JP3217404B2 - Cermet for rotary tools - Google Patents
Cermet for rotary toolsInfo
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- JP3217404B2 JP3217404B2 JP28410391A JP28410391A JP3217404B2 JP 3217404 B2 JP3217404 B2 JP 3217404B2 JP 28410391 A JP28410391 A JP 28410391A JP 28410391 A JP28410391 A JP 28410391A JP 3217404 B2 JP3217404 B2 JP 3217404B2
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Description
【０００１】[0001]
【産業上の利用分野】本発明は切削工具、特に回転工具
（ドリル、エンドミル、ボールエンドミル、リーマ等）
に利用されるサーメットに関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cutting tool, especially a rotary tool (drill, end mill, ball end mill, reamer, etc.).
Cermet used for
【０００２】[0002]
【従来技術・課題】従来ＴｉＣ基ないしはＴｉ（Ｃ、
Ｎ）基サーメットは、ＷＣ基合金に比べ、耐酸化性や被
削材との非親和性に優れている等の特徴があるために、
切削工具として使用されている。2. Description of the Related Art Conventionally, TiC groups or Ti (C,
N) -based cermets have characteristics such as superior oxidation resistance and incompatibility with work materials compared to WC-based alloys.
Used as a cutting tool.
【０００３】ところが、こうしたＴｉＣ基ないしはＴｉ
（Ｃ、Ｎ）基サーメットは、機械的な耐欠損性能（以下
耐欠損性能と称す）、熱衝撃及び熱の不均一による亀裂
の進展に伴う耐欠損性能（以下耐熱亀裂性能と称す）、
高温高圧下での耐塑性変形性能（以下耐塑性変形性能と
称す）が必ずしも高くない等の理由のために使用範囲が
限定されている。However, such a TiC group or Ti
The (C, N) -based cermet has mechanical fracture resistance (hereinafter referred to as fracture resistance), fracture resistance due to crack propagation due to thermal shock and uneven heat (hereinafter referred to as heat crack resistance),
The range of use is limited because plastic deformation resistance under high temperature and high pressure (hereinafter referred to as plastic deformation resistance) is not necessarily high.
【０００４】それ故、ＴｉＣ基ないしはＴｉ（Ｃ、Ｎ）
基サーメントの性能を改善すべく種々の提案がなされて
いる。例えば、特公昭６３−３０１７には、添加成分と
してＷＣ、ＴａＣ、ＮｂＣ、ＺｒＣ、かつ結合相成分と
してＣｏ（Ｎｉ）を用いることにより、耐摩耗性及び耐
衝撃性の向上を図ったものが開示されている。Therefore, TiC groups or Ti (C, N)
Various proposals have been made to improve the performance of the base statement. For example, Japanese Patent Publication No. Sho 63-3017 discloses an improvement in wear resistance and impact resistance by using WC, TaC, NbC, ZrC as an additive component and Co (Ni) as a binder phase component. Have been.
【０００５】しかし、この特公昭６３−３０１７号に開
示されたサーメットを、ドリル、リーマ、エンドミル、
ボールエンドミル等の回転工具に適用した場合、（１）
切刃部は、切削性や再研摩性を考慮してシャープエッジ
が必要であるが、刃先加工中や使用中にチッピングしや
すく、（２）比較的低速切削のため、切削抵抗が高く発
熱しやすいことから、熱亀裂が発生して欠損したり塑性
変形しやすい、などの問題があった。そのため、回転工
具用のＴｉＣ基ないしはＴｉ（Ｃ、Ｎ）基サーメットと
して、特に平均粒径を限定したり（特開平２−２３２３
３３）、粒子径に分布を持たせたりする手法（特開平３
−２３４７）等も試みられてきたが、未だ上記２点を十
分に解決するに至っていない。[0005] However, the cermet disclosed in Japanese Patent Publication No. 63-3017 is disclosed by using a drill, a reamer, an end mill,
When applied to rotating tools such as ball end mills, (1)
The cutting edge must have a sharp edge in consideration of cutting properties and regrindability. However, it is easy to chip during cutting and during use. (2) Since cutting is relatively slow, cutting resistance is high and heat is generated. As a result, there is a problem that a thermal crack is generated, and the chip is easily broken or plastically deformed. For this reason, as a TiC-based or Ti (C, N) -based cermet for a rotary tool, the average particle diameter is particularly limited (Japanese Unexamined Patent Publication (Kokai) No. 2-2323).
