JP2808715B2 - Coated cemented carbide - Google Patents
Coated cemented carbideInfo
- Publication number
- JP2808715B2 JP2808715B2 JP1227238A JP22723889A JP2808715B2 JP 2808715 B2 JP2808715 B2 JP 2808715B2 JP 1227238 A JP1227238 A JP 1227238A JP 22723889 A JP22723889 A JP 22723889A JP 2808715 B2 JP2808715 B2 JP 2808715B2
- Authority
- JP
- Japan
- Prior art keywords
- cemented carbide
- alloy
- binder phase
- layer
- phase
- 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
Landscapes
- Chemical Vapour Deposition (AREA)
- Powder Metallurgy (AREA)
- Physical Vapour Deposition (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、切削工具等に使用される極めて強靭な被覆
超硬合金に関する。The present invention relates to a very tough coated cemented carbide used for cutting tools and the like.
従来から、切削工具等として、WC等の周期律表IV a、
V a、VI a族金属の炭化物及び窒化物の少なくとも１種
を硬質分散相とし、Fe、Ni、Co等の鉄族金属の少なくと
も１種を結合相とする超硬合金が用いられてきた。Conventionally, as a cutting tool, etc., periodic table IVa such as WC,
Cemented carbides have been used in which at least one of carbides and nitrides of Group Va and Group VIa metals is used as a hard dispersed phase and at least one of iron group metals such as Fe, Ni and Co is used as a binder phase.
又、超硬合金の表面にTiC等を蒸着等により被覆した
被覆超硬合金が提供され、超硬合金母材の強靭性と被覆
層の耐摩耗性を併せ持つために、被覆しない超硬合金に
比較して高能率な切削工具として使用されている。In addition, a coated cemented carbide in which the surface of a cemented carbide is coated with TiC or the like by vapor deposition or the like is provided.In order to have both the toughness of the cemented carbide base material and the wear resistance of the coating layer, it is necessary to It is used as a relatively efficient cutting tool.
ところが、最近では切削加工分野においても、NC等の
導入による完全自動化が著しく進行し、切削工具の信頼
性が極めて重要になつている。そのため、従来以上に高
い靭性を有する切削工具が強く求められている。However, recently, in the field of cutting, complete automation by the introduction of NC and the like has remarkably progressed, and the reliability of cutting tools has become extremely important. Therefore, there is a strong demand for cutting tools having higher toughness than ever before.
この問題を解決するため、合金表面のみに、WC−Co層
を有する超硬合金（特開昭52−159299号公報参照）、合
金表面にCo量を富化させた超硬合金（特開昭62−105628
号公報参照）、被覆層直下での脱炭層の発生を防止する
ために合金内部に遊離炭素を存在せしめる方法（特開昭
52−155190号公報参照）が提案されている。In order to solve this problem, a cemented carbide having a WC-Co layer only on the surface of the alloy (see JP-A-52-159299) and a cemented carbide having a Co-enriched surface on the alloy surface (see JP-A-52-159299) 62−105628
And Japanese Patent Application Laid-Open No. H10-157, in which free carbon is present inside the alloy to prevent the formation of a decarburized layer immediately below the coating layer.
52-155190).
しかし、合金表面のみにWC−Co層を有する超硬合金及
び合金表面にCo量を富化させた超硬合金では、靭性は向
上するものの、耐摩耗性に劣る欠点があつた。又、合金
表面にCo量を富化させた超硬合金は、切削速度が高い条
件下ではすくい面摩耗速度が速くなるため、実用上使用
に耐えない場合があつた。一方、合金内部に遊離炭素を
存在させた超硬合金では、遊離炭素量の増加と共に靭性
が向上するが、遊離炭素量が高々0.2％を超えると塊状
化して合金強度そのものを低下させる欠点があつた。However, a cemented carbide having a WC-Co layer only on the alloy surface and a cemented carbide having a Co content enriched on the alloy surface have a defect that the toughness is improved but the wear resistance is inferior. Further, a cemented carbide in which the amount of Co is enriched in the alloy surface has a high rake face wear rate under a high cutting speed condition, and thus may not be practically usable. On the other hand, in a cemented carbide in which free carbon is present inside the alloy, the toughness improves as the amount of free carbon increases, but when the amount of free carbon exceeds 0.2% at the most, there is a drawback that the alloy is aggregated and the alloy strength itself is reduced. Was.
本発明はかかる従来の事情に鑑み、切削加工分野の完
全自動化に伴なつて要望されている信頼性の高い切削工
具を供給するため、優れた耐摩耗性と共に、高い靭性を
兼ね備えた被覆超硬合金を提供することを目的とする。In view of such conventional circumstances, the present invention provides a highly reliable cutting tool required with the full automation of the cutting field, so that coated carbide having both excellent wear resistance and high toughness is provided. It is intended to provide an alloy.
