period of sintering in an atmosphere without nitrogen, the time of this period adjusted to obtain the gradient zone depth desired. The nitrogen pressure required to impede gradient growth depends on composition of the carbide body, sintering temperature and on the furnace used. The time required in atmosphere without nitrogen addition depends on sintering temperature and furnace used. It is within the purview of the skilled artisan to determine whether the requisite binder phase enrichment has been obtained and to modify the sintering conditions in accordance with the present specification, if desired, to effect the desired binder phase enrichment. Cooling can be performed according to standard practice or as disclosed in US 5,484,468. After conventional post sintering treatments including edgerounding a hard, wear resistant coating according to above is applied by CVD- , PVD- or MT-CVD-technique . The present invention also relates to a cutting insert comprising a cemented carbide substrate with a binder phase enriched surface zone and a coating, said substrate consisting of a binder phase of Co and/or Ni , WC and a cubic carbonitride of W , Ti and at least one of the metals Ta, Nb, Mo, V, or Cr with a binder phase enriched surface zone being essentially free of cubic phase .
Preferably the cemented carbide contains 6-14 atom- %, most preferably 8-11 atom-%, binder phase, 3-8 atom- %, most preferably 4-6 atom-%, of Ti and at least one of Ta and Nb and rest WC . The average WC grain size shall be between 1.0 and 4 μm, preferably between 1.5 and 3 μm. The Ti/ (Ta+Nb) atomic ratio in the carbonitride phase shall be >2 , preferably >3 , with a nitrogen content expressed as x in the formula, (Ti,Nb,Ta) (Nx,Cι_ x) shall be >0.2, preferably between 0.3 and 0.4. The depth of the binder phase enriched surface zone close to the edge increases with increased titanium and nitrogen content within the cubic phase and with increased overall carbon content. The maximum nitrogen content that can be used in practice is mainly limited by the increased tendency for A and B type of porosity with increased nitrogen content. However, the maximum nitrogen content can be extended over the above stated limit if the sintering is performed in an inert atmosphere under high pressure. The maximum carbon content that can be used in practice is mainly limited by an increased tendency for carbon precipitation in the binder phase enriched surface zone, reduced coating adhesion and reduced deformation resistance. The carbon content shall correspond to a C-porosity better than CO8, preferably COO just below carbon saturation.
The thickness of the binder phase enriched surface zone shall be 1. below a flat surface 15-45 μm, preferably 25-35 μm
2. close to a sharp edge, before edge rounding, measured perpendicular to the same flat surface as in 1. above, 0.5-1.2 times the gradient zone in 1. above, preferably 0.67-1.2 times the gradient zone in 1. above .
3. at the edge after edge rounding 5-30 μm, preferably 10-25 μm. The gradient zone depth close to the edge depends on the geometry, a blunt, 90 degrees or more, geometry giving deeper gradient zones .
Inserts according to the invention shall preferably have a coating of TiC, TiCN and/or TiN with a total coating thickness of 3-10 μm, most preferably 4-8 μm, possibly in combination with an AI2O3 coating with a thickness of 1-4 μm, most preferably 1.5-3 μm. Other coatings known in the art can also be used such as single or multiple layers of at least one carbide, nitride, carbonitride, oxide or boride of at least one metal of the groups I b, VB and VIB of the periodic table and/or aluminium oxide by known CVD- , PVD- or MT- CVD-methods .
Example 1 (according to invention)
