JP2775298B2 - Cermet tool - Google Patents
Cermet toolInfo
- Publication number
- JP2775298B2 JP2775298B2 JP1166225A JP16622589A JP2775298B2 JP 2775298 B2 JP2775298 B2 JP 2775298B2 JP 1166225 A JP1166225 A JP 1166225A JP 16622589 A JP16622589 A JP 16622589A JP 2775298 B2 JP2775298 B2 JP 2775298B2
- Authority
- JP
- Japan
- Prior art keywords
- hardness
- weight
- cermet
- rake face
- sintered body
- 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 - Lifetime
Links
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- Cutting Tools, Boring Holders, And Turrets (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は耐摩耗性および耐欠損性に優れたサーメット
工具に関する。Description: TECHNICAL FIELD The present invention relates to a cermet tool excellent in wear resistance and fracture resistance.
従来から、切削用焼結体としてはWC−Coを主成分とす
る超硬合金が主として用いられていたが、最近ではTiの
炭化物、窒化物、炭窒化物を主成分とするサーメット焼
結体が用いられている。Conventionally, cemented carbide mainly composed of WC-Co has been mainly used as a sintered body for cutting, but recently, a cermet sintered body mainly composed of carbides, nitrides and carbonitrides of Ti. Is used.
このようなサーメット系焼結体としては、TiCを主成
分とし、鉄族金属を結合相とし、さらに周期律表第IV
a,V a,VI a族金属の炭化物、窒化物、炭窒化物を硬質成
分として加えたTiC基サーメットが主流であった。しか
し乍らこのようなTiC基サーメット焼結体では耐熱性、
強靭性に劣ることから、上記組成にさらにTiN等の窒化
物、炭窒化物を含有させることが提案された。これは、
TiN自体が靭性に富むことにより、焼結体に靭性を付与
するとともに、熱伝導率が高いことにより、耐熱衝撃
性、耐熱塑性変形性を向上させようとするものである。Such a cermet-based sintered body includes TiC as a main component, an iron group metal as a binder phase, and
The mainstream was TiC-based cermets containing carbides, nitrides, and carbonitrides of a, Va, and VIa group metals as hard components. However, such a TiC-based cermet sintered body has heat resistance,
Due to poor toughness, it has been proposed to further include a nitride such as TiN or a carbonitride in the above composition. this is,
The high toughness of TiN itself imparts toughness to the sintered body, and the high thermal conductivity improves thermal shock resistance and thermal plastic deformation.
このようなサーメット焼結体を工具用として用いる場
合には、高い耐摩耗性および耐欠損性が要求され、各種
の改良がなされている。When such a cermet sintered body is used for a tool, high wear resistance and chipping resistance are required, and various improvements have been made.
例えば特公昭59−14534号では液相出現温度以下で窒
素を炉内に導入し、焼結体表面に靭性に富む軟化層を形
成させることが、また特公昭59−17176号ではCO還元雰
囲気で焼成することにより、特定の硬度を有する硬質層
を形成させることが、さらに特公昭60−34618号によれ
ば焼成後の降温時にCO雰囲気と成すことにより表面内部
とも均一な機械特性を有するサーメットを得ることが提
案されている。For example, in Japanese Patent Publication No. 59-14534, nitrogen is introduced into a furnace at a temperature lower than the liquid phase appearance temperature to form a softened layer rich in toughness on the surface of a sintered body. According to Japanese Patent Publication No. 60-34618, it is possible to form a hard layer having a specific hardness by firing, and to form a cermet having uniform mechanical properties inside the surface by forming a CO atmosphere at the time of cooling after firing. It is proposed to get.
しかし乍ら、高速切削加工時の耐摩耗性の知見からは
特公昭59−14534号及び特公昭60−34618号の記載の切削
工具では表面硬度が低いために、性能上不十分である。
一方、特公昭59−17176号には表面に硬質層を形成させ
る方法が開示されているもののその表面硬度はせいぜい
ビッカース硬度（Hv）で2000Kg/mm2までしか達成されて
いない。However, from the knowledge of the wear resistance during high-speed cutting, the cutting tools described in JP-B-59-14534 and JP-B-60-34618 are insufficient in performance due to low surface hardness.