上記目的を達成するため、本発明では、周期律表IV
a、V a、VI a族金属の炭化物及び窒化物の少なくとも１
種を硬質分散相とし、鉄族金属の少なくとも１種を結合
相とする超硬合金において、当該合金の表面から深さ10
〜500μｍの間に結合相量を合金内部より1.2〜５倍に増
加させた結合相富化層を備え、且つ当該合金の表面に周
期律表IV a、V a、VI a族金属の炭化物、窒化物、酸化
物及び硼化物、並びに酸化アルミニウムの少なくとも１
種からなる単層又は複層の被覆層を備えたことを特徴と
する。In order to achieve the above object, in the present invention, the periodic table IV
a, Va, at least one of carbides and nitrides of Group VIa metals
In a cemented carbide having a species as a hard disperse phase and at least one type of iron group metal as a binder phase, a depth of 10
A binder phase-enriched layer in which the amount of the binder phase is increased by 1.2 to 5 times from the inside of the alloy to 500 μm, and the periodic table IVa, Va, a carbide of a Group VIa metal on the surface of the alloy, At least one of nitrides, oxides and borides, and aluminum oxide
It is characterized by comprising a single-layer or multiple-layer covering layer made of a seed.
尚、超硬合金に結合相富化層を形成する方法として
は、型内に結合相の量が異なる合金粉末を順次充填する
か、結合相の量が異なる圧粉体をラミネートし、プレス
成形した後焼結する方法、若しくは同一結合相量の合金
粉末のみを用いてプレス成形した後、焼結過程において
浸炭処理や脱炭処理を繰り返す方法等がある。又、表面
への被覆層の形成には、通常の如くCVD法やPVD法により
気相から蒸着する方法を使用出来る。In addition, as a method of forming the binder phase enriched layer on the cemented carbide, a mold is sequentially filled with alloy powders having different amounts of the binder phase, or a green compact having a different amount of the binder phase is laminated and press-molded. After that, there is a method of sintering, or a method of performing press molding using only alloy powder of the same bonding phase amount, and repeating a carburizing treatment and a decarburizing treatment in a sintering process. For forming a coating layer on the surface, a method of vapor deposition from a gas phase by a conventional CVD method or PVD method can be used.
本発明の被覆超硬合金では、合金表面からの深さ10〜
500μｍの間に合金内部よりも結合相量の多い結合相富
化層を設けることによつて、耐摩耗性に寄与しない部分
で相対的にCo等の結合相量を多くできるので、全体とし
て高い靭性を付与することが出来る。In the coated cemented carbide of the present invention, the depth from the alloy surface 10 ~
By providing the binder phase enriched layer having a larger binder phase amount than the inside of the alloy between 500 μm, the amount of the binder phase such as Co can be relatively increased in the portion that does not contribute to the wear resistance, so that the overall Toughness can be imparted.
上記結合相富化層の存在位置が、合金表面から10μｍ
より浅ければ、切削速度の高い場合に表面軟化がおこり
やすく、又鋳鉄の切削において表面部の耐摩耗性低下を
来しやすい。反対に500μｍよりも深ければ、靭性の改
善が期待できない。The position of the binder phase enriched layer is 10 μm from the alloy surface.
If it is shallower, surface softening tends to occur when the cutting speed is high, and the wear resistance of the surface tends to decrease in cutting of cast iron. Conversely, if it is deeper than 500 μm, improvement in toughness cannot be expected.
結合相富化層における結合相の量は、結合相富化層の
位置について述べた上記と同様の理由により、合金内部
の結合相量の1.2〜５倍とする。The amount of the binder phase in the binder-phase-enriched layer is set to 1.2 to 5 times the amount of the binder phase inside the alloy for the same reason as described above for the position of the binder-phase-enriched layer.
尚、結合相富化層の厚さが５μｍ未満では靭性の向上
に余り寄与せず、逆に100μｍを超えると切削時に結合
相富化層の塑性流動を生じ、刃先部の塑性変形をもたら
すため、厚さは５〜100μｍの範囲が好ましい。If the thickness of the binder-phase-enriched layer is less than 5 μm, it does not contribute much to the improvement of toughness. Conversely, if it exceeds 100 μm, plastic flow of the binder-phase-enriched layer occurs during cutting, which causes plastic deformation of the cutting edge. The thickness is preferably in the range of 5 to 100 μm.
