EP0687744B1 - Alliage dur fritté contenant de l'azote - Google Patents

Alliage dur fritté contenant de l'azote Download PDF

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Publication number
EP0687744B1
EP0687744B1 EP95107670A EP95107670A EP0687744B1 EP 0687744 B1 EP0687744 B1 EP 0687744B1 EP 95107670 A EP95107670 A EP 95107670A EP 95107670 A EP95107670 A EP 95107670A EP 0687744 B1 EP0687744 B1 EP 0687744B1
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Prior art keywords
percent
weight
nitrogen
nitride
carbide
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EP95107670A
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German (de)
English (en)
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EP0687744A2 (fr
EP0687744A3 (fr
Inventor
Keiichi C/O Itami Works Of Sumitomo Elec. Tsuda
Kazutaka C/O Itami Works Of Sumitomo Elec. Isobe
Akihiko C/O Itami Works Of Sumitomo Ikegaya
Nobuyuki C/O Itami Works Of Sumitomo Kitagawa
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Sumitomo Electric Industries Ltd
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Sumitomo Electric Industries Ltd
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Priority claimed from JP10558494A external-priority patent/JP3648758B2/ja
Priority claimed from JP04929095A external-priority patent/JP3803694B2/ja
Application filed by Sumitomo Electric Industries Ltd filed Critical Sumitomo Electric Industries Ltd
Priority to EP97115279A priority Critical patent/EP0822265B1/fr
Publication of EP0687744A2 publication Critical patent/EP0687744A2/fr
Publication of EP0687744A3 publication Critical patent/EP0687744A3/fr
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Publication of EP0687744B1 publication Critical patent/EP0687744B1/fr
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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
    • 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
    • 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
    • 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
    • B22F3/1017—Multiple heating or additional steps
    • B22F3/1028—Controlled cooling
    • 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
    • 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
    • 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
    • B22F2201/00—Treatment under specific atmosphere
    • B22F2201/20—Use of vacuum
    • 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

