JPH07150286A - Ticn-based cermet - Google Patents
Ticn-based cermetInfo
- Publication number
- JPH07150286A JPH07150286A JP6242630A JP24263094A JPH07150286A JP H07150286 A JPH07150286 A JP H07150286A JP 6242630 A JP6242630 A JP 6242630A JP 24263094 A JP24263094 A JP 24263094A JP H07150286 A JPH07150286 A JP H07150286A
- Authority
- JP
- Japan
- Prior art keywords
- hardness
- cermet
- ticn
- sintering
- toughness
- 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.)
- Pending
Links
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は靱性、信頼性に優れた
サーメット切削工具用のサーメットに関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cermet for a cermet cutting tool having excellent toughness and reliability.
【０００２】[0002]
【従来の技術】チタンとタンタル、ニオブ、モリブデ
ン、タンク゛ステンなどの複炭窒化物を鉄、ニッケル、
コバルト、クロム、モリブデン、タンク゛ステンからな
る群より選んだ１種以上の金属で結合した硬質合金を焼
結したいわゆるサーメットよりなる切削工具は超硬合金
製切削工具に比べて鉄との融着性にすぐれていることか
ら、仕上り切削、さらにはフライス加工などに広く実用
化されている。特に型押し、焼結しただけで研削加工を
しない焼結肌チップは、従来の焼結後ダイヤモンド砥石
にて研削加工した研削肌チップに比べ、精度上は何ら遜
色がないことに加え、安価であることから最近特にその
使用量が増大しつつある。サーメットの焼結方法として
は、従来から種々の技術が提案されており、特に焼結中
に脱窒現象が生じないよう、窒素雰囲気中で焼結すると
いうことは、当業者において周知の技術である。2. Description of the Related Art Double carbonitrides such as titanium and tantalum, niobium, molybdenum, and tank dust are mixed with iron, nickel,
A cutting tool made of so-called cermet, which is made by sintering a hard alloy bonded with one or more metals selected from the group consisting of cobalt, chromium, molybdenum, and tank dust, has a better fusion property with iron than a cemented carbide cutting tool. Since it is excellent, it has been widely put to practical use for finishing cutting and milling. In particular, the sintered skin chips that are only stamped and sintered but not ground are comparable to conventional ground skin chips that have been ground with a diamond grindstone after sintering, and at a low cost. Therefore, the amount of its use has been increasing especially recently. As a cermet sintering method, various techniques have been conventionally proposed, and it is known in the art that sintering is performed in a nitrogen atmosphere so that a denitrification phenomenon does not occur during sintering. is there.
【０００３】[0003]
【発明が解決しようとする課題】従来の窒素雰囲気下で
の焼結法をサーメットに実施すると、たしかに脱窒現象
は防止できるものの、焼結後得られたサーメットの表面
部が内部に比べてビッカース硬度で、１００〜４００程
度硬化するという現象が生じる。サーメットにおいて、
硬さと靱性とは相反するため、表面部が硬いと靱性が低
下する。特にサーメットのように仕上げ加工でよく使用
される工具では、使用時の切込みが０．５ｍｍ以下と通
常の２〜５ｍｍの切込みに比べて著しく小さいため、殆
んど表面の硬化部のみで切削していることになり、確か
に耐摩耗性はすぐれるものの、靱性に欠けるため使用中
欠損に至ることが多々あり、サーメット工具の信頼性を
損ねていた。When the cermet is subjected to the conventional sintering method under a nitrogen atmosphere, the denitrification phenomenon can be prevented, but the surface portion of the cermet obtained after sintering is more Vickers than the inside. In terms of hardness, a phenomenon of hardening about 100 to 400 occurs. In cermet,
Since hardness and toughness are contradictory, if the surface is hard, the toughness will decrease. Especially for tools often used for finishing such as cermet, the depth of cut when used is 0.5 mm or less, which is significantly smaller than the normal depth of cut of 2 to 5 mm, so most of the cutting is done only at the hardened part of the surface. Therefore, although it has excellent wear resistance, it often lacks in toughness and may be damaged during use, impairing the reliability of the cermet tool.