又、合金の表面に周期律表IV a、V a、VI a族金属の
炭化物、窒化物、酸化物及び硼化物、並びに酸化アルミ
ニウムの少なくとも１種の硬質物質からなる単層又は複
層の被覆層を備えることによつて、優れた耐摩耗性を確
保できる。In addition, a single-layer or multiple-layer coating made of at least one hard material of carbides, nitrides, oxides and borides of Group IVa, Va and VIa metals and aluminum oxide on the surface of the alloy. By providing the layer, excellent wear resistance can be ensured.
実施例１ WC−５％Co合金粉末をプレス成形後、その外周にWC−
６％Co合金粉末（Ａ）、WC−10％Co合金粉末（Ｂ）、WC
−20％Co合金粉末（Ｃ）、又はWC−25Co合金粉末（Ｄ）
を夫々順次に装填プレスし、更にその外周にWC−5.5％C
o合金粉末を装填した後、SNG432になるようにプレス成
形し、真空雰囲気中において1380℃で焼結して、第１表
に示す構造を有する超硬合金を製造した。尚、上記合金
粉末の組成はいずれも重量％である。Example 1 WC-5% Co alloy powder was press-molded, and WC-
6% Co alloy powder (A), WC-10% Co alloy powder (B), WC
-20% Co alloy powder (C) or WC-25Co alloy powder (D)
And then press each one in turn, and then WC-5.5% C
o After the alloy powder was charged, it was press-molded into SNG432 and sintered at 1380 ° C. in a vacuum atmosphere to produce a cemented carbide having the structure shown in Table 1. The composition of each of the above alloy powders is% by weight.
更に、得られた各超硬合金の表面に、通常のCVD法に
より、内側に５μｍのTiC及び表面側に１μｍのAl2O3を
被覆して被覆超硬合金を得た。 Further, the surface of each of the obtained cemented carbides was coated with 5 μm of TiC inside and 1 μm of Al 2 O 3 on the surface side by a normal CVD method to obtain a coated cemented carbide.
比較のために、組成がWC−５％Co（Ｅ）とWC−10％Co
（Ｆ）の通常の超硬合金（結合相富化層なし）の表面上
に、上記と同様の被覆を形成した。For comparison, the compositions are WC-5% Co (E) and WC-10% Co
The same coating as described above was formed on the surface of the ordinary cemented carbide (F) without the binder phase enriched layer.
得られた各試料について、下記条件による切削テスト
を行ない、結果を第２表に示した。For each of the obtained samples, a cutting test was performed under the following conditions, and the results are shown in Table 2.
切削テスト（逃げ面摩耗量） 切削速度 180m/min 送 り 0.36mm/rev 切込み 2.0mm 被削材 SCM435 切削時間 20分 切削テスト（欠損率） 切削速度 60m/min 送 り 0.20〜0.40mm/rev 切込み 2.0mm 被削材 SCM435（四溝材） 切削時間 30秒 ８回繰り返し 本発明の被覆超硬合金は、耐摩耗性及び靭性共に優れ
ていることが判る。Cutting test (flank wear) Cutting speed 180m / min Feed 0.36mm / rev Depth of cut 2.0mm Work material SCM435 Cutting time 20min Cutting test (defect rate) Cutting speed 60m / min Feed 0.20 ~ 0.40mm / rev Depth of cut 2.0mm work material SCM435 (four groove material) Cutting time 30 seconds 8 times It can be seen that the coated cemented carbide of the present invention is excellent in both wear resistance and toughness.
実施例２ 実施例１の試料Ａと同じ組成であるが、結合相富化層
（表面側深さは実施例１と同じく10μｍ）の厚さを変化
させた試料Ａ−１〜４を製造し、実施例１と同様の切削
テスト及びを行なつて、結果を第３表に示した。Example 2 Samples A-1 to A-4 having the same composition as the sample A of the example 1 but changing the thickness of the binder phase enriched layer (the surface side depth was 10 μm as in the example 1) were manufactured. The same cutting test as in Example 1 was performed, and the results are shown in Table 3.
