JP2002137103A - Cutting tool - Google Patents
Cutting toolInfo
- Publication number
- JP2002137103A JP2002137103A JP2000329631A JP2000329631A JP2002137103A JP 2002137103 A JP2002137103 A JP 2002137103A JP 2000329631 A JP2000329631 A JP 2000329631A JP 2000329631 A JP2000329631 A JP 2000329631A JP 2002137103 A JP2002137103 A JP 2002137103A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- base material
- hard coating
- cutting tool
- tin layer
- 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.)
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は耐摩耗性に優れた硬
質被膜付の切削工具に関し、より詳細には、耐衝撃性と
耐剥離性を向上させた切削工具に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cutting tool with a hard coating having excellent wear resistance, and more particularly to a cutting tool having improved impact resistance and peeling resistance.
【０００２】[0002]
【従来の技術】近年、切削工具として用いられる超硬合
金母材表面に化学気相成長等の手段によって、耐摩耗性
に優れた硬質被膜を被覆した被覆超硬合金が注目されて
いる。通常、このような硬質被膜としては、炭化チタ
ン、炭窒化チタン等のチタン系化合物が強度、靭性の点
において優れるため、強靭性コーティング工具にはチタ
ン系化合物が多く用いられる。2. Description of the Related Art In recent years, attention has been paid to a coated cemented carbide in which a hard coating excellent in wear resistance is coated on the surface of a cemented carbide base material used as a cutting tool by means such as chemical vapor deposition. Normally, titanium compounds such as titanium carbide and titanium carbonitride are excellent in strength and toughness as such a hard coating, and thus titanium compounds are often used in tough coating tools.
【０００３】一方、Ａｌ2Ｏ3は化学的安定性、耐熱性に
優れるので、高速切削領域下で使用する切削工具におい
てチタン系化合物と併用されている。具体的には前記硬
質被膜は少なくとも超硬合金母材と接するＴｉＮ層と該
ＴｉＮ層より外側にＡｌ2Ｏ3層を被覆したものであっ
て、膜厚が７〜１５μｍ程度の複層で構成され、かつ、
下地のＴｉＮ層の厚みがＡｌ2Ｏ3層の約１０〜５０％程
度であった。On the other hand, Al 2 O 3 has excellent chemical stability and heat resistance, and is therefore used together with a titanium compound in a cutting tool used in a high-speed cutting region. Specifically, the hard coating comprises at least a TiN layer in contact with the cemented carbide base material and an Al 2 O 3 layer outside the TiN layer, and is composed of a multilayer having a thickness of about 7 to 15 μm. And
The thickness of the underlying TiN layer was about 10 to 50% of the Al 2 O 3 layer.
【０００４】[0004]
【発明が解決しようとする課題】しかしながら、かかる
従来の超硬合金と接するＴｉＮ層と該ＴｉＮ層より外側
にＡｌ2Ｏ3層を被覆して硬質被膜を形成した切削工具は
耐熱性、耐摩耗性には優れるものの、靭性が低いため超
硬合金母材の靭性を損なっていた。However, such a conventional cutting tool having a hard coating formed by coating a TiN layer in contact with a cemented carbide and an Al 2 O 3 layer outside of the TiN layer is heat-resistant and wear-resistant. Although excellent in toughness, the toughness was low and the toughness of the cemented carbide base material was impaired.
【０００５】また、Ａｌ2Ｏ3層はＣＶＤ法によって形成
するが、硬質被膜をＣＶＤ法によって形成するに際し、
母材と硬質被膜との界面には低級炭化物である脆化層
（η相）が形成されやすい。これは、硬質被膜中に母材
の炭素が被膜に拡散したため生じたものと考えられる。
この脆化層の生成によって母材と硬質被膜との密着強度
が低下するため、これを工具として用いた場合、硬質被
膜の剥離が生じ、母材である超硬合金が露出して急激に
摩耗が進行し、著しく切削性能、寿命が低下するという
欠点を有していた。The Al 2 O 3 layer is formed by a CVD method. When a hard film is formed by a CVD method,
An embrittlement layer (η phase), which is a lower carbide, is easily formed at the interface between the base material and the hard coating. This is considered to be caused by the diffusion of the base material carbon into the hard coating.