33), a method of giving a distribution to the particle size (Japanese Unexamined Patent Application Publication No.
−2347) have been tried, but the above two points have not yet been sufficiently solved.
【０００６】[0006]
【解決手段・作用】したがって、本発明者は、回転工具
として使用した場合であっても、耐摩耗性（耐欠損
性）、耐熱衝撃性、耐塑性変形性に優れ、上記（１）
（２）の課題を解決するサーメットを得るために鋭意検
討した結果、本発明に到達したものである。即ち、本発
明の回転工具用サーメット粉末組成物は、 ａ）４Ａ族遷移金属の炭化物、窒化物及び炭窒化物の１
種以上から主としてなる粉末（４Ａ族粉末という）２０
〜５５重量％、及び ｂ）５Ａ族、６Ａ族遷移金属の炭化物、窒化物及び炭窒
化物の１種以上から主としてなる粉末（５Ａ・６Ａ族粉
末という）２０〜７０重量％、及び ｃ）鉄族金属の１種以上から主としてなる粉末（鉄族粉
末という）１０〜２５重量％を含み、４Ａ族粉末が、平
均粒径０．１〜１．０μｍの微粉末３０重量％、及び平
均粒径１．０〜３．０μｍの粗粉末７０重量％の二群分
布となっている、ことを特徴とする。なお、上記各粉末
は、それぞれ、工業的規格のレベルで不純物を含有する
粉末も該当し、本発明はこれらの場合を含むものである
ため、「主としてなる」のような記載としている。Accordingly, the inventor of the present invention has excellent abrasion resistance (breakage resistance), thermal shock resistance, and plastic deformation resistance even when used as a rotary tool.
As a result of intensive studies to obtain a cermet that solves the problem (2), the present invention has been achieved. That is, the cermet powder composition for a rotary tool of the present invention comprises: a) one of a carbide, nitride and carbonitride of a 4A group transition metal;
Powder consisting of more than one kind (referred to as 4A group powder) 20
And b) 20 to 70% by weight of a powder (referred to as Group 5A / 6A powder) mainly composed of one or more of carbides, nitrides and carbonitrides of Group 5A and Group 6A transition metals; and c) Iron Group 4A powder containing 10 to 25% by weight of a powder (referred to as iron group powder) mainly composed of at least one group metal, 30% by weight of fine powder having an average particle size of 0.1 to 1.0 μm, and an average particle size It is characterized by having a two-group distribution of 70% by weight of coarse powder of 1.0 to 3.0 μm. In addition, each of the above powders also corresponds to a powder containing an impurity at the level of an industrial standard, and the present invention includes these cases.
Therefore, it is described as "mainly" .
【０００７】又、本発明の回転工具用サーメットは ａ）４Ａ族遷移金属の１種以上、５Ａ族及び６Ａ族遷移
金属の１種以上、及びＣ及びＮの１種以上から主として
なる硬質分散相７０〜９５ｖｏｌ％、及び ｂ）鉄族金属の１種以上から主としてなる結合相５〜３
０ｖｏｌ％、からなり硬質分散相が４Ａ族遷移金属の炭
化物、窒化物及び炭窒化物の１種以上から主としてなる
結晶粒子（I型粒子という）、及び４Ａ族遷移金属を芯
部より周辺部に多く含むと共に５Ａ族、６Ａ族遷移金属
の１種以上を周辺部より芯部に多く含む炭化物、窒化物
及び炭窒化物の１種以上から主としてなる結晶粒子（II
型粒子という）、を有し、I型粒子が、平均粒径０．１
〜０．５μｍの微結晶粒子（Ia粒子という）、及び平均
粒径１．０〜２．０μｍの粗結晶粒子（Ib型粒子とい
う）の二群分布となっており、かつIb／（Ia＋Ib）は
０．５以上１．０未満（体積比）である、ことを特徴と
する。なお、上記硬質分散相、結合相、I型粒子、II型
粒子は、それぞれ、工業的規格のレベルで不純物を含む
場合があり、本発明はこれらの場合を含むものであるた
め、「主としてなる」のような記載としている。The cermet for a rotary tool according to the present invention comprises: a) at least one transition metal of group 4A, a transition metal of group 5A and a transition of group 6A;
Mainly from one or more metals and one or more C and N
70 to 95 vol% of a hard dispersed phase, and b) a bonded phase mainly composed of at least one kind of iron group metal.
