JPH0711069B2 - High-strength coated cemented carbide member - Google Patents
High-strength coated cemented carbide memberInfo
- Publication number
- JPH0711069B2 JPH0711069B2 JP63289194A JP28919488A JPH0711069B2 JP H0711069 B2 JPH0711069 B2 JP H0711069B2 JP 63289194 A JP63289194 A JP 63289194A JP 28919488 A JP28919488 A JP 28919488A JP H0711069 B2 JPH0711069 B2 JP H0711069B2
- Authority
- JP
- Japan
- Prior art keywords
- cemented carbide
- carbide
- shape
- plate
- coated cemented
- 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.)
- Expired - Fee Related
Links
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 36
- 239000006104 solid solution Substances 0.000 claims description 32
- 239000011248 coating agent Substances 0.000 claims description 27
- 238000000576 coating method Methods 0.000 claims description 27
- 229910052721 tungsten Inorganic materials 0.000 claims description 14
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 239000011230 binding agent Substances 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 239000002131 composite material Substances 0.000 claims description 5
- 229910052735 hafnium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052715 tantalum Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 claims 2
- 238000005520 cutting process Methods 0.000 description 13
- 239000000843 powder Substances 0.000 description 13
- 239000010936 titanium Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 230000000694 effects Effects 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 230000006866 deterioration Effects 0.000 description 5
- 239000000956 alloy Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 238000005229 chemical vapour deposition Methods 0.000 description 4
- 239000010410 layer Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005240 physical vapour deposition Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 229910052582 BN Inorganic materials 0.000 description 1
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 229910011208 Ti—N Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000007733 ion plating Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000001902 propagating effect Effects 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- -1 tungsten carbides Chemical class 0.000 description 1
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は、強度及び靱性にすぐれており、切削工具用材
料として用いた場合に耐摩耗性及び耐欠損性にすぐれた
効果を発揮するもので、特に切削工具用材料又は耐摩耗
工具用材料として適する高強度被覆超硬合金部材に関す
るものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial field of application) The present invention has excellent strength and toughness, and exhibits excellent effects of wear resistance and chipping resistance when used as a material for cutting tools. In particular, it relates to a high-strength coated cemented carbide member suitable as a material for cutting tools or a material for wear-resistant tools.
（従来の技術） 従来、超硬合金の基材表面に炭化チタン，窒化チタン、
炭窒化チタン、酸化アルミニウムなどのセラミックスか
らなる被覆膜を形成してなる被覆超硬合金が各種の工具
部材として実用化されている。この被覆超硬合金の被覆
膜は、超硬合金の基材に比べて硬質ではあるが、脆弱で
あることから、被覆膜にはクラックが発生しやすく、こ
のクラックが基材に伝播することになり、その結果被覆
超硬合金の強度及び耐欠損性を劣化させるとおう問題が
ある。この問題を解決するものとして、被覆超硬合金に
おける基材についての提案が多数行われ、その代表的な
ものに、特開昭53-131909号公報及び特開昭55-154561号
公報がある。(Prior Art) Conventionally, titanium carbide, titanium nitride,
Coated cemented carbide formed by forming a coating film made of ceramics such as titanium carbonitride and aluminum oxide has been put into practical use as various tool members. The coating film of the coated cemented carbide is harder than the substrate of the cemented carbide, but is fragile, so that cracks easily occur in the coating film and the cracks propagate to the substrate. As a result, there is a problem that the strength and fracture resistance of the coated cemented carbide are deteriorated. As a solution to this problem, many proposals have been made for a base material in a coated cemented carbide, and typical ones thereof are JP-A-53-131909 and JP-A-55-154561.
（発明が解決しようとする問題点） 特開昭53-131909号公報は、超硬合金と被覆膜との間に
超硬合金よりも靱性に富むと共に軟質で、しかも被覆膜
側から超硬合金側に向って硬さが連続的に増加する硬さ
勾配をもった中間層を介在させてなる被覆超硬合金工具
が開示されている。この特開昭53-131909号公報の被覆
超硬合金工具は、中間層が被覆膜に発生したクラックの
超硬合金内部への伝播を阻止することにより、強度及び
耐欠損性を向上させたものであるけれども、被覆膜が摩
耗により消滅した後は、耐欠損性，耐溶着性の劣化が生
じて短寿命になるという問題がある。(Problems to be Solved by the Invention) Japanese Patent Application Laid-Open No. 53-131909 discloses that between the cemented carbide and the coating film, the toughness is richer and softer than that of the cemented carbide, and the coating film side has Disclosed is a coated cemented carbide tool including an intermediate layer having a hardness gradient in which the hardness continuously increases toward the hard alloy side. The coated cemented carbide tool disclosed in JP-A-53-131909 has improved strength and fracture resistance by preventing the crack generated in the coating film from propagating inside the cemented carbide in the intermediate layer. However, after the coating film has disappeared due to wear, there is a problem that the chipping resistance and the welding resistance are deteriorated and the life is shortened.