Definitions

  • the present invention relates to a nitrogen-containing sintered hard alloy, and more particularly, it relates to a nitrogen-containing sintered hard alloy which is improved in thermal shock resistance, wear resistance and strength for serving as a material for a cutting tool and enabling application to wet cutting.
  • a nitrogen-containing sintered hard alloy having a hard phase of a carbo-nitride mainly composed of Ti, which is bonded by a metal containing Ni and Co, has already been put into practice as a cutting tool.
  • This nitrogen-containing sintered hard alloy is widely applied to a cutting tool similarly to the so-called cemented carbide which is mainly composed of WC, since the hard phase is extremely fined as compared with a conventional sintered hard alloy which is free from nitrogen to remarkably improve high-temperature creep resistance as the result.
  • Japanese Patent Laying-Open No. 2-15139 (1990) proposes means of improving surface roughness of a material containing at least 50 percent by weight of Ti in terms of a carbide or the like and less than 40 percent by weight of an element belonging to the group 6A (the group VIB in the CAS version) in terms of a carbide and having an atomic ratio N/(C + N) of 0.4 to 0.6 with a high nitrogen content by controlling the sintering atmosphere, for forming a modified part having high toughness and hardness in a surface layer part.
  • 5-9646 (1993) discloses a cermet which is prepared by sintering a material, which is mainly composed of Ti, containing less than 40 percent by weight of W, Mo and Cr in total in terms of a carbide, and thereafter controlling a cooling step for providing a surface part with a region having a smaller amount of binder phase as compared with the interior, to leave compressive stress on the surface.
  • each of the cermets disclosed in the aforementioned gazettes is insufficient in chipping resistance as compared with the coated cemented carbide, although wear resistance and toughness are improved. Further, the cermet is so inferior in thermal shock resistance that sudden chipping is easily caused by occurrence of thermal cracking or crack extension resulting from both thermal and mechanical shocks in particular, and sufficient reliability cannot be attained. Although the manufacturing cost for such prior art is reduced due to omission of a coating step, the performance cannot be sufficiently improved. This suggests that improvement in strength against chipping is naturally limited in the category of the so-called cermet which is prepared on the premise that the same contains Ti in excess of a certain degree of amount.
  • the inventors have made deep study on analysis of cutting phenomenons such as temperature distributions in various cutting operations and arrangements of material components in tools, to obtain the following recognition:
  • a cutting portion is partially exposed to high-temperature environment in a surface part of an insert which is in contact with a workpiece, a part of a rake face which is fretted by chips, and the like.
  • the thermal conductivity of the former is about half that of the latter as hereinabove described, and hence heat which is generated on the surface of the cermet is so hardly diffused into the interior that the temperature is abruptly reduced in the interior although the surface is at a high temperature.
  • the cermet is extremely easily chipped.
  • the cermet is rapidly quenched with water-soluble cutting oil from a high temperature state or cooled with cutting in lost motion, further, only an extremely small part of its surface is quenched.
  • the thermal expansion coefficient of the former is about 1.3 times that of the latter as hereinabove described, and hence tensile stress is caused on a surface layer part to extremely easily cause thermal cracking.
  • the cermet is inferior in thermal shock resistance to the cemented carbide.
  • the fracture toughness of the former is reduced by about 30 to 50 % as compared with the latter, and hence crack extension resistance is also reduced in the interior of the alloy.
  • An object of the present invention is to provide a nitrogen-containing sintered hard alloy which can be employed as a cutting tool in high reliability with no surface coating also in a working region under conditions bringing a strong thermal shock with no requirement for the high-priced coated cemented carbide which has been employed in general.
  • the nitrogen-containing sintered hard alloy according to the present invention is provided in its interior with a larger amount of WC as compared with the conventional nitrogen-containing sintered hard alloy in structure, to be improved in resistance against crack extension.
  • WC particles toward the alloy surface appear in the conventional nitrogen-containing sintered hard alloy to provide a tool material called a P-type material, while this tool material is inferior in smoothness of the machined surface. Therefore, this material is also remarkably inferior in abrasive wear resistance to the so-called cermet or coated cemented carbide.