0 vol%, and the hard dispersed phase is a 4A transition metal charcoal.
Mainly consisting of one or more of nitrides, nitrides and carbonitrides
Crystal particles (referred to as type I particles) and 4A transition metal
Group 5A, group 6A transition metal
And nitrides containing at least one of the following in the core than in the periphery
And crystal grains mainly composed of at least one carbonitride (II
I-type particles having an average particle size of 0.1
~ 0.5μm microcrystalline particles (referred to as Ia particles) and average
Coarse crystal particles having a particle size of 1.0 to 2.0 μm (called Ib type particles)
U), and Ib / (Ia + Ib)Is
0.5that's all1.0Less than(Volume ratio)
I do. The hard dispersed phase, the binder phase, the I-type particles, the II-type
Each particle contains impurities at the level of the industrial standard
In some cases, the present invention includes these casesWas
"Become the Lord"It is described as follows.
【０００８】本発明者はＴｉＣ基ないしはＴｉ（Ｃ、
Ｎ）基サーメットをドリル、エンドミル等の回転工具と
して応用展開する際、上記課題（１）（２）を解決する
ために、さらなる耐欠損性能や耐摩耗性能を得る必要性
にせまられ、以下の様な組成及び組織制御によって多大
なる作用効果を見い出した。The present inventor has proposed a TiC group or Ti (C,
N) When applying and developing the base cermet as a rotary tool such as a drill and an end mill, it is necessary to obtain further fracture resistance and wear resistance in order to solve the above problems (1) and (2). A great amount of action and effect was found by such composition and tissue control.
【０００９】すなわち、サーメット粉末組成物について
４Ａ族粉末の平均粒径を微粉末０．１〜１．０μｍ、粗
粉末１．０〜３．０μｍの二群分布とし、得られるサー
ミットについてＩ型粒子の粒径分布を（Ｉａ型）0.1〜
0.5μｍ、（Ｉｂ型）1.0〜2.0μｍ、Ｉｂ／（Ｉａ＋Ｉ
ｂ）は0.5以上1.0未満（体積比）の二群分布とすること
によって、最も耐摩耗性能、耐溶着性能が優れることを
発明した。なお、さらに好ましくは（Ｉａ型）0.1〜0.3
μｍ、（Ｉｂ型）1.0〜2.0μｍ、Ｉｂ／（Ｉａ＋Ｉｂ）
＝0.6〜0.8である。That is, in the cermet powder composition, the average particle diameter of the 4A group powder is a two-group distribution of fine powder of 0.1 to 1.0 μm and coarse powder of 1.0 to 3.0 μm. (Ia type) 0.1 ~
0.5 μm, (Ib type) 1.0 to 2.0 μm, Ib / (Ia + I
By inventing b) as a two-group distribution of 0.5 or more and less than 1.0 (volume ratio), the inventors have invented the most excellent wear resistance and welding resistance. In addition, (Ia type) 0.1 to 0.3 is more preferable.
μm, (Ib type) 1.0-2.0 μm, Ib / (Ia + Ib)
= 0.6 to 0.8.
【００１０】このようにＩ型粒子の粒子径に分布を持た
せることにより、耐摩耗性・耐溶着性の改良に効果があ
り、しかも二群分布とすることにより、弊害である靱性
の低下を防止する効果がある。Providing a distribution in the particle size of the I-type particles in this way is effective in improving abrasion resistance and welding resistance. In addition, by forming a two-group distribution, a reduction in toughness, which is an adverse effect, is obtained. It has the effect of preventing.
【００１１】一般に、４Ａ族金属の炭化物、窒化物及び
炭窒化物は焼結過程において、組織中の硬質相となる５
Ａ族、６Ａ族金属の炭化物、窒化物あるいは炭窒化物と
固溶して硬質粒子を形成したり、硬質粒子の芯部として
その周辺に５Ａ族、６Ａ族金属の炭化物、窒化物あるい
は炭窒化物を析出生成していわゆる二重構造組織の硬質
粒子を形成したり、一部結合相へ固溶するのが通例であ
った。この時、４Ａ族の炭化物、窒化物あるいは炭窒化
物が５Ａ族、６Ａ族の炭化物、窒化物、炭窒化物と固溶
することにより（ＩＩ型粒子）、生成される粒子（硬質
相）の硬度や靱性が向上する。In general, carbides, nitrides and carbonitrides of Group 4A metals become hard phases in the structure during the sintering process.