特開昭55-154561号公報は、WCとBl型固溶体とを硬質層
とし、これをFe,Co,Ni,Cr,Mo,Wの１種もしくはそれ以上
の金属で結合した超硬合金部品の表面から0.1〜10μｍ
の深さにおけるBl型固溶体の量が、該超硬合金部品の上
記以外の内部における量に比して大である超硬合金の表
面にAl2O3及び／又はZr2Oを被覆した被覆超硬合金部品
が開示されている。この特開昭55-154561号公報の被覆
超硬合金部品は、超硬合金中に含有しているCoがAl2O3
及び／又はZr2Oの被覆膜の特性を劣化するのをBl型固溶
体の量を大にした表面層を有する超硬合金により防止
し、耐摩耗性をより一段と向上させたものであるけれど
も、被覆膜中に発生したクラックが超硬合金の内部に伝
播しやすいために強度及び耐欠損性の劣下が生じるとい
う問題がある。Japanese Patent Laid-Open No. 55-154561 discloses a cemented carbide part in which WC and a Bl-type solid solution are used as a hard layer and these are bonded with one or more metals of Fe, Co, Ni, Cr, Mo and W. 0.1-10 μm from the surface
The amount of the Bl-type solid solution at the depth of is larger than the amount in the interior of the cemented carbide component other than the above, the coating of Al 2 O 3 and / or Zr 2 O on the surface of the cemented carbide. Cemented carbide parts are disclosed. In the coated cemented carbide part disclosed in JP-A-55-154561, Co contained in the cemented carbide is Al 2 O 3
And / or the deterioration of the characteristics of the Zr 2 O coating film is prevented by a cemented carbide having a surface layer with a large amount of Bl type solid solution, and the wear resistance is further improved. However, there is a problem that cracks generated in the coating film easily propagate inside the cemented carbide, resulting in deterioration of strength and fracture resistance.
本発明は、上述のような問題点を解決したもので、具体
的には、板状体に形成した炭化タングステン、もしくは
板状体の炭化タングステンとBl型固溶体とを含有してな
る超硬合金の表面に被覆膜を形成することにより、強
度，耐欠損性、耐摩耗性，耐塑性変形性及び耐熱性にす
ぐれるようにした高強度被覆超硬合金部材の提供を目的
とするものである。The present invention has solved the above-mentioned problems, specifically, tungsten carbide formed in a plate-like body, or a cemented carbide containing a plate-like tungsten carbide and a Bl-type solid solution. It is intended to provide a high strength coated cemented carbide member having excellent strength, fracture resistance, wear resistance, plastic deformation resistance and heat resistance by forming a coating film on the surface of is there.
（問題点を解決するための手段） 本発明者らは、超硬合金の表面に各種のセラミックスで
なる被覆膜を形成してなる被覆超硬合金の強度及び耐欠
損性が超硬合金自体の強度及び耐欠損性に比べて極端に
劣下するのを防止することについて検討していた所、WC
の単結晶におけるそれぞれの結晶面のビッカース硬さは
（0001）面が2100±40kgf/mm2，（１00）面が1080±5
0kgf/mm2，（１01）面が1060±20kgf/mm2で、この
内、硬さの高い（0001）面の成長してなる板状体の炭化
タングステンの含有してなる超硬合金の表面に被覆膜を
形成した被覆超硬合金の場合は、強度及び耐欠損性の劣
化が著しく少ないこと、又板状体の炭化タングステンと
Bl型固溶体の両方の含有してなる超硬合金の表面に被覆
膜を形成した被覆超硬合金の場合は、耐摩耗性にすぐれ
ると共に、強度及び耐欠損性の劣下も少ないという知見
を得たものである。この知見に基づいて、本発明を完成
するに至ったものである。(Means for Solving Problems) The inventors of the present invention have found that the strength and the fracture resistance of a coated cemented carbide obtained by forming a coating film made of various ceramics on the surface of the cemented carbide are the cemented carbide itself. WC was examined to prevent the deterioration of the strength and fracture resistance of the
The Vickers hardness of each crystal plane in the single crystal of is 1100 ± 40kgf / mm 2 for (0001) plane and 1080 ± 5 for (100) plane.
0 kgf / mm 2, at (101) plane is 1060 ± 20kgf / mm 2, these, high hardness (0001) plane growth comprising tungsten carbide of the plate formed by the surface of the cemented carbide In the case of a coated cemented carbide with a coating film formed on it, the deterioration of strength and fracture resistance is extremely small.
In the case of a coated cemented carbide with a coating film formed on the surface of a cemented carbide containing both Bl-type solid solution, it was found that it has excellent wear resistance and less deterioration in strength and fracture resistance. Is what I got. The present invention has been completed based on this finding.