  • the nitrogen-containing sintered hard alloy includes:
  • the content of the hard phase is set in the range of at least 75 percent by weight and not more than 95 percent by weight. This is because wear resistance and plastic deformation resistance are remarkably reduced if the content of the hard phase is less than 75 percent by weight while strength and toughness are insufficient if the content exceeds 95 percent by weight.
  • the Ti content is set in the range of at least 5 percent by weight and not more than 60 percent by weight in terms of a carbide or the like since wear resistance cannot reach a desired level if the Ti content is less than 5 percent by weight while toughness is deteriorated if the Ti content exceeds 60 percent by weight.
  • the Ti content is preferably at least 5 percent by weight and not more than 50 percent by weight, and particularly preferably at least 20 percent by weight and not more than 50 percent by weight.
  • the content of the metal belonging to the group 6A of the periodic table is set in the range of at least 30 percent by weight and not more than 70 percent by weight in terms of a carbide since desired toughness cannot be attained if the content is less than 30 percent by weight while a large amount of WC particles remain in the surface to disadvantageously result in insufficient wear resistance if the content exceeds 70 percent by weight.
  • the content of the metal belonging to the group 6A of the periodic table is preferably at least 40 percent by weight and not more than 70 percent by weight, and particularly preferably at least 40 percent by weight and not more than 60 percent by weight in terms of the carbide.
  • the atomic ratio of nitrogen/(carbon + nitrogen) in the hard phase is set in the range of at least 0.2 and less than 0.5, since both toughness and wear resistance cannot reach desired levels if the atomic ratio is less than 0.2 while the degree of sintering is reduced and toughness is deteriorated if the atomic ratio exceeds 0.5.
  • This atomic ratio is preferably at least 0.2 and less than 0.4.
  • the thickness of the layer hardly provided with the hard phase containing WC is set in the range of at least 3 ⁇ m and not more than 30 ⁇ m in the portion immediately under the soft layer consisting of the binder phase metal and WC located on the outermost surface since desired abrasive wear resistance and crater wear resistance cannot be attained if the thickness is less than 3 ⁇ m while no effect of facilitating crack extension resistance is attained and toughness is reduced as the result if the thickness exceeds 30 ⁇ m.
  • the abundance of the hard phase containing WC is gradually increased toward the interior from the layer hardly provided with the hard phase containing WC up to a maximum depth of 1 mm from the outermost surface in the aforementioned composition.
  • the abundance of the hard phase containing WC is gradually increased toward the interior from the layer provided with not more than 1 percent by volume of the hard phase containing WC up to the maximum depth of 1 mm from the outermost surface, whereby abrupt change of the WC content distribution is prevented in the boundary between the regions provided and not provided with WC, so that occurrence of residual stress is relieved in this boundary.
  • the nitrogen-containing sintered hard alloy includes:
  • the nitrogen-containing sintered hard alloy contains a metal belonging to the group 4A of the periodic table excluding Ti and/or the group 5A in addition to the metal belonging to the group 6A of the periodic table excluding W, at least 2 percent by weight and not more than 15 percent by weight of Ta and Nb in total in terms of a carbide, a nitride or a carbo-nitride, and not more than 5 percent by weight of V, Zr and Hf in total in terms of a carbide, a nitride or a carbo-nitride, a functional effect which is similar to that of the composition according to the first aspect can be attained.
  • Crater wear resistance is not improved if the total content of Ta and Nb is less than 2 percent by weight in terms of a carbide or the like, while chipping resistance is reduced if the content exceeds 15 percent by weight.
  • the alloy preferably contains V, Zr and Hf to be improved in strength and hardness under a high temperature, while the degree of sintering is reduced and chipping resistance is also reduced as the result if the total content of V, Zr and Hf exceeds 5 percent by weight in terms of the carbide etc.
  • the abundance of the hard phase containing WC is gradually increased toward the interior from the layer hardly provided with the hard phase containing WC up to a maximum depth of 1 mm from the outermost surface in the aforementioned composition.