【０００４】[0004]
【課題を解決するための手段】この発明は上記した従来
技術によるサーメットの表面硬化層の欠陥を解消するべ
く検討の結果得られたものである。即ち、この発明はサ
ーメットを従来技術によって窒素雰囲気中１３５０〜１
５５０℃で焼結したのち、焼結温度より１２００℃まで
を５０℃／分以上、好ましくは１００℃／分以上の冷却
速度で冷却することによって内部と表面部の硬度がほぼ
等しいサーメット工具を提供するものである。この発明
によるサーメットの内部から表面にかけての硬度分布
は、その一例が第１図に示されているように、表面部の
硬度が深さ０．３ｍｍより内部の硬度に対し、好ましく
はビッカース硬度で±７％以内にあることを特徴として
いる。The present invention was obtained as a result of investigations for eliminating the defects in the surface-hardened layer of the cermet according to the above-mentioned prior art. That is, according to the present invention, the cermet is formed in a nitrogen atmosphere at 1350-1
After sintering at 550 ° C., the cermet tool having substantially the same hardness as the inside is provided by cooling from the sintering temperature to 1200 ° C. at a cooling rate of 50 ° C./min or more, preferably 100 ° C./min or more. To do. The hardness distribution from the inside to the surface of the cermet according to the present invention, as an example thereof is shown in FIG. 1, is such that the hardness of the surface portion is more than Vickers hardness with respect to the hardness of the inside from a depth of 0.3 mm. It is characterized by being within ± 7%.
【０００５】[0005]
【作用】この発明において上記の硬度分布を実現し、そ
の焼結法において上記の冷却速度を実施するためには種
々の方法が考えられるが、なかでも工業的には熱伝導率
の高い気体によってガス冷却する方法が最も好ましい。
熱伝導率の高い気体とは、例えば水素、ヘリウム、一酸
化炭素などである。サーメットの表面硬化層がなぜ生じ
るかについては種々異論のあるところであるが、チタン
とタンタル、ニオブ、モリブデン、タンク゛ステンなど
の複炭窒化物を鉄、ニッケル、コバルト、クロム、モリ
ブデン、タンク゛ステンなどの金属で結合した焼結硬質
合金であるサーメットが、焼結温度において生じる液相
から冷却中に硬質分散相が生じる際に、焼結体と焼結雰
囲気とが非平衡な状態となり、その結果、焼結体内に組
成の不均一が生じるため、と考えられる。そのため、こ
の焼結体に生じた液相から硬質分散相が冷却中に生じる
際に、組成の不均一が生じない、もしくはたとえ生じて
も無視しうる程度に抑えるためには、焼結温度から該サ
ーメットの液相出現温度までを十分なる速度で急速冷却
してやればよい。Various methods are conceivable in order to realize the above hardness distribution in the present invention and to carry out the above cooling rate in the sintering method. Among them, industrially, a gas having a high thermal conductivity is used. The method of gas cooling is most preferred.
The gas having high thermal conductivity is, for example, hydrogen, helium, carbon monoxide or the like. Although there are various disagreements as to why the cermet surface-hardened layer is formed, double carbonitrides such as titanium and tantalum, niobium, molybdenum, and tank dsten are replaced with metals such as iron, nickel, cobalt, chromium, molybdenum, and tank dsten. Cermet, which is a bonded sintered hard alloy, has a non-equilibrium state between the sintered body and the sintering atmosphere when a hard dispersed phase is generated during cooling from the liquid phase generated at the sintering temperature, resulting in sintering. It is considered that this is because the composition is nonuniform in the body. Therefore, when a hard dispersed phase is generated during cooling from the liquid phase generated in this sintered body, compositional non-uniformity does not occur, or even if it occurs, in order to suppress it to a negligible level, from the sintering temperature The liquid phase appearance temperature of the cermet may be rapidly cooled at a sufficient rate.
【０００６】具体的には焼結温度より１２００℃までを
急速冷却してやればよい。この際、１２００℃以下まで
急速冷却しても効果に変わりはなく、１２００℃以上で
急速冷却を中止すると、表面硬質層が完全になくならな
いため好ましくない。急速冷却としては、５０℃／分以
上、好ましくは１００℃／分以上が必要である。また急
冷する方法としては、種々考えられるが、工業的にはさ
きに記したように、水素、ヘリウム、一酸化炭素など熱
伝導率の高いガスを用いるガス冷却が適当である。具体
的には３００°Ｋにおける熱伝導率が２．５×１０-4Ｗ
／ｃｍ・ｄｅｇ以上のものであれば、ほぼ冷却速度が７
０℃／分以上になることがわかった。Specifically, the temperature may be rapidly cooled from the sintering temperature to 1200 ° C. At this time, the effect does not change even if it is rapidly cooled to 1200 ° C or lower, and if the rapid cooling is stopped at 1200 ° C or higher, the hard surface layer is not completely lost, which is not preferable. Rapid cooling requires 50 ° C./min or more, preferably 100 ° C./min or more. There are various conceivable methods for rapid cooling, but as described industrially, gas cooling using a gas having a high thermal conductivity such as hydrogen, helium, carbon monoxide is suitable. Specifically, the thermal conductivity at 300 ° K is 2.5 × 10 -4 W
If it is more than / cm · deg, the cooling rate is almost 7
It was found to be 0 ° C / min or more.