すなわち、本発明の高強度被覆超硬合金部材は、ＷとTi
とを含有した複合炭化物，複合炭窒化物，複合炭酸化
物，複合炭窒酸化物、及びＷとTiとZr,Hf,V,Nb,Ta,Cr,M
oの中の少なくとも１種とを含有した複合炭化物，複合
炭窒化物，複合炭酸化物，複合炭窒酸化物から選ばれた
少なくとも１種のBl型固溶体と、炭化タングステンとで
異なる硬質相80〜98重量％と、残りCo及び／又はNiを主
成分とする結合相と不可避不純物とからなる超硬合金の
表面に被覆膜を形成してなる被覆超硬合金であって、該
超硬合金は三角形状、又は最大寸法が２〜20μｍで、こ
の最大寸法が最小寸法の少なくとも２倍でなる針状，棒
状，四角形状を主とする多角形状の中の少なくとも１種
として観察される板状体の炭化タングステンが該超硬合
金全体の少なくとも５体積％混在していることを特徴と
するものである。That is, the high strength coated cemented carbide member of the present invention is
Composite carbides, complex carbonitrides, complex carbonitrides, complex carbonitrides, and W, Ti and Zr, Hf, V, Nb, Ta, Cr, M containing
At least one Bl-type solid solution selected from complex carbides, complex carbonitrides, complex carbonates, and complex carbonitrides containing at least one of o and a hard phase different from tungsten carbide 80 ~ A coated cemented carbide obtained by forming a coating film on the surface of a cemented carbide consisting of 98 wt% and the binder phase containing Co and / or Ni as the main components and unavoidable impurities. Is a triangular shape, or a plate shape with a maximum dimension of 2 to 20 μm, which is observed as at least one of a needle shape, a rod shape, and a polygonal shape mainly including a quadrangular shape whose maximum dimension is at least twice the minimum dimension. At least 5% by volume of the entire body of the cemented carbide is mixed with the body tungsten carbide.
本発明の高強度被覆超硬合金部材における超硬合金中の
硬質相は、板状体の炭化タングステンとBl型固溶体から
なる場合、又は板状体の炭化タングステンと従来の塊状
体で、ほぼ等寸法として観察される炭化タングステンと
Bl型固溶体とからなる場合がある。The hard phase in the cemented carbide in the high-strength coated cemented carbide member of the present invention is composed of a plate-shaped tungsten carbide and a Bl-type solid solution, or a plate-shaped tungsten carbide and a conventional lump, and approximately the same. Tungsten Carbide Observed as a Dimension
It may consist of Bl type solid solution.
この硬質相中に混在する板状体の炭化タングステンは、
（0001）面の成長してなる炭化タングステンであって、
具体的には超硬合金の任意の断面における炭化タングス
テンの形状が針状，棒状，四角形状を主とする多角形状
又は三角形状でなるもので、この内三角形状の炭化タン
グステンは（0001）面の成長してなる三角柱状の板状体
の炭化タングステンであることから、全て板状体の炭化
タングステンであるとみなすことができる。また、超硬
合金の任意の断面において存在する板状体の炭化タング
ステンは、三角形状の炭化タングステンの他に、針状，
棒状又は台形状のように四角形状を主とする多角形状の
形態に観察でき、これらの炭化タングステンの中で、最
大寸法が２〜20μｍ、この最大寸法が最小寸法の少なく
とも２倍でなるものである。これらの板状体の炭化タン
グステンは、超硬合金全体の５体積％未満になると破壊
靱性値，強度及び耐熱亀裂性を高める効果が弱くなる。
このために、板状体の炭化タングステンは、超硬合金全
体の少なくとも５体積％混在していることが必要で、耐
欠損性及び耐摩耗性からBl型固溶体を除いた全ての硬質
相が板状体の炭化タングステンであることが好ましいこ
とである。The plate-shaped tungsten carbide mixed in this hard phase is
(0001) plane grown tungsten carbide,
Specifically, the shape of tungsten carbide in any cross section of the cemented carbide is a polygonal shape mainly having a needle shape, a rod shape, a quadrangular shape, or a triangular shape, and the tungsten carbide having a triangular shape has a (0001) plane. Since it is a tungsten carbide having a plate shape of a triangular prism formed by growing, it can be considered that all the tungsten carbide has a plate shape. Further, the tungsten carbide of a plate-like body existing in any cross section of the cemented carbide is not only triangular tungsten carbide but also needle-shaped,
It can be observed in the form of a polygon such as a rod or a trapezoid, which is mainly quadrangular. Among these tungsten carbides, the maximum dimension is 2 to 20 μm, and this maximum dimension is at least twice the minimum dimension. is there. When the tungsten carbide of these plate-like materials is less than 5% by volume of the whole cemented carbide, the effect of enhancing the fracture toughness value, strength and heat crack resistance becomes weak.
For this reason, it is necessary for the plate-shaped tungsten carbide to be mixed in at least 5% by volume of the entire cemented carbide, and all hard phases except for the Bl-type solid solution are plate-shaped due to chipping resistance and wear resistance. It is preferable that it is a tungsten carbide in the form of a body.