On the other hand, Japanese Patent Publication No. 59-17176 discloses a method for forming a hard layer on the surface, but the surface hardness is at most 2000 Vg / mm 2 in Vickers hardness (Hv).
そこで、本発明者等は、特願昭63−243623号におい
て、表面のビッカース硬度2000以上の耐摩耗性に優れた
サーメット焼結体を提案したが、このように硬度を高め
て耐摩耗性を向上させると、靭性が低下し、耐欠損性が
劣るため、このようなサーメットはその用途も一部に限
られてしまうという問題があった。Accordingly, the present inventors have proposed a cermet sintered body excellent in wear resistance with a Vickers hardness of 2,000 or more on the surface in Japanese Patent Application No. 63-243623. If the cermet is improved, the toughness is reduced, and the fracture resistance is inferior. Therefore, there has been a problem that the use of such a cermet is limited to a part.
本発明者等は、通常、逃げ面とすくい面から構成され
る切削工具において、摩耗は主に逃げ面に発生し、欠損
はすくい面より発生し易いこと、また一般的に硬度が高
いものは耐摩耗性に優れ、硬度が低くなると靭性が向上
することに着目し、切削工具の逃げ面の硬度を高く、ま
たすくい面の硬度を低く設定することにより、工具とし
ての耐摩耗性および耐欠損性を向上させ、工具の長寿命
化が達成できることを知見した。The present inventors have found that, in a cutting tool that is usually composed of a flank and a rake face, wear mainly occurs on the flank, chipping is more likely to occur from the rake face, and those having a high hardness are generally Focusing on excellent wear resistance and improving toughness as hardness decreases, setting the hardness of the flank face of the cutting tool to high and the hardness of the rake face low allows for wear resistance and chipping resistance as a tool. It has been found that the operability can be improved and the tool life can be extended.
即ち、本発明のサーメット工具は、Tiを炭化物、窒化
物あるいは炭窒化物として50乃至80重量％、周期律表第
VI a族金属を炭化物として10乃至40重量％の割合で含有
するとともに、窒素／（炭素＋窒素）で表される原子比
が0.4乃至0.6の範囲にある硬質相成分70乃至95重量％
と、鉄族金属を主成分とする結合相成分５乃至30重量％
とから成り、内部よりも高硬度の表面部が形成されたサ
ーメットのすくい面を研磨除去して前記逃げ面の硬度を
内部の硬度および前記すくい面の硬度よりも高くしたこ
とを特徴とするものである。That is, the cermet tool of the present invention is characterized in that Ti is a carbide, nitride or carbonitride in an amount of 50 to 80% by weight,
70-95% by weight of a hard phase component containing a VIa group metal as a carbide in a ratio of 10-40% by weight and having an atomic ratio of nitrogen / (carbon + nitrogen) in a range of 0.4-0.6.
And 5 to 30% by weight of a binder phase component mainly composed of an iron group metal
Wherein the rake face of the cermet on which a surface part having a higher hardness than the inside is formed is polished and removed so that the hardness of the flank is higher than the hardness of the inside and the hardness of the rake face. It is.
以下、本発明を詳述する。 Hereinafter, the present invention will be described in detail.
本発明のサーメットは、硬質相を形成する成分とし
て、Tiを炭化物、窒化物あるいは炭窒化物として50乃至
80重量％、特に55乃至65重量％と、Ｗ、Mo等の周期律表
VI a族金属を炭化物として10乃至40重量％、特に15乃至
30重量％の割合でそれぞれ含有するもので、硬質相は、
これらは相互に固溶して炭窒化物を形成している。The cermet of the present invention is characterized in that Ti is a carbide, nitride or carbonitride of 50 to 50 as a component forming a hard phase.
80% by weight, especially 55 to 65% by weight, periodic table of W, Mo, etc.
VI Group a metal is 10 to 40% by weight as a carbide, especially 15 to 40% by weight.
30% by weight, each containing the hard phase,
These form a solid solution with each other to form a carbonitride.