Form a hard particle by forming a solid solution with a carbide, nitride or carbonitride of a group A or 6A metal, or form a core of the hard particle around a carbide, nitride or carbonitride of a group 5A or 6A metal It is customary to precipitate and form a product to form hard particles having a so-called double structure, or to form a solid solution in a part of the binder phase. At this time, when the carbide, nitride or carbonitride of the 4A group forms a solid solution with the carbide, nitride or carbonitride of the 5A or 6A group (II type particles), the particles (hard phase) formed are formed. Hardness and toughness are improved.
【００１２】また，４Ａ族金属の炭化物、窒化物あるい
は炭窒化物を単独粒子として存在させれば（Ｉ型粒
子）、４Ａ族金属の炭化物、窒化物あるいは炭窒化物粒
子の本来の性質である高強度、高融点が生かされ、工具
としての耐摩耗性や耐熱性が向上する。Further, if carbide, nitride or carbonitride of Group 4A metal is present as a single particle (I-type particles), it is an intrinsic property of carbide, nitride or carbonitride particles of Group 4A metal. Utilizing high strength and high melting point, wear resistance and heat resistance as a tool are improved.
【００１３】したがって、添加した４Ａ族金属の炭化
物、窒化物あるいは炭窒化物の効果を十二分に発揮する
為には一部を単独粒子として残留させ残部を他の硬質相
中へ固溶させるのが最も効果的である。Therefore, in order to sufficiently exert the effect of the added carbide, nitride or carbonitride of the Group 4A metal, a part is left as a single particle and the remainder is dissolved in another hard phase. Is most effective.
【００１４】このような４Ａ族金属の炭化物、窒化物あ
るいは炭窒化物粒子の残留、固溶を高精度に制御し上記
効果を得る為には、原料粉末について粒子径の小さい粒
子ほど固溶が速く進行する性質を利用して、必要固溶量
分の４Ａ族金属の炭化物、窒化物、炭窒化物粒子をあら
かじめ微粒化し、残留しうる分量を粗粒化しておく、即
ち粒子径の二群分布化を作っておくことが最も効果的で
ある。In order to control the residual and solid solution of such carbide, nitride or carbonitride particles of the Group 4A metal with high accuracy and to obtain the above-mentioned effect, the solid solution of the raw material powder should have a smaller particle diameter. Utilizing the fast-moving property, the necessary solid solution amount of carbide, nitride and carbonitride particles of the Group 4A metal is atomized beforehand, and the remaining amount is coarsened in advance. It is most effective to create a distribution.
【００１５】その結果として、焼結体の組織中の４Ａ族
金属の炭化物、窒化物、炭窒化物の単独粒子（Ｉ型粒
子）は、粒子径の二群分布（Ia型粒子、Ib型粒子）をも
つこととなるのである。尚、こうした本発明の作用を模
式的に図１に示す。もっとも、Ｉ型粒子の全てが所定の
二群分布（Ｉａ，Ｉｂ）に該当する必要はなく、Ｉ型粒
子全体の８０ｖｏｌ％以上がＩａ型粒子、Ｉｂ型粒子に
なっていればよい。ＩＩ型粒子の場合は、基本的には二
群の分布をとる必要性はないが、0.5〜3.0μｍの範囲が
良好で、好ましくは1.0〜2.0μｍである。上記範囲外0.
5μｍ以下では靱性が低下し、3.0μｍ以上では加工時に
チッピングが生じ、シャープエッジが作れない。又耐摩
耗性も低下してしまう。そのため、原料としての５Ａ・
６Ａ族粉末の平均粒径についても１．０〜３．０μｍの
範囲にすることが好ましい。又、原料粉末としての４Ａ
族粉末、５Ａ・６Ａ族粉末は相互に固溶された粉末を使
用してもよい。As a result, the single particles (I-type particles) of carbides, nitrides, and carbonitrides of the Group 4A metal in the structure of the sintered body have two particle size distributions (Ia-type particles, Ib-type particles). ). FIG. 1 schematically shows the operation of the present invention. However, it is not necessary that all of the I-type particles correspond to the predetermined two-group distribution (Ia, Ib), and it suffices that 80% by volume or more of the entire I-type particles are Ia-type particles and Ib-type particles. In the case of type II particles, there is basically no need to take the distribution of two groups, but the range of 0.5 to 3.0 μm is good, preferably 1.0 to 2.0 μm. Outside the above range 0.