この硬質相中にBl型固溶体の含有している場合には、高
温における耐摩耗性、金属などとの耐溶着性及び耐酸化
性にすぐれていることから、特に刃先が高温になるよう
な条件で用いられる切削工具用材料としてすぐれた効果
を発揮する。一方、硬質相中にBl型固溶体の含有してい
ない板状体の炭化タングステンでなる硬質相の場合、又
は板状体の炭化タングステンと従来のほぼ等寸法として
観察される炭化タングステンとでなる硬質相の場合があ
る。このBl型固溶体の含有していない硬質相の場合に
は、常温又は使用時にそれほど高温にならない、例えば
プリント基板用ドリルなどの切削工具用材料、もしくは
スリッタなどの耐摩耗工具用材料としてすぐれた効果を
発揮する。When the Bl-type solid solution is contained in this hard phase, it has excellent wear resistance at high temperatures, resistance to welding with metals, etc. and excellent oxidation resistance, so that the cutting edge is particularly high in temperature. It has excellent effects as a material for cutting tools used in. On the other hand, in the case of a hard phase made of a plate-shaped tungsten carbide that does not contain a Bl-type solid solution in the hard phase, or a hard plate made of a plate-shaped tungsten carbide and a tungsten carbide that is observed as a conventional almost equal size. It can be a phase. In the case of a hard phase that does not contain this Bl-type solid solution, it does not become so hot at room temperature or during use, for example, it is an excellent effect as a material for cutting tools such as drills for printed circuit boards, or a material for wear-resistant tools such as slitters. Exert.
さらに、この板状体の炭化タングステンが後述するよう
な実施例の方法でもって一定方向に配向されていると、
例えば炭化タングステンの（0001）面が超硬合金の或る
面に平行に配向された場合は、この面の高度及びこの面
を張力面とする抗折強度は上昇し、しかもこの面に生じ
るクラックは進展しにくゝなり、耐欠損性が向上するの
で好ましいことである。Furthermore, when the tungsten carbide of the plate-shaped body is oriented in a certain direction by the method of the embodiment described below,
For example, when the (0001) plane of tungsten carbide is oriented parallel to a certain plane of cemented carbide, the altitude of this plane and the bending strength with this plane as a tension plane are increased, and cracks generated on this plane Is preferable because it is less likely to progress and the fracture resistance is improved.
硬質相中に混在しているBl型固溶体は、具体的には、例
えば（W,Ti）C,（W,Ti）（Ｃ、Ｎ）， （W,Ti）（C,O），（W,Ti）（C,N,O）， （W,Ti,M）C,（W,Ti,M）（C,N）， （W,Ti,M）（C,O），（W,Ti,M）（C,N,O）（但し、Ｍは
Zr,Hf,Ta,Nb,V,Cr,Moの中の少なくとも１種を示す。）
で表わせる立方晶構造の化合物を挙げることができる。The Bl-type solid solution mixed in the hard phase is specifically, for example, (W, Ti) C, (W, Ti) (C, N), (W, Ti) (C, O), (W , Ti) (C, N, O), (W, Ti, M) C, (W, Ti, M) (C, N), (W, Ti, M) (C, O), (W, Ti , M) (C, N, O) (However, M is
At least one of Zr, Hf, Ta, Nb, V, Cr and Mo is shown. )
A compound having a cubic crystal structure represented by
これらの炭化タングステンとBl型固溶体とからなる硬質
相が超硬合金全体の80重量％未満になると、相対的に結
合相が20重量％を超えて多くなって耐塑性変形性及び耐
摩耗性の低下となる。このために、（0001）面の成長し
てなる板状体の炭化タングステンを超硬合金中に存在さ
せても、その効果が殆んど現われない傾向となる。逆
に、硬質相が超硬合金全体の98重量％を超えて多くなる
と、相対的に結合相が２重量％未満となって緻密な超硬
合金になり難く、その結果（0001）面の成長してなる板
状体の炭化タングステンを超硬合金中に存在させても強
度に対する著しい効果が現われない傾向となる。これら
の理由から、本発明の高強度被覆超硬合金部材中の硬質
相は、80〜98重量％と定めたものである。When the hard phase composed of these tungsten carbide and Bl type solid solution is less than 80% by weight of the whole cemented carbide, the relative amount of the binder phase exceeds 20% by weight and the plastic deformation resistance and wear resistance are relatively increased. It will decrease. For this reason, even if the tungsten carbide in the form of a plate having a (0001) plane grown therein is present in the cemented carbide, the effect tends to be hardly exhibited. On the other hand, if the hard phase exceeds 98% by weight of the total cemented carbide, the binder phase becomes relatively less than 2% by weight, and it becomes difficult to form a dense cemented carbide, resulting in the growth of the (0001) plane. Even if the plate-shaped tungsten carbide formed as described above is present in the cemented carbide, there is a tendency that no remarkable effect on the strength appears. For these reasons, the hard phase in the high-strength coated cemented carbide member of the present invention is defined as 80 to 98% by weight.