From a powder mixture comprising 1.69 weight-% TiC, 1.28 weight-% TiN, 1.21 weight-% TaC, 0.76 weight-% NbC, 7.5 weight-% Co, and balance WC with 0.12 weight-% overstoichiometric carbon content, turning inserts CNMG120408 were pressed. The inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1200°C, and after that with a protective gas of 40 mbar nitrogen up to 1380°C the furnace was then evacuated and filled with nitrogen to 60 mbar and heated to sintering temperature, 1450°C, and held there for 60 minutes, during these 60 minutes the furnace was evacuated for 15 in and then refilled with nitrogen.
The structure in the surface of the cutting inserts consisted of a 30 μm thick binder phase enriched zone below the flat flank face with a minimum if 25 μm close to the edge .
Example 2 (according to invention)
From a powder mixture comprising 1.69 weight-% TiC, 1.28 weight-% TiN, 1.21 weight-% TaC, 0.76 weight-% NbC, 7.5 weight-% Co, and balance WC with 0.12 weight-% overstoichiometric carbon content, turning inserts CNMG120408 were pressed. The inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1200°C, and after that with a protective gas of 40 mbar nitrogen up to 1380°C the furnace was then evacuated and filled with nitrogen to 200 mbar heated to sintering temperature, 1450°C, and held there for 10 minutes and then cooled to 1380°C, evacuated and held at 1380°C for 50 minutes and then cooled.
The structure in the surface of the cutting inserts consisted of a 33 μm thick binder phase enriched zone below the flat flank face with a minimum if 23 μm close to the edge .
Example 3 (prior art)
From a powder mixture comprising 1.69 weight-% TiC, 1.28 weight-% TiN, 1.21 weight-% TaC, 0.76 weight-% NbC, 7.5 weight-% Co, and balance WC with 0.12 weight-% overstoichiometric carbon content, turning inserts
CNMG120408 were pressed. The inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1200°C, and after that with a protective gas of 40 mbar nitrogen up to 1380°C the furnace was then evacuated and filled with argon to 40 mbar heated to sintering temperature, 1450°C, and held there for 1 hour and then cooled.
The structure in the surface of the cutting inserts consisted of a 46 μm thick binder phase enriched zone below the flat flank face with a minimum if 30 μm close to the edge .
Example 4 (prior art)
From a powder mixture comprising 1.69 weight-% TiC, 1.28 weight-% TiN, 1.21 weight-% TaC, 0.76 weight-% NbC, 7.5 weight-% Co, and balance WC with 0.12 weight-% overstoichiometric carbon content, turning inserts CNMG120408 were pressed. The inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1380°C the furnace was then filled with argon to 40 mbar heated to sintering temperature, 1410°C, and held there for 1 hour and then cooled.
The structure in the surface of the cutting inserts consisted of a 40 μm thick binder phase enriched zone below the flat flank face with a minimum if 26 μm close to the edge .
Example 5 (comparative)
From a powder mixture comprising 1.69 weight-% TiC, 1.28 weight-% TiN, 1.21 weight-% TaC, 0.76 weight-% NbC, 7.5 weight-% Co, and balance WC with 0.12 weight-% overstoichiometric carbon content, turning inserts CNMG120408 were pressed. The inserts were sintered with H2 up to 450°C for dewaxing, further in vacuum to 1200°C, and after that with a protective gas of 40 mbar nitrogen up to 1380°C the furnace was then evacuated and filled with nitrogen to 100 mbar heated to sintering temperature, 1450°C, and held there for 1 hour and then cooled. The structure in the surface of the cutting inserts consisted of a 26 μm thick binder phase enriched zone below the flat flank face with a minimum if 12 μm close to the edge.
Examples 1 and 2 show that it is possible to control the depth of the gradient zone without loosing the desired gradient in the vicinity of the edge as in example 5. Examples 3 and 4 show that the gradient zone may grow excessively without nitrogen addition under a part of the sintering.