If it is 5 μm or less, the toughness decreases, and if it is 3.0 μm or more, chipping occurs during processing, and a sharp edge cannot be formed. Also, wear resistance is reduced. Therefore, 5A
The average particle diameter of the 6A group powder is also preferably in the range of 1.0 to 3.0 μm. 4A as raw material powder
As the powder of the group 5A and the powder of the group 6A and 6A, powders which are mutually dissolved may be used.
【００１６】本発明はI型粒子及びII型粒子を有するサ
ーメットであれば種々の組成のものに適用できる。特に
特開平２−１９０４３８号に開示されたサーメット、即
ち遷移金属（４Ａ族、５Ａ、６Ａ族）と非金属（Ｃ、
Ｎ）とのモル比が１：０．８５〜１．０であり、遷移金
属相互のモル比が４Ａ族：５Ａ族：６Ａ族＝０．５〜
０．８５：０．０５〜０．３０：０．０５〜０．３０で
あり、かつ４Ａ族遷移金属についてＴｉ／ＩＶ族≧０．
８、５Ａ族遷移金属についてＴａ／５Ａ族≧０．３、６
Ａ族遷移金属についてＷ／６Ａ族≧０．９であり、非金
属相互のモル比がＣ：Ｎ＝０．４〜０．９：０．１〜
０．６である組成のものに好適である。又、I型粒子は
硬質分散相中に５〜５０ｖｏｌ％含まれ、Ｎ／（Ｃ＋
Ｎ）≧０．２５であるものが好ましく、II型粒子は４Ａ
族、５Ａ族及び６Ａ族金属の含有比率が傾斜的になって
いること、換言すれば４Ａ族金属の含有率が芯部から周
辺部に向けて傾斜的に大となり、一方５Ａ族、６Ａ族金
属の含有率が芯部から周辺部に向けて傾斜的に小となっ
ていることが好ましい。尚、I型、II型粒子の意義や組
成の限定理由等については同公報を参照されたい。The present invention can be applied to various cermets having I-type particles and II-type particles. In particular, cermets disclosed in JP-A-2-190438, namely, transition metals (groups 4A, 5A, 6A) and nonmetals (C,
N) and the molar ratio of transition metals to each other is group 4A: group 5A: group 6A = 0.5 to
0.85: 0.05 to 0.30: 0.05 to 0.30, and Ti / IV ≧ 0.
Ta / 5A group> 0.3,6 for group 8,5A transition metals
The group A transition metal is W / 6A ≧ 0.9, and the molar ratio between nonmetals is C: N = 0.4 to 0.9: 0.1 to
It is suitable for those having a composition of 0.6. Further, the type I particles are contained in the hard dispersed phase in an amount of 5 to 50 vol%, and N / (C +
N) ≧ 0.25 is preferred, and the type II particles are 4A
Group, group 5A and group 6A metal content is graded, in other words, the group 4A metal content is graded from core to periphery, while group 5A and group 6A metal. It is preferable that the content of the metal decreases inclining from the core to the periphery. For the significance of the type I and type II particles and the reasons for limiting the composition, refer to the publication.
【００１７】[0017]
【実施例】平均粒径2.0μｍ以下のＴｉＣ、ＴｉＮ、Ｔ
ａＣ、ＴａＮ、ＷＣ、Ｎｉ、Ｃｏ粉末及び種々の固溶体
粉末｛（Ｔａ、Ｎｂ、Ｗ）Ｃ、（Ｔｉ、Ｔａ、Ｗ）Ｃな
ど｝を用いて表１に示す配合組成の混合粉末を得た。こ
のとき、ＴｉＣ及びＴｉＮ原料粉末は、粒度分布の異な
る粉末を同時に混合したり、あらかじめ予備粉砕したも
のを未粉砕の粉末と混合したりして、平均粒径０．１〜
１．０μｍの微粉末３０ｖｏｌ％及び１．０〜３．０μ
ｍの粗粉末７０ｖｏｌ％の二群分布とした。EXAMPLE TiC, TiN, T having an average particle size of 2.0 μm or less
Using aC, TaN, WC, Ni, Co powders and various solid solution powders {(Ta, Nb, W) C, (Ti, Ta, W) C, etc.}, mixed powders having the composition shown in Table 1 were obtained. . At this time, the TiC and TiN raw material powders are obtained by mixing powders having different particle size distributions at the same time, or by mixing a preliminarily crushed powder with an unmilled powder to obtain an average particle diameter of 0.1 to
30 μ% of fine powder of 1.0 μm and 1.0 to 3.0 μ
m, a two-group distribution of 70 vol% of coarse powder.