Due to the formation of the embrittlement layer, the adhesion strength between the base material and the hard coating is reduced. When this is used as a tool, the hard coating is peeled off, and the cemented carbide as the base material is exposed and rapidly worn. , The cutting performance and the life are remarkably reduced.
【０００６】さらにＡｌ2Ｏ3層を含む上記複層硬質被膜
は上記η層および炭素の拡散のために、母材との境界
域、或いは各層間の境界域が弱く、これに起因して工具
破損が起こる場合があった。一般にステンレス鋼などの
難削材を切削する際、複層硬質被膜には特に機械的な負
荷がかかるため、それぞれの硬質層の特性、および各層
間、母材界面の付着力を向上させることが特に重要であ
る。Further, the multilayer hard coating containing an Al 2 O 3 layer has a weak boundary area with the base material or a boundary area between the respective layers due to the diffusion of the η layer and carbon. In some cases, damage occurred. Generally, when cutting difficult-to-cut materials such as stainless steel, a multi-layered hard coating is particularly subjected to a mechanical load. Therefore, it is possible to improve the characteristics of each hard layer and the adhesion between each layer and the interface of the base material. Of particular importance.
【０００７】本発明は、かかる従来技術の問題点に鑑み
てなされたもので、超硬合金母材と接するＴｉＮ層と該
ＴｉＮ層より外側にＡｌ2Ｏ3層を被覆して硬質被膜を形
成した切削工具において、切削工具の耐衝撃性と硬質被
膜の母材との或いは各層間の耐剥離性の両方を向上させ
ることを目的とする。The present invention has been made in view of the problems of the prior art, and forms a hard film by coating a TiN layer in contact with a cemented carbide base material and an Al 2 O 3 layer outside the TiN layer. It is an object of the present invention to improve both the impact resistance of a cutting tool and the peeling resistance of a hard coating base material or between layers.
【０００８】[0008]
【課題を解決するための手段】本発明者は上記の問題点
に対し、検討を重ねた結果、ＷＣを主成分とする超硬合
金母材に硬質被膜を形成した切削工具において、上記硬
質被膜の膜厚が１乃至１０μｍという設定の中で下地Ｔ
ｉＮ層をＡｌ2Ｏ3膜よりも厚く設けることにより、切削
工具の耐衝撃性と硬質被膜の母材との或いは各層間の耐
剥離性の両方が顕著に向上することを見出した。すなわ
ち、請求項１の切削工具は、WCを主成分とし、周期律表
第４ａ,５ａ,６ａ族元素の炭化物、窒化物、炭窒化物の
群から選ばれる少なくとも１種の硬質相成分と、鉄族元
素の少なくとも１種からなる結合相から構成される超硬
合金母材の表面に硬質被膜を形成してなる切削工具であ
って、前記硬質被膜は少なくとも前記母材と接するＴｉ
Ｎ層と該ＴｉＮ層より外側にＡｌ2Ｏ3層を被覆した、膜
厚が１乃至１０μｍの複層で構成されるとともに、前記
母材と接するＴｉＮ層の厚みが前記Ａｌ2Ｏ3層よりも大
であることを特徴とする。Means for Solving the Problems The present inventor has studied the above problems, and as a result, has found that in a cutting tool in which a hard film is formed on a cemented carbide base material mainly composed of WC, the hard film is hardened. In the setting of the film thickness of 1 to 10 μm,
By providing the iN layer thicker than the Al 2 O 3 film, it has been found that both the impact resistance of the cutting tool and the peel resistance between the hard coating base material and each layer are significantly improved. That is, the cutting tool of claim 1 has WC as a main component, and at least one hard phase component selected from the group consisting of carbides, nitrides, and carbonitrides of Group 4a, 5a, and 6a elements of the periodic table; A cutting tool in which a hard coating is formed on a surface of a cemented carbide base material composed of a binder phase made of at least one iron group element, wherein the hard coating is formed of at least Ti which is in contact with the base material.
An N 2 layer and an Al 2 O 3 layer coated on the outer side of the TiN layer, a multilayer having a thickness of 1 to 10 μm, and a TiN layer in contact with the base material having a thickness smaller than that of the Al 2 O 3 layer Is also large.