本発明の高強度被覆超硬合金部材における超硬合金中の
結合相は、Coのみからなる場合、Niのみからなる場合、
又は少なくとも50％のCo及び／又はNiと残り、例えばF
e,W,Cr,Mo,Ti,Zr,Hf,Ta,Nb,Vの中の少なくとも１種とか
らなる場合がある。The binder phase in the cemented carbide in the high-strength coated cemented carbide member of the present invention, if only Co, if only Ni,
Or remaining with at least 50% Co and / or Ni, eg F
It may consist of at least one of e, W, Cr, Mo, Ti, Zr, Hf, Ta, Nb, and V.
本発明の高強度被覆超硬合金部材における被覆膜は、従
来の超硬合金の表面に形成されている各種の被覆膜を形
成することができ、例えば周期律表4a,5a,6a族金属の炭
化物，窒化物，炭酸化物，窒酸化物，ホウ化物及びこれ
らの相互固溶体、又は酸化アルミニウム，窒化アルミニ
ウム，酸窒化アルミニウム，炭化ケイ素，窒化ケイ素，
立方晶窒化ホウ素、ダイヤモンドの中の少なくとも１種
の単層、もしくは多重層でなるものを挙げることができ
る。The coating film in the high-strength coated cemented carbide member of the present invention can form various coating films formed on the surface of conventional cemented carbide, for example, Periodic Table 4a, 5a, 6a group Metal carbides, nitrides, carbonates, oxynitrides, borides and their mutual solid solutions, or aluminum oxide, aluminum nitride, aluminum oxynitride, silicon carbide, silicon nitride,
Examples include cubic boron nitride, and a single layer or a multi-layer of at least one kind of diamond.
本発明の高強度被覆超硬合金部材は、次のような方法で
作製することができる。The high-strength coated cemented carbide member of the present invention can be manufactured by the following method.
まず、Bl型固溶体の硬質相を含有した超硬合金を作製す
る場合は、本発明者らが先に提案した、例えば特願昭63
-198700号で開示の方法でもって行い、Bl型固溶体の硬
質相を含有していない超硬合金を作製する場合は、例え
ば特開昭57-34008号公報又は特公昭47-23049号公報で開
示の方法を応用して作製することができる。このように
して作製した超硬合金の表面を必要に応じて研摩、又は
洗浄などの処理を施した後、従来から行われている物理
蒸着法（PVD法）や化学蒸着法（CVD法）でもって目的と
する被覆膜を超硬合金の表面に形成することにより本発
明の高強度被覆超硬合金部材を得ることができる。First, in the case of producing a cemented carbide containing a hard phase of a Bl type solid solution, the present inventors have previously proposed, for example, Japanese Patent Application No.
-198700, in the case of producing a cemented carbide that does not contain the hard phase of the Bl type solid solution, disclosed in, for example, JP-A-57-34008 or JP-B-47-23049. It can be manufactured by applying the above method. After polishing or cleaning the surface of the cemented carbide prepared in this way as necessary, it is possible to use the conventional physical vapor deposition method (PVD method) or chemical vapor deposition method (CVD method). Therefore, the high-strength coated cemented carbide member of the present invention can be obtained by forming an intended coating film on the surface of the cemented carbide.
（作用） 本発明の高強度被覆超硬合金部材は、超硬合金を構成し
ている板状体の炭化タングステンが摩擦摩耗時に被覆膜
に発生したクラックの超硬合金内部への伝播を阻止する
作用をし、さらに被覆膜の消滅後に超硬合金中の硬質相
粒子の脱落するのを防止する作用をし、その結果、耐摩
耗性，破壊靱性値，耐塑性変形性及び強度がすぐれてい
るものである。特に、Bl型固溶体と板状体の炭化タング
ステンとを含有した硬質相でなる超硬合金の表面に被覆
膜を形成した本発明の高強度被覆超硬合金の場合は、被
覆膜の消滅後も高温での耐摩耗性にすぐれると共に、耐
溶着性，耐熱性にもすぐれるものである。(Operation) The high-strength coated cemented carbide member of the present invention prevents the propagation of cracks generated in the coating film during the frictional wear of the tungsten carbide of the plate-shaped body forming the cemented carbide to the inside of the cemented carbide. It also acts to prevent the hard phase particles from falling out of the cemented carbide after the coating film disappears, resulting in excellent wear resistance, fracture toughness, plastic deformation resistance and strength. It is what In particular, in the case of the high-strength coated cemented carbide of the present invention in which a coating film is formed on the surface of the cemented carbide made of a hard phase containing a Bl-type solid solution and a plate-shaped tungsten carbide, the coating film disappears. It also has excellent wear resistance at high temperatures as well as excellent welding resistance and heat resistance.
（実施例） 実施例１ 重量比で、WC/TiC/TaC＝80/15/5の固溶体粉末（第１固
溶体）,WC/TiC/TaC＝45/22/33の固溶体粉末（第２固溶
体）,WC/TiC＝70/30の固溶体粉末（第３固溶体）及び平
均粒径1.0〜2.0μｍのWC,Coの各粉末を用いて、ほぼ73.