このような硬質相成分において、Tiの量が50重量％を
下回ると耐摩耗性が低下し、80重量％を超えると焼結性
が低下し、好ましくない。また、第VI a族金属は粒成長
抑制、結合相とのぬれ性を向上させる効果を有するが、
10重量％を下回ると上記効果が得られず、硬質相が粗大
化し、硬度、強度が低下する。また、40重量％を超える
とη相等の不健全相が生じると共に焼結が困難となる。In such a hard phase component, if the amount of Ti is less than 50% by weight, the wear resistance decreases, and if it exceeds 80% by weight, the sinterability decreases, which is not preferable. Group VIa metal has the effect of suppressing grain growth and improving the wettability with the binder phase.
If the content is less than 10% by weight, the above effect cannot be obtained, the hard phase becomes coarse, and the hardness and strength are reduced. On the other hand, if it exceeds 40% by weight, an unhealthy phase such as an η phase is generated and sintering becomes difficult.
また、硬質相成分としては上記の他、耐クレータ摩耗
性向上を目的としてTa,Nbを、さらに耐塑性変形性向上
を目的としてZr,V,Hf等を窒化物、炭化物、炭窒化物換
算で５乃至40重量％の割合で含むことも可能であるが、
40重量％を超えると耐摩耗性劣化、ポア、ボイドの発生
が著しく増加する傾向にあり好ましくない。As the hard phase component, in addition to the above, Ta, Nb for the purpose of improving crater wear resistance, and Zr, V, Hf, etc. for the purpose of improving plastic deformation resistance, are converted into nitride, carbide, carbonitride. It is possible to contain 5 to 40% by weight,
If it exceeds 40% by weight, deterioration of wear resistance, generation of pores and voids tends to increase remarkably, which is not preferable.
一方、結合相はFe,Co,Ni等の鉄族金属を主体として成
るもので、一部、硬質相形成成分が含まれる場合もあ
る。On the other hand, the binder phase is mainly composed of an iron group metal such as Fe, Co, and Ni, and may partially include a hard phase forming component.
焼結体全体として硬質相成分は70乃至95重量％、結合
相成分は５〜30重量％の割合から成る。The hard phase component comprises 70 to 95% by weight and the binder phase component comprises 5 to 30% by weight in the whole sintered body.
本発明における組成上の特徴は、硬質相成分中におい
て（窒素／炭素＋窒素）で表される原子比が0.4乃至0.
6、特に0.4〜0.5の範囲に設定される点にある。即ち、
この原子比が0.4を下回るは靭性、耐摩耗性の向上が望
めず、本発明の目的が達成されず、0.6を超えると焼結
体中にポア、ボイドが発生し、工具としての信頼性が低
下する。The feature of the composition in the present invention is that the atomic ratio represented by (nitrogen / carbon + nitrogen) in the hard phase component is 0.4 to 0.4.
6, especially in the range of 0.4 to 0.5. That is,
If the atomic ratio is less than 0.4, improvement in toughness and wear resistance cannot be expected, and the object of the present invention is not achieved.If the atomic ratio exceeds 0.6, pores and voids are generated in the sintered body, and the reliability as a tool is reduced. descend.
このような組成のサーメットを用いて、逃げ面、すく
い面の硬度の異なる工具を製造するための１つの例を説
明する。まず、TiC、TiNあるいはTiCNの原料粉末を50乃
至80重量％と、WC、Mo2C、MoC等の周期律表第VI a族金
属の炭化物を10乃至40重量％とを、（窒素／炭素＋窒
素）で表される原子比が0.4乃至0.6の範囲となるように
調製した硬質相成分を70乃至95重量％と、鉄族金属を５
乃至30重量％の割合で配合した成形体を作製する。One example for manufacturing tools having different flank and rake hardnesses using a cermet having such a composition will be described. First, 50 to 80% by weight of a raw material powder of TiC, TiN or TiCN, and 10 to 40% by weight of a carbide of a Group VIa metal of the periodic table such as WC, Mo 2 C, MoC (nitrogen / carbon + Nitrogen) in an amount of 70 to 95% by weight of a hard phase component prepared so that the atomic ratio represented by
A molded article blended at a ratio of about 30% by weight is produced.