  • the sample 1 had a Ti content of 34 percent by weight in terms of TiCN, a W content of 45 percent by weight in terms of WC, and a Ta and Nb content of 6 percent by weight in terms of TaC + Nb.
  • the atomic ratio N/(C + N) was 0.3. Only no WC particles were present in a region of 10 ⁇ m in thickness located immediately under a soft layer.
  • samples 2 to 4 were prepared by conventional methods respectively.
  • the sample 2 was prepared by sintering a stamped compact which was identical to that of the sample 1 under a nitrogen partial pressure of 5 Torr at 1400°C.
  • the sample 3 was prepared by cooling a sintered body which was identical to that of the sample 2 under a CO partial pressure of 200 Torr after sintering.
  • the sample 4 was prepared by cooling a sintered body which was identical to that of the sample 2 under a nitrogen partial pressure of 180 Torr after sintering.
  • the abundances of hard phases containing WC located immediately under soft layers were 10 percent by volume, 15 percent by volume and 5 percent by volume respectively.
  • TaC, NbC, ZrC and VC of 1 to 3 ⁇ m in mean particle size were blended in weight ratios shown in Table 1 to form sintered alloys through steps similar to those for the sample 1, thereby preparing samples 5 to 10 having reduced contents shown in Table 1.
  • Ni, Co, ZrC and VC were omitted from Table 1 since the reduced contents thereof were substantially identical to the blending compositions.
  • Table 2 shows atomic ratios N/(C + N), thicknesses of layers provided with not more than 1 percent by volume of hard phases containing WC located immediately under soft layers in alloy surface parts.
  • Sample No. Blending Composition (weight %) Reduced Content (weight %) (TiTaNbW)CN WC TaC NbC ZrC VC Ni Co TiCN WC TaC + NbC 1 2* 3* 45 40 - - - - 7 8 34 45 6 4* 5 30 40 4 4 2 - 5 15 22 45 11 6 60 20 3 - - 2 10 5 44 30 9 7* 80 2 2 - 2 - 7 7 58 15 11 8* 89 - - - - - 5 6 65 14 10 9* 50 40 - 2 - - 4 4 37 48 7 10* 45 25 2 - 2 - 13 13 3 32 7 Note) Asterisked numerals indicate comparative samples, and underlined numeric values are out of the inventive ranges.
  • Sample No. N/C+N Average Ratio Thickness of Region Provided with Not More Than 1 vol.% of Hard Phase Containing WC ( ⁇ m) 1 0.30 10 2* 0.30 0 3* 0.30 0 4* 0.30 0 5 0.27 5 6 0.41 15 7* 0.44 200 8* 0.44 Overall Alloy Region 9* 0.34 10 10* 0.36 60 Note) Asterisked numerals indicate comparative samples, and underlined numeric values are out of the inventive ranges.
  • the samples 1, 5 and 6 having compositions etc. satisfying the conditions according to the first or second aspect of the present invention are superior in wear resistance, toughness and thermal shock resistance to the samples 2 to 4 and 7 to 10 having compositions etc. which are out of the inventive conditions.
  • Raw powder materials shown in Table 5 were blended and mixed/crushed to attain respective reduced contents, thereby forming samples 11 to 23.
  • Each TiCN powder material had a mean particle size of 2 ⁇ m and an atomic ratio C/N of 5/5, while the remaining powder materials were 1 to 3 ⁇ m in mean particle size.
  • Blending compositions of the respective samples were omitted from Table 5 since the same were substantially identical to the reduced contents.
  • Sample No. Reduced Content (wt.%) TiCN TiC TiN WC Mo 2 C TaC NbC ZrC HfC Ni Co 11 45 - - 35 5 - - - - 5 10 12 40 - - 30 5 4 2 2 2 5 10 13 - 15 21 44 - - - - - 10 10 14 - 10 16 44 - - 7 3 - 10 10 15 - 23 12 50 - - - - - 8 7 16 - 10 25 50 - - - - - 8 7 17 - 26 17 37 3 3 - - - 6 8 18* 55 - - 25 - 4 - - - 8 8 19* 18 - - 72 - - - - - 5 5 20* - 25 10 50 - - - - - 8 7 21* - 7 28 50 - - - -
  • samples 11 to 23 were heated in a vacuum of 10 -2 Torr at 3°C/min., degassed at 1200°C for 15 minutes, thereafter sintered under a nitrogen gas partial pressure of 15 to 40 Torr at 1450°C for 1 hour, thereafter control-cooled in a vacuum to 1200°C at 3°C/min., and thereafter nitrogen-quenched.
  • samples 11A to llC and 12A to 12C were formed after sintering under the same conditions, under various cooling conditions.
  • the samples 11A and 12A were cooled under a CO partial pressure of 150 Torr after sintering under the same conditions as the samples 11 and 12 respectively, the samples 11B and 12B were cooled under a nitrogen partial pressure of 200 Torr, and the samples 11C and 12C were heated to 1530°C, thereafter sintered for 1.5 hours, and thereafter control-cooled.
  • Table 6 shows atomic ratios N/(C + N), thicknesses of regions provided with not more than 1 percent by volume of hard phases containing WC located immediately under soft layers in alloy surface parts.
  • Sample No. N/C+N Atomic Ratio
  • the samples 11, 12 and 13 to 17 having compositions etc. satisfying the conditions according to the first or second aspect of the present invention are superior in wear resistance, toughness and thermal shock resistance to the samples 11A to 11C, 12A to 12C and 18 to 23 having compositions etc. which are out of the inventive conditions.