【００１８】[0018]
【表１】 [Table 1]
【００１９】これらの混合粉末を、丸棒形状に成形し、
１０〜２００ＴｏrrＮ2雰囲気中１４００〜１５５０℃
で１時間焼結し、試料No.１〜１９の焼結体を製作し
た。次に、焼結体を化学分析することによって、硬質分
散相成分（Ｔｉ、Ｔａ、Ｗ）、結合相成分（Ｎｉ、Ｃ
ｏ）及び軽元素（Ｃ、Ｎ）を定量した（表２）。即ち、
硬質分散相成分や結合相を構成する４Ａ族、５Ａ族、６
Ａ族元素及び鉄族元素については、試料（焼結体）を粉
砕し、これをフッ酸・硫酸溶液中に加熱分解し、ＩＣＰ
発光分析法（誘導結合プラズマ発光分析法）により定量
した。軽元素（Ｃ，Ｎ）については、粉砕した試料を用
いて赤外線吸光法により定量した。又、Ｉａ，Ｉｂ型粒
子の量比については、試料の組織をＳＥＭで観察し、得
られた組織写真について画像解析を行なうことにより測
定した。さらに全ての試料No.１〜１９について、直径
１０ｍｍ、全長６０ｍｍのストレートシャンク４枚刃ソ
リッドエンドミルを製作し、テスト、を行なった。The mixed powder is formed into a round bar shape,
1400-1550 ° C. in 10-200 Torr N 2 atmosphere
For 1 hour to produce sintered bodies of Sample Nos. 1 to 19. Next, a hard dispersed phase component (Ti, Ta, W) and a binder phase component (Ni, C
o) and light elements (C, N) were quantified (Table 2). That is,
Group 4A, group 5A, 6 constituting the hard dispersed phase component or the binder phase
For group A element and iron group element, a sample (sintered body) is pulverized and decomposed by heating in a hydrofluoric acid / sulfuric acid solution to obtain an ICP.
It was quantified by emission spectrometry (inductively coupled plasma emission spectrometry). Light elements (C, N) were quantified by an infrared absorption method using a crushed sample. The quantitative ratio of the Ia and Ib type particles was measured by observing the structure of the sample by SEM and performing image analysis on the obtained structure photograph. Further, a straight shank 4-flute solid end mill having a diameter of 10 mm and a total length of 60 mm was manufactured and tested for all samples Nos. 1 to 19.
【００２０】試料No.１〜４は本発明の組成の検討、No.
１２〜１３はその比較例、No.５〜７は本発明のＮ／Ｃ
＋Ｎ比検討、No.１４〜１５はその比較例、No.８〜９は
本発明の結合相の検討、No.１６〜１７はその比較例、N
o.１０〜１１は本発明の粒径の検討、No.１８〜１９は
その比較例である。なお、ＴａＣ，ＴａＮに代えてＮｂ
Ｃ，ＮｂＮを使用しても同様な効果が得られた。Samples Nos. 1 to 4 were obtained by examining the composition of the present invention.
12 to 13 are comparative examples, and Nos. 5 to 7 are N / C of the present invention.
Nos. 14 to 15 are comparative examples, Nos. 8 to 9 are studies on the binder phase of the present invention, Nos. 16 to 17 are comparative examples thereof, N
o.10 to 11 are studies of the particle size of the present invention, and Nos. 18 to 19 are comparative examples. Note that Nb is used instead of TaC and TaN.
Similar effects were obtained by using C and NbN.