6wt％WC-13.8wt％TiC-4.6wt％TaC−8wt％Co組成になる
ように第１表の如く配合した。この配合粉末を混合及び
加圧成形後、真空炉で1400℃,1時間保持にて焼結し、次
いでTiCl4-H2-CH4の混合ガスによる従来のCVD法でもっ
て、超硬合金の表面に約２μｍのTiC被覆膜を形成して
本発明品１及び比較品１を得た。さらに、本発明品１の
内、超硬合金の焼結後、冷却時に一方向から過熱状態で
30kgf/cm2の圧力を加えて、超硬合金中の板状体WCの（0
001）面を一方向に向けるように配向させた以外は本発
明品と同様にして、本発明品２を得た。(Example) Example 1 A solid solution powder of WC / TiC / TaC = 80/15/5 (first solid solution) and a solid solution powder of WC / TiC / TaC = 45/22/33 (second solid solution) by weight. , WC / TiC = 70/30 solid solution powder (third solid solution) and WC and Co powders with an average particle size of 1.0 to 2.0 μm, approximately 73.
6 wt% WC-13.8 wt% TiC-4.6 wt% TaC-8 wt% Co were compounded as shown in Table 1. After mixing and pressure molding this compounded powder, it is sintered in a vacuum furnace at 1400 ° C. for 1 hour and then sintered by a conventional CVD method using a mixed gas of TiCl 4 —H 2 —CH 4 to produce a cemented carbide. Inventive product 1 and comparative product 1 were obtained by forming a TiC coating film of about 2 μm on the surface. Furthermore, among the products 1 of the present invention, after the cemented carbide is sintered, it is heated from one direction in an overheated state during cooling.
By applying a pressure of 30 kgf / cm 2 , the plate-shaped body WC (0
The present invention product 2 was obtained in the same manner as the present invention product, except that the (001) plane was oriented so as to face in one direction.
こうして得た本発明品1,2及び比較品１の合金組織中の
板状体WCの量、及び被覆超硬合金の抗折力値を求めて第
２表に示した。The amounts of the plate-shaped bodies WC in the alloy structures of the invention products 1 and 2 and the comparative product 1 thus obtained and the transverse rupture strength values of the coated cemented carbides were determined and shown in Table 2.
次に、本発明品1,2及び比較品１を下記の条件でもって
切削試験を行い、その結果を第２表に併記した。Next, the present invention products 1 and 2 and the comparative product 1 were subjected to a cutting test under the following conditions, and the results are also shown in Table 2.
フライス切削試験条件 被削材 SCM440（HB250） 50×150mm面の切削 チップ形状 SNP432 切削速度 150m/min 送り 0.2mm/刃 切込み量 2.0mm 評価法 10Pass切削を10回繰返したときの欠損
してない比率（未欠損率） 尚、超硬合金中の板状体WCは、任意の断面（破断面でも
可）を走査型電子顕微鏡にて観察し、三角状のものは全
て板状体WCとし、他の針状，棒状及び四角形状のWCにつ
いては最大寸法及び最小寸法を測定して板状体か否か決
め、板状体WCの量を求めた。Milling cutting test conditions Work material SCM440 (H B 250) 50 × 150 mm surface cutting Tip shape SNP432 Cutting speed 150 m / min Feed 0.2 mm / Flute depth 2.0 mm Evaluation method 10Pass Defect after cutting 10 times No ratio (non-missing rate) In addition, the plate-shaped body WC in the cemented carbide is observed with a scanning electron microscope at any cross section (even a fractured surface is possible), and all triangular shapes are plate-shaped bodies WC, other needle-shaped and rod-shaped. For the rectangular WC, the maximum dimension and the minimum dimension were measured to determine whether or not it was a plate-like body, and the amount of the plate-like body WC was obtained.
実施例２ 重量比で、WC/TiC/TaC＝70/15/15の固溶体粉末（第４固
溶体），実施例１で用いた第２固溶体，第３固溶体,WC,
Coの各粉末でもって、ほぼ63.0wt％WC-13.5wt％TiC-13.
5wt％TaC-10wt％Co組成になるように第３表の如く配合
した。この配合粉末を実施例１と同様の工程及び条件に
より超硬合金とした後、Ti-N2による従来のイオンプレ
ーテイング法（PVD法）でもって、超硬合金の表面に約
２μｍのTiN被覆膜を形成して本発明品３及び比較品２
を得た。さらに、本発明品３の内、超硬合金の焼結後に
実施例１の本発明品２と同条件でもって板状体WCの配向
を行った以外は本発明品３と同様に行って本発明品４を
得た。Example 2 By weight ratio, WC / TiC / TaC = 70/15/15 solid solution powder (fourth solid solution), second solid solution, third solid solution, WC, used in Example 1.
With each powder of Co, almost 63.0wt% WC-13.5wt% TiC-13.