〔発明の効果〕 本発明によれば、合金表面から所定深さに結合相富化
層を及び合金表面上に硬質の被覆層を夫々備えることに
よつて、優れた靭性と耐摩耗性とを兼ね備え、切削工具
用として好適な被覆超硬合金を提供することが出来る。 [Effects of the Invention] According to the present invention, by providing a binder phase-enriched layer at a predetermined depth from the alloy surface and a hard coating layer on the alloy surface, excellent toughness and wear resistance can be obtained. Also provided is a coated cemented carbide suitable for cutting tools.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２３Ｃ 14/08 Ｃ２３Ｃ 14/08 Ａ (58)調査した分野(Int.Cl.6，ＤＢ名) C23C 16/00 - 16/56 C23C 14/06 C23C 14/08 C22C 29/08,1/05──────────────────────────────────────────────────続 き Continuation of front page (51) Int.Cl. 6 identification symbol FI C23C 14/08 C23C 14/08 A (58) Field surveyed (Int.Cl. 6 , DB name) C23C 16/00-16 / 56 C23C 14/06 C23C 14/08 C22C 29 / 08,1 / 05
Claims (2)
及び窒化物の少なくとも１種を硬質分散相とし、鉄族金
属の少なくとも１種を結合相とする超硬合金において、
当該合金の表面から深さ10〜500μｍの間に結合相量を
合金内部より1.2〜５倍に増加させた結合相富化層を備
え、且つ当該合金の表面に周期律表IV a、V a、VI a族
金属の炭化物、窒化物、酸化物及び硼化物、並びに酸化
アルミニウムの少なくとも１種からなる単層又は複層の
被覆層を備えたことを特徴とする被覆超硬合金。1. A cemented carbide comprising at least one of carbides and nitrides of Group IVa, Va, and VIa metals as a hard dispersed phase and at least one of iron group metals as a binder phase.
A binder phase-enriched layer in which the amount of the binder phase is increased 1.2 to 5 times from the inside of the alloy at a depth of 10 to 500 μm from the surface of the alloy, and the periodic table IVa, Va A coated cemented carbide comprising a single layer or a multiple layer of at least one of carbides, nitrides, oxides and borides of Group VIa metals, and aluminum oxide.
ことを特徴とする、請求項（１）記載の被覆超硬合金。2. The coated cemented carbide according to claim 1, wherein the thickness of the binder phase enriched layer is 5 to 100 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1227238A JP2808715B2 (en) | 1989-09-01 | 1989-09-01 | Coated cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1227238A JP2808715B2 (en) | 1989-09-01 | 1989-09-01 | Coated cemented carbide |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0390575A JPH0390575A (en) | 1991-04-16 |
| JP2808715B2 true JP2808715B2 (en) | 1998-10-08 |
Family
ID=16857680
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1227238A Expired - Lifetime JP2808715B2 (en) | 1989-09-01 | 1989-09-01 | Coated cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2808715B2 (en) |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61110771A (en) * | 1984-11-06 | 1986-05-29 | Hitachi Metals Ltd | Surface covered sintered hard alloy |
-
1989
- 1989-09-01 JP JP1227238A patent/JP2808715B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0390575A (en) | 1991-04-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2598791B2 (en) | Sintered body for chip forming | |
| US5296016A (en) | Surface coated cermet blade member | |
| USRE35538E (en) | Sintered body for chip forming machine | |
| JP2762745B2 (en) | Coated cemented carbide and its manufacturing method | |
| EP0515340A2 (en) | Titanium based carbonitride alloy with binder phase enrichment | |
| JP2775955B2 (en) | Manufacturing method of coating cermet with excellent wear resistance | |
| KR20090028444A (en) | Coated cutting insert for milling applications | |
| JP4170402B2 (en) | Titanium-based carbonitride alloy with nitrided surface region | |
| JPH0196084A (en) | Surface-coated cubic boron nitride-based material sintered under superhigh pressure to be used for cutting tool | |
| JP2808715B2 (en) | Coated cemented carbide | |
| JP3850085B2 (en) | Coated cermet for cutting tools | |
| JP2625923B2 (en) | Surface coated cermet for cutting tools | |
| JPH10237650A (en) | Wc base cemented carbide and its production | |
| JPH04231467A (en) | Coated tic-base cermet | |
| JPS597349B2 (en) | Coated cemented carbide tools | |
| JP2819648B2 (en) | Coated cemented carbide for wear-resistant tools | |
| JPH0698540B2 (en) | Method for manufacturing a cutting tool made of thermite with excellent wear resistance | |
| JP2645340B2 (en) | Manufacturing method of coated cemented carbide tool | |
| JP2801484B2 (en) | Cemented carbide for cutting tools | |
| JP4126451B2 (en) | Cemented carbide | |
| JPH0215159A (en) | Production of cutting made of surface-treated cermet | |
| JPH0530881B2 (en) | ||
| JP2808714B2 (en) | Coated cemented carbide for wear-resistant tools | |
| JPH04231468A (en) | Surface coated ticn-base cermet | |
| JP2970199B2 (en) | Surface-coated Ti-carbon boride based cermet cutting tool with excellent adhesion of hard coating layer |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20080731 Year of fee payment: 10 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20080731 Year of fee payment: 10 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090731 Year of fee payment: 11 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090731 Year of fee payment: 11 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100731 Year of fee payment: 12 |
|
| EXPY | Cancellation because of completion of term | ||
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100731 Year of fee payment: 12 |