【００２１】〈テスト方法〉 耐摩耗試験（ＮＣフライスによる連続切削） テスト品形状…ストレートシャンク４枚刃ソリッドエン
ドミル 被切削材…ＪＩＳ・ＳＮＣＭ８（ブリネル硬さＨB＝３
００） 切削速度…１００ｍ／ｍｉｎ、乾式 送り …0.2ｍｍ／ｒｅｖ 切込み …５ｍｍ 寿命判定…底刃、外周刃の摩耗量及び刃先状況<Test Method> Wear resistance test (continuous cutting by NC milling machine) Test product shape: straight shank, 4-flute solid end mill Cutting material: JIS SNCM8 (Brinell hardness H B = 3)
00) Cutting speed: 100 m / min, dry feed: 0.2 mm / rev Depth of cut: 5 mm Life judgment: Wear of bottom blade and outer peripheral blade and cutting edge condition
【００２２】 耐熱衝撃試験（ＮＣフライスによる断
続切削） テスト品形状…ストレートシャンク４枚刃ソリッドエン
ドミル 被切削材…ＪＩＳ・ＳＮＣＭ８ 切削速度…１００ｍ／ｍｉｎ、湿式 送り …0.3ｍｍ／ｒｅｖ 切込み …５ｍｍ 寿命判定…衝撃回数及び刃先状況Thermal shock test (intermittent cutting by NC milling) Test product shape: straight shank 4-flute solid end mill Cutting material: JIS / SNCM8 Cutting speed: 100 m / min, wet feed: 0.3 mm / rev Depth: 5 mm Life span judgment ... number of impacts and cutting edge conditions
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【発明の効果】以上の結果より本発明による回転工具用
サーメット試料No.１〜No.１１は、組成や組織を厳密に
制御することにより回転工具として使用するに十分な耐
摩耗性能、耐熱衝撃性能が得られた。From the above results, the cermet samples No. 1 to No. 11 for rotary tools according to the present invention have sufficient wear resistance and thermal shock resistance to be used as rotary tools by strictly controlling the composition and structure. Performance was obtained.
【図１】 本発明を模式的に表わした図FIG. 1 is a diagram schematically illustrating the present invention.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 29/00 - 29/18 B22F 7/00 - 7/08 C22C 1/04 - 1/05 ──────────────────────────────────────────────────続 き Continued on the front page (58) Fields surveyed (Int. Cl. 7 , DB name) C22C 29/00-29/18 B22F 7 /00-7/08 C22C 1/04-1/05
Claims (4)
炭窒化物の１種以上から主としてなる粉末（４Ａ族粉末
という）２０〜５５重量％、 ｂ）５Ａ族、６Ａ族遷移金属の炭化物、窒化物及び炭窒
化物の１種以上から主としてなる粉末（５Ａ・６Ａ族粉
末という）２０〜７０重量％、及び ｃ）鉄族金属の１種以上から主としてなる粉末（鉄族粉
末という）１０〜２５重量％を含み、 ４Ａ族粉末が、平均粒径０．１〜１．０μｍの微粉末３
０重量％、及び平均粒径１．０〜３．０μｍの粗粉末７
０重量％の二群分布となっている、ことを特徴とする回
転工具用サーメット粉末組成物。1. a) 20 to 55% by weight of a powder (referred to as Group 4A powder) mainly composed of at least one of carbides, nitrides and carbonitrides of Group 4A transition metals; b) a powder of Group 5A and Group 6A transition metals 20 to 70% by weight of a powder mainly composed of one or more of carbides, nitrides and carbonitrides (referred to as 5A or 6A group powder); and c) Powder mainly composed of one or more of iron group metals (referred to as iron group powder) Group A powder comprising 10 to 25% by weight;
0% by weight and coarse powder 7 having an average particle size of 1.0 to 3.0 μm
A cermet powder composition for a rotary tool, which has a two-group distribution of 0% by weight .