Claims

Claims
1. Method of making a cutting insert comprising a cemented carbide substrate with a binder phase enriched surface zone and a coating, said substrate consisting of a binder phase of Co and/or Ni, WC and a cubic carbonitride phase, said binder phase enriched surface zone being essentially free of said cubic carbonitride phase and with an essentially constant thickness around the insert characterised in forming a powder mixture containing WC, 6-14 atom-%, preferably 8-11 atom-%, binder phase and 3-8 atom-%, preferably 4-6 atom-%, of Ti and at least one of Ta and Nb such that the Ti/ (Ta+Nb) atomic ratio is >2, preferably >3 , Ta and/or Nb being added as carbide and Ti as carbide, nitride and/or carbonitride in such proportions that the nitrogen content of the carbonitride phase expressed as x in the formula, (Ti , b, Ta) (Nx, Cι_x) , is >0.2, preferably 0.3-0.4 adding to said powder mixture pressing agent and possibly carbon such that the carbon content is 0-0.15 weight-% above the stoichiometric content milling and drying the mixture to obtain a powder material compacting and sintering the powder material whereby between 1200°C and pore closure nitrogen gas may be supplied to the furnace at 0-500 mbar, preferably 10-40 mbar, after which sintering is performed at a temperature of 1380-1520°C, preferably 1410-1450°C, in a protective atmosphere consisting essentially of nitrogen, the nitrogen pressure adjusted to impede gradient growth, with a period of sintering in an atmosphere without nitrogen, the time of this period adjusted to the gradient zone desired, followed by cooling according to standard practice applying conventional post sintering treatments including edgerounding and forming a hard, wear resistant coating of single or multiple layers of at least one carbide, nitride, carbonitride, oxide or boride of at least one metal of the groups IVb, VB and VIB of the periodic table and/or aluminium oxide by known CVD- , PVD- or MT-CVD-technique .
2. Cutting insert for machining of sticky work piece materials such as stainless steel comprising a cemented carbide substrate with a binder phase enriched surface zone and a coating, said substrate consisting of a Co binder phase, WC and a cubic carbonitride phase of W and at least one of the metals Ti, Ta, Nb, Mo, V, or Cr said binder phase enriched surface zone being essentially free of said cubic phase characterised in a thickness of said binder phase enriched surface zone of 15-45 μm on a flat surface of said insert and of 5-30 μm in the cutting edge.
3. Cutting insert according to claim 2 characterised in said substrate consisting of 6-14 atom-% binder phase, 3-8 atom-%, preferably 4-6 atom-% of Ti and at least one of Ta and Nb such that the Ti/ (Ta+Nb) atomic ratio is >2 and that the nitrogen content of the carbonitride phase expressed as x in the formula, (Ti ,Nb, Ta) (Nx, C1--x) , is >0.2.
4. Cutting insert according to claim 3 characterised in said Ti/ (Ta+Nb) atomic ratio >3.
5. Cutting insert according to claims 3 or 4 characterised in 0.3<x<0.4.
6. Cutting insert according to any of claims 2, 3, 4 or 5 characterised in said coating consisting of at least one of TiC, TiCN or TiN with a total coating thickness of 3-10 μm.
PCT/SE1997/001690 1996-10-11 1997-10-09 Method of making cemented carbide with binder phase enriched surface zone WO1998016665A1 (en)

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US09/242,683 US6299992B1 (en) 1996-10-11 1997-10-09 Method of making cemented carbide with binder phase enriched surface zone
AT97945149T ATE231930T1 (en) 1996-10-11 1997-10-09 METHOD FOR PRODUCING SINTERED CARBIDE WITH A BINDER PHASE-ENRICHED SURFACE ZONE
DE69718805T DE69718805T2 (en) 1996-10-11 1997-10-09 METHOD FOR PRODUCING SINTER CARBIDE WITH BIN PHASE ENRICHED SURFACE ZONE
EP97945149A EP0931171B1 (en) 1996-10-11 1997-10-09 Method of making cemented carbide with binder phase enriched surface zone
JP51825998A JP3934160B2 (en) 1996-10-11 1997-10-09 Method for producing cemented carbide with surface area enriched in binder phase

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SE9603758A SE517474C2 (en) 1996-10-11 1996-10-11 Way to manufacture cemented carbide with binder phase enriched surface zone
SE9603758-5 1996-10-11

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WO1998016665A1 true WO1998016665A1 (en) 1998-04-23

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EP (1) EP0931171B1 (en)
JP (1) JP3934160B2 (en)
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WO2002077312A2 (en) * 2001-03-27 2002-10-03 Widia Gmbh Method for increasing compression stress or reducing internal tension stress of a layer
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US6998173B2 (en) 2000-03-24 2006-02-14 Kennametal Inc. Cemented carbide tool and method of making
US8101291B2 (en) 2006-12-27 2012-01-24 Sandvik Intellectual Property Ab Coated cemented carbide insert particularly useful for heavy duty operations
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JP2002520484A (en) * 1998-07-09 2002-07-09 サンドビック アクティエボラーグ（プブル） Cemented carbide insert with bonded phase enriched surface zone
US6699526B2 (en) 1999-02-05 2004-03-02 Sandvik Ab Method of making cemented carbide insert
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US8101291B2 (en) 2006-12-27 2012-01-24 Sandvik Intellectual Property Ab Coated cemented carbide insert particularly useful for heavy duty operations
US11858049B2 (en) 2022-01-19 2024-01-02 Sumitomo Electric Industries, Ltd. Cemented carbide and tool containing the same

Also Published As

Publication number Publication date
SE517474C2 (en) 2002-06-11
JP3934160B2 (en) 2007-06-20
ATE231930T1 (en) 2003-02-15
EP0931171B1 (en) 2003-01-29
SE9603758L (en) 1998-04-12
US6299992B1 (en) 2001-10-09
JP2001502249A (en) 2001-02-20
EP0931171A1 (en) 1999-07-28
DE69718805D1 (en) 2003-03-06
DE69718805T2 (en) 2003-08-07
SE9603758D0 (en) 1996-10-11

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