【０００９】かかる構成により、切削工具の耐衝撃性と
硬質被膜の母材との或いは各層間の耐剥離性の両方が顕
著に向上するメカニズムは次のように考えられる。The mechanism by which both the impact resistance of the cutting tool and the peeling resistance of the hard coating base material or between the respective layers are remarkably improved by the above configuration is considered as follows.
【００１０】すなわち、硬質被膜として用いられる材質
の中で最も強度の高いＴｉＮ層を母材に接する下地層と
して厚く設けることで、この下地層が硬質被膜全体の緩
衝材として働き、さらに、母材からの炭素の拡散を防ぐ
効果によって硬質被膜の母材との或いは各層間の密着強
度が向上する。That is, by providing a TiN layer having the highest strength among the materials used as the hard coating as a thick underlayer in contact with the base material, this base layer functions as a buffer material for the entire hard coating, and furthermore, Adhesion strength between the hard coating and the base material or between the layers is improved by the effect of preventing carbon from diffusing.
【００１１】これら効果は該ＴｉＮ層が前記Ａｌ2Ｏ3層
よりも大であるときに顕著にあらわれるものである。These effects are remarkable when the TiN layer is larger than the Al 2 O 3 layer.
【００１２】これに対して、硬質被膜の厚みが１μｍ未
満の場合は硬質被膜としての耐摩耗性を発揮しない。ま
た、硬質被膜の厚みが１０μｍより大きい場合、あるい
は、下地ＴｉＮ層がＡｌ2Ｏ3膜よりも同じ厚さ、あるい
は薄い場合には耐剥離性の向上が見られない。加えて、
硬質被膜の厚みが１０μｍより大きい場合、耐衝撃性の
向上が見られない。On the other hand, when the thickness of the hard coating is less than 1 μm, the hard coating does not exhibit wear resistance. When the thickness of the hard coating is larger than 10 μm or when the thickness of the underlying TiN layer is the same or smaller than that of the Al 2 O 3 film, no improvement in peeling resistance is observed. in addition,
When the thickness of the hard coating is larger than 10 μm, no improvement in impact resistance is observed.
【００１３】また、ＷＣの含有量が５０重量％未満であ
るサーメットを母材とする場合については、サーメット
にＣＶＤ法による硬質被膜を形成する場合、被膜各層の
異常粒成長が発生するため、総合的な性能として耐衝撃
性・耐剥離性に不足する。In the case where a cermet having a WC content of less than 50% by weight is used as a base material, when a hard coating is formed on the cermet by the CVD method, abnormal grain growth occurs in each layer of the coating. Insufficient impact resistance and peeling resistance.
【００１４】次に、請求項２の切削工具は、前記硬質被
膜の表面粗さの最大高さ（Ｒｙ）が５μｍ以下であり、
かつ、前記Ａｌ2Ｏ3層の結晶粒径が０．１乃至３．０μ
ｍであることを特徴とする。Next, in the cutting tool of the present invention, the maximum height (Ry) of the surface roughness of the hard coating is 5 μm or less,
The Al 2 O 3 layer has a crystal grain size of 0.1 to 3.0 μm.
m.