この時、硬質相成分は、Tiと周期律表第VI a族金属を
含む複合炭化物、複合炭窒化物等として配合することも
できる。なお、Ti系原料としてはTiCを用いると焼結性
が低下し、部分的粒成長を起こす場合があるため、Ti
（CN）あるいはTi（CN）とTiNとの組み合わせがより好
ましい。At this time, the hard phase component may be compounded as a composite carbide, a composite carbonitride, or the like containing Ti and a metal of Group VIa of the periodic table. When TiC is used as a Ti-based material, sinterability is reduced, and partial grain growth may occur.
(CN) or a combination of Ti (CN) and TiN is more preferred.
得られた成形体は真空炉内に設置され，焼成に移され
る。The obtained compact is placed in a vacuum furnace and transferred to firing.
焼成は、1400〜1700℃の焼成温度で行われるが本発明
によれば、焼成は、まず0.5Torr以下の真空炉内で加熱
し、所定の時間に70Torr以上、特に100〜200Torrの圧力
の窒素ガスを導入する。The firing is performed at a firing temperature of 1400 to 1700 ° C. According to the present invention, the firing is first performed by heating in a vacuum furnace of 0.5 Torr or less, and nitrogen at a pressure of 70 Torr or more, particularly 100 to 200 Torr for a predetermined time. Introduce gas.
この窒素ガスの導入は、昇温過程において、鉄族金属
の液相出現温度以上で、特に耐理論密度比が初期の成形
体より５％程度以上緻密化した段階で導入する。即ち、
液相出現温度以上で成形体の表面には液相により被膜が
形成される。この被膜形成後に窒素ガスを導入すること
により、窒化物の分解を抑制するとともに結合相と硬質
相粒子の濡れ性低下を防止し、結果的に焼結体中にポ
ア、ボイドが残留するのを防止することができる。This nitrogen gas is introduced at a temperature higher than the liquid phase appearance temperature of the iron group metal in the temperature raising process, particularly at a stage where the theoretical density ratio is about 5% or more higher than the initial compact. That is,
Above the liquid phase appearance temperature, a film is formed on the surface of the molded body by the liquid phase. By introducing nitrogen gas after the formation of the film, the decomposition of nitrides is suppressed and the wettability of the binder phase and the hard phase particles is prevented, and as a result, pores and voids remain in the sintered body. Can be prevented.
しかし、窒素ガスの導入の時期が焼結最高温度到達
後、特に対理論密度比90％を超えた付近では、実質上、
窒化物の分解抑制効果は得られず、焼結体表面に荒れが
生じる。However, when the time of introduction of nitrogen gas reaches the maximum sintering temperature, especially around the point where the theoretical density ratio exceeds 90%, substantially,
The effect of suppressing the decomposition of nitride cannot be obtained, and the surface of the sintered body becomes rough.
窒素ガスは炉内の温度が最高焼結温度に達した後は、
所定時間保持後、ただちに真空に戻して焼成を続ける。After the temperature in the furnace reaches the maximum sintering temperature,
After holding for a predetermined time, the pressure is immediately returned to the vacuum, and the firing is continued.
これは、最高焼結温度到達後にさらに圧力を上げる
と、焼結体表面部で粗粒で金属をほとんど含有しない、
脆い窒化層が生成され、焼肌面の荒れを生じるととも
に、表面部の靭性を著しく低下させてしまう。This means that if the pressure is further increased after reaching the maximum sintering temperature, the surface of the sintered body contains coarse metal and almost no metal,
A brittle nitride layer is generated, causing roughening of the burnt surface and significantly reducing the toughness of the surface.
このように、焼成中の特定の時期に窒素ガスを導入す
ることによって焼結体の表面部には第１図に示すように
硬度勾配を有する非常に高硬度な層が形成される。これ
は、窒素ガス導入後、成形体内部と炉内雰囲気との間に
圧力が生じている。そこへ、急激に真空に戻すと成形体
表面付近の結合金属が内部に移動し、表面部付近は内部
に対し、結合相量が減少することにより、硬度が高くな
ると考えられる。Thus, by introducing nitrogen gas at a specific time during firing, a very high hardness layer having a hardness gradient is formed on the surface of the sintered body as shown in FIG. This is because a pressure is generated between the inside of the compact and the atmosphere in the furnace after the introduction of the nitrogen gas. It is considered that when the pressure is rapidly returned to vacuum, the bonding metal near the surface of the molded body moves into the inside, and the hardness increases near the surface due to a decrease in the amount of the bonding phase relative to the inside.