【０００７】[0007]
【実施例】市販のＴｉ（ＣＮ）、ＴａＣ、Ｍｏ2Ｃ、Ｎ
ｉ、Ｃｏ粉末を混合し、プレス成型したのち、真空焼結
炉にて１２００℃までを１×１０-2Ｔｏｒｒの真空で,
１２００℃以上、１４００℃までを４０Ｔｏｒｒの窒素
雰囲気中で昇温し、１４００℃で２０Ｔｏｒｒの窒素雰
囲気中で１時間焼結した。［得られた合金の組成はモル
比で（Ｔｉ0.85Ｔａ0.05Ｍｏ0.05Ｗ0.05）（Ｃ0.88Ｎ
0.12）−８重量％Ｃｏ−４重量％Ｎｉである。］然るの
ち、焼結炉を排気してから水素ガスを１気圧導入（水素
ガスは熱交換機を用いて焼結炉内を循環している）して
ガス冷却を行った。１４００℃から１２００℃まで冷却
するのに１．５分間かかった。EXAMPLES Commercially available Ti (CN), TaC, Mo 2 C, N
After mixing i and Co powders and press-molding, a vacuum sintering furnace up to 1200 ° C. under a vacuum of 1 × 10 -2 Torr,
The temperature was raised from 1200 ° C. to 1400 ° C. in a nitrogen atmosphere of 40 Torr and sintered at 1400 ° C. in a nitrogen atmosphere of 20 Torr for 1 hour. [The composition of the obtained alloy is (Ti 0.85 Ta 0.05 Mo 0.05 W 0.05 ) (C 0.88 N in molar ratio.
0.12 ) -8 wt% Co-4 wt% Ni. Then, after exhausting the sintering furnace, hydrogen gas was introduced at 1 atm (hydrogen gas is circulated in the sintering furnace using a heat exchanger) to cool the gas. It took 1.5 minutes to cool from 1400 ° C to 1200 ° C.
【０００８】かくして得られたチップをＡとし、従来通
り焼結完了後炉内を真空に保ち、炉冷したチップ（１４
００℃から１２００℃まで冷却するのに１５分かかっ
た）をＢとした。これらチップＡおよびＢを切断し、表
面から内部までの硬さを測定したところ、第１図に示す
結果が得られた。また、このチップＡおよびＢについて
下記の切削条件で切削テストを行った。 切削条件 被削材 Ｓ４５Ｃ（ＨB＝２２０） ５０ｍｍ×１００ｍｍ角 切削速度 １５０ｍ／ｍｉｎ 送り ０．０５ｍｍ／ｒｅｖ 切り込み ０．２ｍｍ カッター ＦＰＧ ４１００Ｒ チップ形状 ＳＤＫＮ ４２ＭＴ 上記条件にて１０分間切削し、Ａが最大フランク摩耗
０．０４ｍｍであったのに対し、Ｂはチッピングが生
じ、最大フランク摩耗は０．３１ｍｍであった。The chip thus obtained was designated as A, and after the sintering was completed, the inside of the furnace was kept vacuum and the furnace cooled chip (14
It took 15 minutes to cool from 00 ° C to 1200 ° C) was designated as B. When these chips A and B were cut and the hardness from the surface to the inside was measured, the results shown in FIG. 1 were obtained. Further, a cutting test was performed on the chips A and B under the following cutting conditions. Cutting conditions Work material S45C (H B = 220) 50mm × 100mm square Cutting speed 150m / min Feed 0.05mm / rev Depth of cut 0.2mm Cutter FPG 4100R Tip shape SDKN 42MT Cutting for 10 minutes under the above conditions, A is the maximum The flank wear was 0.04 mm, while B chipped and the maximum flank wear was 0.31 mm.
【０００９】[0009]
【発明の効果】以上説明したように、この発明によれば
欠損の少ない、靱性に富む高信頼性のサーメット切削工
具が得られることが認められた。As described above, according to the present invention, it has been recognized that a highly reliable cermet cutting tool with few defects and high toughness can be obtained.
【図１】この発明になるサーメットＡと従来技術による
サーメットＢの表面より内部への硬度分布を示す線図で
ある。FIG. 1 is a diagram showing hardness distribution from the surface to the inside of cermet A according to the present invention and cermet B according to a conventional technique.