The composition was as shown in Table 3 so that the composition was 5 wt% TaC-10 wt% Co. This compounded powder was made into a cemented carbide by the same steps and conditions as in Example 1, and then the surface of the cemented carbide was coated with TiN of about 2 μm by the conventional ion plating method (PVD method) using Ti—N 2. Inventive product 3 and comparative product 2 by forming a covering film
Got Furthermore, among the products 3 of the present invention, the same procedures as those of the product 3 of the present invention were performed except that the plate-like body WC was oriented under the same conditions as those of the product 2 of the present invention of Example 1 after sintering the cemented carbide. Invention product 4 was obtained.
こうして得た本発明品3,4及び比較品２の合金組織中の
板状体WCの量、及び被覆超硬合金の抗折力値を求めて第
４表に示し、さらに実施例１の切削試験条件でもって切
削試験を行い、その結果を第４表に併記した。The amounts of the plate-shaped bodies WC in the alloy structures of the inventive products 3 and 4 and the comparative product 2 thus obtained, and the transverse rupture strength value of the coated cemented carbide are determined and shown in Table 4. A cutting test was conducted under the test conditions, and the results are also shown in Table 4.
実施例３ 重量比で、WC/TiC/TaC＝60/10/30の固溶体粉末（第５固
溶体），実施例１で用いた第２固溶体,WC,Co及び平均粒
径1.5μmTaCの各粉末でもって、ほぼ53.4wt％WC-8.9wt
％TiC-26.7wt％TaC-11wt％Co組成になるように第５表の
如く配合した。この配向粉末を実施例１と同様の工程及
び条件により超硬合金とした後、TiCl4-N2-H2-CH4の混
合ガスによる従来のCVD法でもって、超硬合金の表面に
約２μｍのTi（C,N）被覆膜を形成して本発明品５及び
比較品３を得た。さらに、本発明品５の内、超硬合金の
焼結後に実施例１の本発明品２と同条件でもって板状体
WCの配向を行った以外は本発明品５と同様に行って本発
明品６を得た。 Example 3 By weight ratio, solid solution powder of WC / TiC / TaC = 60/10/30 (fifth solid solution), second solid solution used in Example 1, WC, Co and each powder of average particle size 1.5 μm TaC. Therefore, almost 53.4wt% WC-8.9wt
% TiC-26.7 wt% TaC-11 wt% Co was compounded as shown in Table 5. This oriented powder was formed into a cemented carbide by the same steps and conditions as in Example 1, and then the surface of the cemented carbide was coated with a conventional CVD method using a mixed gas of TiCl 4 —N 2 —H 2 —CH 4. Inventive product 5 and comparative product 3 were obtained by forming a Ti (C, N) coating film having a thickness of 2 μm. Further, among the product 5 of the present invention, a plate-like body was produced under the same conditions as the product 2 of the present invention of Example 1 after sintering the cemented carbide.
Inventive product 6 was obtained in the same manner as in the inventive product 5, except that the WC was oriented.
こうして得た本発明品5,6及び比較品３の合金組織中の
板状体WCの量、及び被覆超硬合金の抗折力値を求めて第
６表に示し、さらに実施例１の切削試験条件でもって切
削試験を行い、その結果を第６表に併記した。The amounts of the plate-shaped bodies WC in the alloy structures of the inventive products 5 and 6 and the comparative product 3 thus obtained, and the transverse rupture strength value of the coated cemented carbide are determined and shown in Table 6. A cutting test was conducted under the test conditions, and the results are also shown in Table 6.
実施例４ 特開昭57-34008号公報に開示の方法で作製した板状体の
炭化タングステンの含有したWC（Ａ−WC）と市販のWC
（Ｂ−WC）とCoとの各粉末を用いてWC−６％Co組成にな
るように第７表の如く配合した。この配合粉末を実施例
１と同様の工程及び条件により超硬合金とした後、実施
例１と同様にして超硬合金の表面にTiC被覆膜を形成し
て本発明品７及び比較品４を得た。 Example 4 WC (A-WC) containing tungsten carbide in a plate-like body produced by the method disclosed in JP-A-57-34008 and commercially available WC
Powders of (B-WC) and Co were used and blended as shown in Table 7 so as to have a WC-6% Co composition. This compounded powder was made into a cemented carbide by the same steps and conditions as in Example 1, and then a TiC coating film was formed on the surface of the cemented carbide in the same manner as in Example 1 to invent the present invention 7 and the comparative product 4. Got
こうして得た本発明品７及び比較品４の超硬合金中の板
状体WCの量と被覆超硬合金の抗折力を求めて第７表に併
記した。The amounts of the plate-shaped bodies WC in the cemented carbides of the invention products 7 and the comparative products 4 thus obtained and the transverse rupture strength of the coated cemented carbides were determined and shown in Table 7.
（発明の効果） 本発明の高強度被覆超硬合金部材は、従来の被覆超硬合
金に比べて、抗折力において15％〜39％向上するという
効果があり、切削試験による耐欠損性において、極めて
著しく向上するという効果がある。 (Effect of the Invention) The high-strength coated cemented carbide member of the present invention has an effect of improving the transverse rupture strength by 15% to 39% as compared with the conventional coated cemented carbide, and has a fracture resistance in a cutting test. It has an effect of remarkably improving.