この表面部の硬度は焼成時に導入する窒素ガスの圧力
に大きく依存し、たとえば、ビッカース硬度2000以上の
硬度を得るためには、窒素ガス圧力をおよそ70Torr以上
に設定すればよい。The hardness of the surface portion largely depends on the pressure of the nitrogen gas introduced at the time of firing. For example, in order to obtain a Vickers hardness of 2000 or more, the nitrogen gas pressure may be set to about 70 Torr or more.
本発明における上記のサーメットは窒素を多量に含む
ことによって、高靭性、高硬度および耐熱性が優れるも
ので、特にその表面部は高い硬度を有することから耐摩
耗性に非常に優れるという性質を有する反面、靭性は若
干内部より劣る。一方、内部の硬度は表面部より劣る
が、靭性が高いという性質を有する。The cermet in the present invention contains a large amount of nitrogen, has high toughness, high hardness and excellent heat resistance, and particularly has a property that the surface portion thereof has very high wear resistance because of its high hardness. On the other hand, the toughness is slightly inferior to the inside. On the other hand, although the internal hardness is lower than that of the surface portion, it has a property of high toughness.
そこで本発明によれば、第２図のサーメット焼結体の
断面図において表面部に高硬度な層１を有するサーメッ
ト工具のすくい面Ａを例えば破線Ｘまで研磨して、表面
部の高硬度な層を除去することにより、すくい面の硬度
を低くし、靭性の高い内部２を表面に露出させる。これ
により、すくい面Ａと逃げ面Ｂには硬度差及び靭性差が
生じる。この研磨工程では、第１図に示したようにサー
メットの表面部から内部に硬度勾配が形成されているこ
とから、研磨量を調整量を調整することによって、すく
い面の硬度を適宜設定することができる。Therefore, according to the present invention, the rake face A of the cermet tool having the hard layer 1 on the surface in the sectional view of the cermet sintered body of FIG. The removal of the layer lowers the hardness of the rake face and exposes the tough interior 2 to the surface. Thereby, a difference in hardness and a difference in toughness occur between the rake face A and the flank B. In this polishing step, since the hardness gradient is formed from the surface of the cermet to the inside as shown in FIG. 1, the hardness of the rake face should be appropriately set by adjusting the polishing amount. Can be.
また、逃げ面の硬度は、逃げ面自体が、工具の摩耗特
性に大きく寄与することから、ビッカース硬度2000以上
であることが望ましく、一方すくい面は工具の欠損性に
大きく寄与することから、高靭性であることが望まれる
が、すくい面も適度の耐摩耗性が要求されることから、
ビッカース硬度1500以上であることが望ましく、特に逃
げ面とすくい面の硬度差が200以上であることが好まし
い。Further, the hardness of the flank is desirably at least Vickers hardness 2,000 because the flank itself greatly contributes to the wear characteristics of the tool, while the rake face greatly contributes to the chipping property of the tool. It is desired to be tough, but since the rake face is also required to have appropriate wear resistance,
The Vickers hardness is desirably 1500 or more, and the hardness difference between the flank and the rake face is particularly desirably 200 or more.
以下、本発明を次の例で説明する。 Hereinafter, the present invention will be described with reference to the following examples.
〔実施例１〕 原料粉末として平均粒径１〜1.5μｍの粉末を用い
て、下記第１表の組成に調合した。[Example 1] A powder having an average particle diameter of 1 to 1.5 µm was used as a raw material powder, and was prepared to have the composition shown in Table 1 below.
これら２種の調合品をそれぞれ振動ミルで粉砕を行
い、バインダーを添加したものをTNMA332チップ形状に
ブレス成形し、300℃で脱バインダー後、焼成した。 Each of these two types of preparations was pulverized by a vibration mill, and a mixture to which a binder had been added was formed into a TNMA332 chip shape by pressing, and the binder was removed at 300 ° C. and then fired.