Ａ：本願発明に係るサーメット Ｂ：従来技術によるサーメット A: Cermet according to the present invention B: Cermet according to conventional technology
Claims (1)
ン、タンク゛ステンなどの複炭窒化物を鉄、ニッケル、
コバルト、クロム、モリブデン、タンク゛ステンからな
る群より選んだ１種以上の金属で結合したＴｉＣＮ基サ
ーメットにおいて、内部から表面部に向けて、硬度が内
部とほぼ等しいままであることを特徴とするＴｉＣＮ基
サーメット。1. Titanium and double carbonitrides such as tantalum, niobium, molybdenum, and tank dust are mixed with iron, nickel,
In a TiCN-based cermet bonded with one or more metals selected from the group consisting of cobalt, chromium, molybdenum and tank dust, the hardness of the TiCN-based cermet from the inside to the surface remains almost the same as the inside. cermet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6242630A JPH07150286A (en) | 1994-10-06 | 1994-10-06 | Ticn-based cermet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6242630A JPH07150286A (en) | 1994-10-06 | 1994-10-06 | Ticn-based cermet |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61200519A Division JPH0791604B2 (en) | 1986-08-27 | 1986-08-27 | Sintering method of TiCN-based cermet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07150286A true JPH07150286A (en) | 1995-06-13 |
Family
ID=17091916
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6242630A Pending JPH07150286A (en) | 1994-10-06 | 1994-10-06 | Ticn-based cermet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07150286A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103589929A (en) * | 2013-10-17 | 2014-02-19 | 株洲钻石切削刀具股份有限公司 | Metal ceramic alloy preparation method and product thereof |
| RU2509170C1 (en) * | 2012-10-22 | 2014-03-10 | Российская Федерация, от имени которой выступает Министерство промышленности и торговли Российской Федерации (Минпромторг России) | Wearproof alloy for high-loaded friction assemblies |
| CN104878267A (en) * | 2015-05-29 | 2015-09-02 | 南京理工大学 | TiCN-base metal ceramic tool material and its microwave sintering process |
| CN108441664A (en) * | 2018-05-22 | 2018-08-24 | 湘潭大学 | Superhigh intensity can coating TiCN bases bond hard alloy containing cobalt steels and preparation method |
| CN111411248A (en) * | 2020-03-24 | 2020-07-14 | 广州铁路职业技术学院（广州铁路机械学校） | Multi-scale structure alloy material, preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5757866A (en) * | 1980-09-24 | 1982-04-07 | Toshiba Tungaloy Co Ltd | Hard alloy having nitride layer |
| JPS5914534A (en) * | 1982-07-14 | 1984-01-25 | Nissan Motor Co Ltd | Floor trim of vehicle |
| JPS6034618A (en) * | 1979-01-12 | 1985-02-22 | アクゾ・エヌ・ヴエー | Silicate fiber, production thereof and friction lining containing said fiber |
-
1994
- 1994-10-06 JP JP6242630A patent/JPH07150286A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6034618A (en) * | 1979-01-12 | 1985-02-22 | アクゾ・エヌ・ヴエー | Silicate fiber, production thereof and friction lining containing said fiber |
| JPS5757866A (en) * | 1980-09-24 | 1982-04-07 | Toshiba Tungaloy Co Ltd | Hard alloy having nitride layer |
| JPS5914534A (en) * | 1982-07-14 | 1984-01-25 | Nissan Motor Co Ltd | Floor trim of vehicle |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU2509170C1 (en) * | 2012-10-22 | 2014-03-10 | Российская Федерация, от имени которой выступает Министерство промышленности и торговли Российской Федерации (Минпромторг России) | Wearproof alloy for high-loaded friction assemblies |
| CN103589929A (en) * | 2013-10-17 | 2014-02-19 | 株洲钻石切削刀具股份有限公司 | Metal ceramic alloy preparation method and product thereof |
| CN103589929B (en) * | 2013-10-17 | 2015-10-07 | 株洲钻石切削刀具股份有限公司 | Cermet preparation method and products thereof |
| CN104878267A (en) * | 2015-05-29 | 2015-09-02 | 南京理工大学 | TiCN-base metal ceramic tool material and its microwave sintering process |
| CN108441664A (en) * | 2018-05-22 | 2018-08-24 | 湘潭大学 | Superhigh intensity can coating TiCN bases bond hard alloy containing cobalt steels and preparation method |
| CN108441664B (en) * | 2018-05-22 | 2020-06-30 | 湘潭大学 | Ultrahigh-strength coatable TiCN-based cobalt-containing steel bonded hard alloy and preparation method thereof |
| CN111411248A (en) * | 2020-03-24 | 2020-07-14 | 广州铁路职业技术学院（广州铁路机械学校） | Multi-scale structure alloy material, preparation method and application thereof |
| CN111411248B (en) * | 2020-03-24 | 2021-07-27 | 广州铁路职业技术学院（广州铁路机械学校） | Multi-scale structure alloy material, preparation method and application thereof |
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