び６Ａ族遷移金属の１種以上、及びＣ及びＮの１種以上
から主としてなる硬質分散相７０〜９５ｖｏｌ％、及び ｂ）鉄族金属の１種以上から主としてなる結合相５〜３
０ｖｏｌ％、からなり、 硬質分散相が４Ａ族遷移金属
の炭化物、窒化物及び炭窒化物の１種以上から主として
なる結晶粒子（I型粒子という）、及び４Ａ族遷移金属
を芯部より周辺部に多く含むと共に５Ａ族、６Ａ族遷移
金属の１種以上を周辺部より芯部に多く含む炭化物、窒
化物及び炭窒化物の１種以上から主としてなる結晶粒子
（II型粒子という）、を有し、 I型粒子が、平均粒径０．１〜０．５μｍの微結晶粒子
（Ia粒子という）、及び平均粒径１．０〜２．０μｍの
粗結晶粒子（Ib型粒子という）の二群分布となってお
り、かつIb／（Ia＋Ib）は０．５以上１．０未満（体積
比）である、ことを特徴とする回転工具用サーメット。2. a) 70 to 95% by volume of a hard dispersed phase mainly comprising one or more group 4A transition metals, one or more group 5A and 6A transition metals, and one or more C and N; and b) Bonded phase 5 to 3 mainly composed of one or more iron group metals
0 vol%, and the hard dispersed phase is mainly composed of at least one of carbides, nitrides, and carbonitrides of group 4A transition metal (referred to as I-type particles), and group 4A transition metal from the core to the periphery. And crystal grains (referred to as type II grains) mainly composed of at least one of carbides, nitrides, and carbonitrides, which contain more than one type of transition metal of group 5A or 6A in the core than in the periphery. The type I particles are composed of microcrystalline particles having an average particle size of 0.1 to 0.5 μm (referred to as Ia particles) and coarse crystal particles having an average particle size of 1.0 to 2.0 μm (referred to as Ib type particles). A cermet for a rotating tool, wherein the cermet has a group distribution, and Ib / (Ia + Ib) is 0.5 or more and less than 1.0 (volume ratio).
である請求項２記載の回転工具用サーメット。3. The type II particles have an average particle size of 0.5 to 3.0 μm.
The cermet for a rotary tool according to claim 2, wherein
属（Ｃ、Ｎ）とのモル比が１：０．８５〜１．０であ
り、 遷移金属相互のモル比が４Ａ族：５Ａ族：６Ａ族＝０．
５〜０．８５：０．０５〜０．３０：０．０５〜０．３
０であり、かつ４Ａ族遷移金属についてＴｉ／４Ａ族≧
０．８、５Ａ族遷移金属についてＴａ／５Ａ族≧０．
３、６Ａ族遷移金属についてＷ／６Ａ族≧０．９であ
り、 非金属相互のモル比がＣ：Ｎ＝０．４〜０．９：０．１
〜０．６である、請求項２記載の回転工具用サーメッ
ト。4. The transition metal (group 4A, 5A, 6A) and the non-metal (C, N) have a molar ratio of 1: 0.85 to 1.0, and the transition metal has a mutual molar ratio of group 4A. : 5A group: 6A group = 0.
5 to 0.85: 0.05 to 0.30: 0.05 to 0.3
0, and Ti / 4A group ≧ 4 group 4A transition metal
0.8 For group 5A transition metals, Ta / 5A group ≧ 0.
W / 6A group ≧ 0.9 for group 3,6A transition metals, and the molar ratio between non-metals is C: N = 0.4-0.9: 0.1
The cermet for a rotary tool according to claim 2, wherein the cermet is ~ 0.6.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28410391A JP3217404B2 (en) | 1991-10-04 | 1991-10-04 | Cermet for rotary tools |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28410391A JP3217404B2 (en) | 1991-10-04 | 1991-10-04 | Cermet for rotary tools |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0598382A JPH0598382A (en) | 1993-04-20 |
| JP3217404B2 true JP3217404B2 (en) | 2001-10-09 |
Family
ID=17674244
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP28410391A Expired - Fee Related JP3217404B2 (en) | 1991-10-04 | 1991-10-04 | Cermet for rotary tools |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3217404B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR0140409B1 (en) * | 1994-09-29 | 1998-06-01 | 김은영 | Process for preparing sintered titanium nitride |
| US8202344B2 (en) | 2007-05-21 | 2012-06-19 | Kennametal Inc. | Cemented carbide with ultra-low thermal conductivity |
| CN102574223B (en) | 2009-11-26 | 2014-01-29 | 京瓷株式会社 | Rotation tool |
| CN101912888B (en) * | 2010-07-15 | 2012-08-22 | 江阴东大新材料研究院 | Manufacturing method of die core of wire-drawing die |
-
1991
- 1991-10-04 JP JP28410391A patent/JP3217404B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0598382A (en) | 1993-04-20 |
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