焼成は真空炉内で昇温し、液相出現後、1350℃で窒素
ガスを組成１には100Torr、組成２では150Torrの圧力で
導入し、いずれも1500℃の焼結最高温度に到達後、５分
間保持しただちに真空に戻した。なお、温度は1500℃で
１時間保持後、冷却した。In sintering, the temperature was raised in a vacuum furnace, and after the appearance of the liquid phase, nitrogen gas was introduced at 1350 ° C at a pressure of 100 Torr for composition 1 and 150 Torr for composition 2, and after reaching the maximum sintering temperature of 1500 ° C, The vacuum was returned after holding for 5 minutes. The temperature was kept at 1500 ° C. for 1 hour and then cooled.
得られた焼結体に対し、硬質相の炭素、窒素を定量分
析し、N/（Ｃ＋Ｎ）原子比を求めたところ、組成１が0.
5、組成２が0.45であった。The obtained sintered body was quantitatively analyzed for carbon and nitrogen in the hard phase, and the N / (C + N) atomic ratio was determined.
5, composition 2 was 0.45.
また、この焼結体に対し、表面にわずかに析出した金
属成分を研磨除去した後、ビッカース硬度を測定したと
ころ組成１が2350、組成２が2400であった。The metal component slightly precipitated on the surface of this sintered body was polished and removed, and then the Vickers hardness was measured. As a result, the composition 1 was 2350 and the composition 2 was 2400.
なお、上記とまったく同様にして作製した特性測定用
試料に対し、約５゜の角度で研磨し、該研磨に対し、垂
直方向でビッカース硬度を表面からの距離（深さ）を変
えて測定したところ、いずれの焼結体も表面から内部に
亘り硬度が低くなる硬度勾配が生じていた。The sample for property measurement produced in exactly the same manner as above was polished at an angle of about 5 °, and the Vickers hardness was measured in a perpendicular direction with respect to the polishing by changing the distance (depth) from the surface. However, each of the sintered bodies had a hardness gradient in which the hardness decreased from the surface to the inside.
このようにして得た組成1,2のサーメットに対し、そ
のすくい面を研磨量をかえて研磨して、第２表に示すよ
うにすくい面の硬度の異なる数種の切削工具を得た。With respect to the cermets of compositions 1 and 2 thus obtained, the rake face was polished by varying the amount of polishing to obtain several types of cutting tools having different rake face hardnesses as shown in Table 2.
得られた切削工具に対して、耐摩耗性試験、耐欠損性
試験の次の条件で行った。The obtained cutting tool was subjected to the following conditions of a wear resistance test and a fracture resistance test.
結果は第１表に示した。 The results are shown in Table 1.
第１表の結果によれば、何ら研磨を行わなかったNo1,
5の試料に対し、すくい面を研磨したNo.2〜4,6,7の試料
はいずれも耐摩耗性はかわらないが、耐欠損性が大きく
向上していることがわかる。 According to the results in Table 1, No1 was not polished at all.
As compared to the sample No. 5, the samples of Nos. 2 to 4, 6, and 7 whose rake faces were polished did not show any change in wear resistance, but it was found that the chipping resistance was greatly improved.
以上、詳述したように、本発明のサーメット工具は、
窒素を多量に含む組成系から成り、その逃げ面とすくい
面に特定の硬度差および靭性差を設けることによって、
工具における耐摩耗性、耐欠損性を大幅に向上すること
ができ、工具としての長寿命化を達成することができ
る。As described above in detail, the cermet tool of the present invention is:
It consists of a composition system containing a large amount of nitrogen, and by providing a specific hardness difference and a toughness difference on its flank and rake face,
The wear resistance and fracture resistance of the tool can be significantly improved, and the life of the tool can be extended.