Claims (4)

  1. Alliage dur fritté contenant de l'azote comprenant :
    au moins 75 pourcent en poids et pas plus de 95 pourcent en poids d'une phase dure contenant (Ti. WxMy)(CuN1-u) (M représente au moins un métal appartenant au groupe 6A de la classification périodique des éléments excluant W, 0 ≤ x ≤ 1, 0 ≤ y ≤ 0,9 et 0 ≤ u ≤ 0,9) et WC, et au moins 5 pourcent en poids et pas plus de 25 pourcent en poids d'une phase de liant contenant Ni, Co et des impuretés inévitables, et contenant :
    au moins 5 pourcent en poids et pas plus de 60 pourcent en poids de Ti en termes d'un carbure, d'un nitrure ou d'un carbonitrure, et au moins 30 pourcent en poids et pas plus de 70 pourcent en poids d'un métal appartenant au groupe 6A de la classification périodique des éléments en terme d'un carbure, le rapport atomique de l'azote/(carbone + azote) dans ladite phase dure étant d'au moins 0,2 et inférieur à 0,5, ledit alliage dur fritté contenant de l'azote étant fourni avec une couche molle contenant un métal de phase de liant et WC dans sa surface extérieure, avec une couche d'au plus 1% en volume de ladite phase dure dans une partie se trouvant immédiatement sous ladite couche molle dans une épaisseur d'au moins 3 µm et inférieure à 30 µm.
  2. Alliage dur fritté contenant de l'azote selon la revendication 1, dans lequel l'abondance de ladite phase dure augmente progressivement vers l'intérieur à partir de ladite couche étant fournie de manière dure avec ladite phase dure jusqu'à une profondeur maximale de 1 mm à partir de ladite surface extérieure.
  3. Alliage dur fritté contenant de l'azote comprenant :
    au moins 75 pourcent en poids et pas plus de 95 pourcent en poids d'une phase dure contenant (Ti.WxMy) (CuN1-u) (M représente au moins un métal appartenant aux groupes 4A, 5A et 6A de la classification périodique des éléments excluant Ti et W, 0< x <1, 0 ≤ y ≤ 0,9 et 0 ≤ u ≤ 0,9) et WC, et au moins 5 pourcent en poids et pas plus de 25 pourcent en poids d'une phase de liant contenant Ni, Co et des impuretés inévitables, et contenant :
    au moins 5 pourcent en poids et pas plus de 60 pourcent en poids de Ti en termes d'un carbure, d'un nitrure ou d'un carbonitrure, au moins 30 pourcent en poids et pas plus de 70 pourcent en poids d'un métal appartenant au groupe 6A de la classification périodique des éléments en terme d'un carbure, au moins 2 pourcent en poids et pas plus de 15 pourcent en poids de Ta et de Nb au total en termes d'un carbure, d'un nitrure ou d'un carbonitrure, et pas plus de 5 pourcent en poids de V, Zr et Hf au total en termes d'un carbure, d'un nitrure ou d'un carbonitrure, le rapport atomique de l'azote/(carbone + azote) dans ladite phase dure étant d'au moins 0,2 et inférieur à 0,5, ledit alliage dur fritté contenant de l'azote étant fourni avec une couche molle contenant un métal de phase de liant et WC dans sa surface extérieure, avec une couche d'au plus 1% en volume de ladite phase dure dans une partie se trouvant immédiatement sous ladite couche molle dans une épaisseur d'au moins 3 µm et inférieure à 30 µm.
  4. Alliage dur fritté contenant de l'azote selon la revendication 3, dans lequel l'abondance de ladite phase dure augmente progressivement vers l'intérieur à partir de ladite couche étant fournie de manière dure avec ladite phase dure jusqu'à une profondeur maximale de 1 mm à partir de ladite surface extérieure.
EP95107670A 1994-05-19 1995-05-18 Alliage dur fritté contenant de l'azote Expired - Lifetime EP0687744B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP97115279A EP0822265B1 (fr) 1994-05-19 1995-05-18 Alliage dur fritté contenant de l'azote

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP10558494A JP3648758B2 (ja) 1994-05-19 1994-05-19 窒素含有焼結硬質合金
JP10558494 1994-05-19
JP105584/94 1994-05-19
JP04929095A JP3803694B2 (ja) 1995-02-15 1995-02-15 窒素含有焼結硬質合金
JP49290/95 1995-02-15
JP4929095 1995-02-15

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EP0687744A2 EP0687744A2 (fr) 1995-12-20
EP0687744A3 EP0687744A3 (fr) 1996-08-21
EP0687744B1 true EP0687744B1 (fr) 1999-11-03

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EP95107670A Expired - Lifetime EP0687744B1 (fr) 1994-05-19 1995-05-18 Alliage dur fritté contenant de l'azote

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KR (1) KR0180522B1 (fr)
DE (2) DE69523342T2 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7449043B2 (en) 2003-12-15 2008-11-11 Sandvik Intellectual Property Aktiebolag Cemented carbide tool and method of making the same

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19845376C5 (de) * 1998-07-08 2010-05-20 Widia Gmbh Hartmetall- oder Cermet-Körper
EP1095168B1 (fr) 1998-07-08 2002-07-24 Widia GmbH Corps en metal dur ou en cermet, et son procede de production
US6110603A (en) * 1998-07-08 2000-08-29 Widia Gmbh Hard-metal or cermet body, especially for use as a cutting insert
DE19922057B4 (de) * 1999-05-14 2008-11-27 Widia Gmbh Hartmetall- oder Cermet-Körper und Verfahren zu seiner Herstellung
CA2547926C (fr) 2003-12-15 2013-08-06 Sandvik Intellectual Property Ab Outils en carbure cemente destines a des applications minieres et a des applications de construction et leur procede de fabrication
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Publication number Publication date
EP0687744A2 (fr) 1995-12-20
KR950032671A (ko) 1995-12-22
DE69513086D1 (de) 1999-12-09
DE69523342T2 (de) 2002-06-27
KR0180522B1 (ko) 1999-02-18
EP0822265A3 (fr) 1998-04-15
DE69523342D1 (de) 2001-11-22
EP0822265A2 (fr) 1998-02-04
EP0822265B1 (fr) 2001-10-17
DE69513086T2 (de) 2000-07-13
EP0687744A3 (fr) 1996-08-21

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