このことから、本発明の高強度被覆超硬合金部材は、従
来の被覆超硬合金の用途から、さらに従来の被覆超硬合
金では耐欠損性又は耐衝撃性の問題から困難とされてい
るような用途にまで使用できる産業上有用な材料であ
る。From this, it is considered that the high-strength coated cemented carbide member of the present invention is difficult because of the use of the conventional coated cemented carbide, and the conventional coated cemented carbide has a problem of fracture resistance or impact resistance. It is an industrially useful material that can be used for various purposes.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２３Ｃ 16/22 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Internal reference number FI technical display location C23C 16/22
Claims (4)
化物，複合炭酸化物，複合炭窒酸化物、及びＷとTiとZ
r,Hf,V,Nb,Ta,Cr,Moの中の少なくとも１種とを含有した
複合炭化物，複合炭窒化物，複合炭酸化物，複合炭窒酸
化物から選ばれた少なくとも１種のBl型固溶体と、炭化
タングステンとでなる硬質相80〜98重量％と、残りCo及
び／又はNiを主成分とする結合相と不可避不純物とから
なる超硬合金の表面に被覆膜を形成してなる被覆超硬合
金であって、該超硬合金は三角形状、又は最大寸法が２
〜20μｍで、この最大寸法が最小寸法の少なくとも２倍
でなる針状，棒状，四角形状を主とする多角形状の中の
少なくとも１種として観察される板状体の炭化タングス
テンが該超硬合金全体の少なくとも５体積％混在してい
ることを特徴とする高強度被覆超硬合金部材。1. A composite carbide containing W and Ti, a composite carbonitride, a composite carbonate, a composite carbonitride, and W, Ti and Z.
At least one Bl type selected from complex carbide containing at least one of r, Hf, V, Nb, Ta, Cr and Mo, complex carbonitride, complex carbonate, complex carbonitride A coating film is formed on the surface of a cemented carbide consisting of a solid solution and 80 to 98% by weight of a hard phase composed of tungsten carbide, the remaining binder phase containing Co and / or Ni as a main component, and inevitable impurities. A coated cemented carbide, the cemented carbide having a triangular shape or a maximum dimension of 2
A plate-shaped tungsten carbide, which is observed as at least one of a polygonal shape having a maximum dimension of at least 20 μm and at least twice the minimum dimension, such as a needle-like shape, a rod-like shape, or a quadrangular shape. A high-strength coated cemented carbide member characterized by being mixed in at least 5% by volume of the whole.
向に配向されていることを特徴とする特許請求の範囲第
１項記載の高強度被覆超硬合金部材。2. The high-strength coated cemented carbide member according to claim 1, wherein the tungsten carbide in the plate-shaped body is oriented in a fixed direction.
％と、残りCo及び／又はNiを主成分とする結合相と不可
避不純物とからなる超硬合金の表面に被覆膜を形成して
なる被覆超硬合金であって、該超硬合金は三角形状、又
は最大寸法が２〜20μｍで、この最大寸法が最小寸法の
少なくとも２倍でなる針状，棒状，四角形状を主とする
多角形状の中の少なくとも１種として観察される板状体
の炭化タングステンが該超硬合金全体の少なくとも５体
積％混在していることを特徴とする高強度被覆超硬合金
部材。3. A coating film is formed on the surface of a cemented carbide which is composed of 80 to 98% by weight of a hard phase made of tungsten carbide, the remainder being a binder phase containing Co and / or Ni as a main component and unavoidable impurities. Which is a coated cemented carbide, wherein the cemented carbide has a triangular shape, or a polygon having a maximum dimension of 2 to 20 μm and having a maximum dimension that is at least twice the minimum dimension, such as a needle shape, a rod shape, or a square shape. A high-strength coated cemented carbide member, characterized in that at least 5% by volume of the plate-shaped tungsten carbide observed as at least one of the shapes is mixed in the entire cemented carbide.
向に配向されていることを特徴とする特許請求の範囲第
３項記載の高強度被覆超硬合金部材。4. The high-strength coated cemented carbide member according to claim 3, wherein the tungsten carbide of the plate-shaped body is oriented in a fixed direction.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63289194A JPH0711069B2 (en) | 1988-11-16 | 1988-11-16 | High-strength coated cemented carbide member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63289194A JPH0711069B2 (en) | 1988-11-16 | 1988-11-16 | High-strength coated cemented carbide member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02138434A JPH02138434A (en) | 1990-05-28 |
| JPH0711069B2 true JPH0711069B2 (en) | 1995-02-08 |
Family
ID=17739995
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63289194A Expired - Fee Related JPH0711069B2 (en) | 1988-11-16 | 1988-11-16 | High-strength coated cemented carbide member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0711069B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100286970B1 (en) | 1996-12-16 | 2001-04-16 | 오카야마 노리오 | Cemented carbide, its production method and cemented carbide tools |
-
1988
- 1988-11-16 JP JP63289194A patent/JPH0711069B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02138434A (en) | 1990-05-28 |
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