第１図は本発明において用いられるサーメット焼結体の
硬度分布を示す図であり、第２図は本発明において用い
られるサーメット焼結体の断面図である。 A:すくい面 B:逃げ面FIG. 1 is a diagram showing a hardness distribution of a cermet sintered body used in the present invention, and FIG. 2 is a sectional view of the cermet sintered body used in the present invention. A: rake face B: flank face
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭63−125637（ＪＰ，Ａ) 特開 昭63−62873（ＪＰ，Ａ) 特開 昭54−139815（ＪＰ，Ａ) 特開 平２−122030（ＪＰ，Ａ) 特開 昭63−227739（ＪＰ，Ａ) 特公 昭60−47906（ＪＰ，Ｂ２) (58)調査した分野(Int.Cl.6，ＤＢ名) B23B 27/14──────────────────────────────────────────────────続 き Continuation of front page (56) References JP-A-63-125637 (JP, A) JP-A-63-62873 (JP, A) JP-A-54-139815 (JP, A) JP-A-2- 122030 (JP, A) JP-A-63-227739 (JP, A) JP-B-60-47906 (JP, B2) (58) Fields investigated (Int. Cl. 6 , DB name) B23B 27/14
Claims (1)
て50乃至80重量％、周期律表第VI a族金属を炭化物とし
て10乃至40重量％の割合で含有するとともに、窒素／
（炭素＋窒素）で表される原子比が0.4乃至0.6の範囲に
ある硬質相成分70乃至95重量％と、鉄族金属を主成分と
する結合相成分５乃至30重量％とから成り、内部よりも
高硬度の表面部が形成されたサーメットのすくい面を研
磨除去して、前記逃げ面の硬度を内部の硬度および前記
すくい面の硬度よりも高くしたことを特徴とするサーメ
ット工具。(1) Ti is contained in a proportion of 50 to 80% by weight as a carbide, nitride or carbonitride, and a Group VIa metal of the periodic table in a proportion of 10 to 40% by weight as a carbide.
It comprises 70 to 95% by weight of a hard phase component having an atomic ratio of (carbon + nitrogen) in the range of 0.4 to 0.6, and 5 to 30% by weight of a binder phase component mainly composed of an iron group metal. A cermet tool characterized in that the rake face of the cermet on which a surface portion having a higher hardness is formed is polished and removed, so that the hardness of the flank is higher than the internal hardness and the hardness of the rake face.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1166225A JP2775298B2 (en) | 1989-06-28 | 1989-06-28 | Cermet tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1166225A JP2775298B2 (en) | 1989-06-28 | 1989-06-28 | Cermet tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0332502A JPH0332502A (en) | 1991-02-13 |
| JP2775298B2 true JP2775298B2 (en) | 1998-07-16 |
Family
ID=15827433
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1166225A Expired - Lifetime JP2775298B2 (en) | 1989-06-28 | 1989-06-28 | Cermet tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2775298B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100239844B1 (en) * | 1991-06-27 | 2000-01-15 | 이토우 겐스케 | Sintered alloy of golden color |
| EP0659699B1 (en) * | 1993-07-13 | 1999-11-10 | Sumitomo Electric Industries, Ltd. | Optical fiber drawing furnace and drawing method |
| US5976707A (en) * | 1996-09-26 | 1999-11-02 | Kennametal Inc. | Cutting insert and method of making the same |
| JP5004145B2 (en) * | 2004-06-09 | 2012-08-22 | 株式会社タンガロイ | Cermet and coated cermet and methods for producing them |
| SE528427C2 (en) * | 2004-07-09 | 2006-11-07 | Seco Tools Ab | A coated cutter for metalworking and ways to manufacture it |
| JP5334704B2 (en) * | 2009-06-25 | 2013-11-06 | 京セラ株式会社 | Cutting tools |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5917176B2 (en) * | 1978-04-24 | 1984-04-19 | 三菱マテリアル株式会社 | Sintered hard alloy with hardened surface layer |
| JPS6047906A (en) * | 1983-08-26 | 1985-03-15 | Hiroshi Fujii | Detecting device of length of let-out fishline |
| JPS6362873A (en) * | 1986-09-03 | 1988-03-19 | Hitachi Ltd | Ion-implanted cutting tool |
| JPH0617533B2 (en) * | 1986-11-17 | 1994-03-09 | 日本特殊陶業株式会社 | Cutting tip for cutting tools |
-
1989
- 1989-06-28 JP JP1166225A patent/JP2775298B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0332502A (en) | 1991-02-13 |
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