【００１５】かかる構成によれば、表面粗さや結晶粒径
を上記の範囲に制御することにより被削材の切屑と刃部
表面との抵抗が低減されるので耐摩耗性を維持できると
ともに局部的な外部応力の発生を防止することができ、
膜の欠損を低減することができ、工具寿命を向上させる
ことができ、前記切削工具の耐衝撃性と各層間耐剥離性
の両方を向上させることを、よりいっそう確実とするこ
とができる。なお、上記最大高さ（Ｒｙ）が５μｍを超
える場合、あるいは結晶粒径が３．０μｍを超える場
合、耐摩耗性の低下や突発的な欠損をする恐れがある。
また、結晶粒径が０．１μｍ未満のＡｌ2Ｏ3層を得るの
は非常に困難である。以下、本発明を詳述する。本発明
において用いられる基体としては、それ自体ある程度の
機械的強度を必要とするため、WCを主成分とし、周期律
表第４ａ,５ａ,６ａ族元素の炭化物、窒化物、炭窒化物
の群から選ばれる少なくとも１種の硬質相成分と、鉄族
元素の少なくとも１種からなる結合相から構成する。上
記硬質被膜は、膜厚が１乃至１０μｍの複層で構成され
るとともに、母材と接するＴｉＮ層と該ＴｉＮ層より外
側にＡｌ2Ｏ3層を被覆した。ここで前記母材と接するＴ
ｉＮ層の厚みが前記Ａｌ2Ｏ3層よりも大であることが重
要である。この構成により、Ａｌ2Ｏ3層の靭性の低さお
よび硬質被膜の母材との或いは各層間の密着強度の低さ
という欠点を、母材と接するＴｉＮ層の厚さを大にする
ことにより補うものである。なお、母材に接するＴｉＮ
層の上に第２層として柱状結晶組織でなるＴｉＣＮ層等
を設け、その外側にＡｌ2Ｏ3層を設けることによって
も、１乃至１０μｍの範囲であるならばこの効果は損な
われない。According to this configuration, by controlling the surface roughness and the crystal grain size within the above ranges, the resistance between the chips of the work material and the blade surface can be reduced, so that the wear resistance can be maintained and the local area can be maintained. External stress can be prevented,
The loss of the film can be reduced, the tool life can be improved, and both the impact resistance and the interlayer peeling resistance of the cutting tool can be further assured. If the maximum height (Ry) exceeds 5 μm, or if the crystal grain size exceeds 3.0 μm, the abrasion resistance may decrease or sudden loss may occur.
Also, it is very difficult to obtain an Al 2 O 3 layer having a crystal grain size of less than 0.1 μm. Hereinafter, the present invention will be described in detail. Since the substrate used in the present invention itself requires a certain level of mechanical strength, it is mainly composed of WC, and is a group of carbides, nitrides, and carbonitrides of elements of Groups 4a, 5a, and 6a of the periodic table. And a binder phase composed of at least one of iron group elements. The hard coating was composed of a multilayer having a thickness of 1 to 10 μm, and was covered with a TiN layer in contact with the base material and an Al 2 O 3 layer outside the TiN layer. Here, T in contact with the base material
It is important that the thickness of the iN layer is larger than that of the Al 2 O 3 layer. With this configuration, the disadvantages of low toughness of the Al 2 O 3 layer and low adhesion strength between the hard coating and the base material or between the layers are reduced by increasing the thickness of the TiN layer in contact with the base material. It is a supplement. Note that TiN in contact with the base material
Even if a TiCN layer or the like having a columnar crystal structure is provided as a second layer on the layer and an Al 2 O 3 layer is provided outside the TiCN layer, this effect is not impaired as long as the thickness is in the range of 1 to 10 μm.
【００１６】また、上記硬質被膜はＡｌ2Ｏ3層の外側に
最外層としてＴｉＮ層を形成したものであっても良い。
最外層のＴｉＮ層は使用済み刃先の識別の目的で設ける
ものであって耐衝撃性や耐剥離性には悪影響は及ぼさな
い。The hard coating may have a TiN layer formed as an outermost layer outside the Al 2 O 3 layer.
The outermost TiN layer is provided for the purpose of identifying the used cutting edge, and does not adversely affect impact resistance and peeling resistance.
【００１７】上記母材と接するＴｉＮ層の厚みとしては
１乃至４μｍであることが好ましい。これに対して、厚
みが１μｍ以下では耐衝撃性・耐剥離性が十分ではな
く、４μｍ以上になると硬質被膜としての耐摩耗性を維
持できなくなる恐れがある。The thickness of the TiN layer in contact with the base material is preferably 1 to 4 μm. On the other hand, when the thickness is 1 μm or less, the impact resistance and peeling resistance are not sufficient, and when the thickness is 4 μm or more, the wear resistance as a hard coating may not be maintained.
【００１８】他方、上記Ａｌ2Ｏ3層の厚みとしては０．
５乃至２μｍであることが好ましい。これは０．５μｍ
以下では耐摩耗性が不足し、２μｍ以上になると結晶粒
が成長し耐衝撃性・耐剥離性に悪影響を及ぼす恐れがあ
る。On the other hand, the thickness of the Al 2 O 3 layer is 0.1 mm.
It is preferably 5 to 2 μm. This is 0.5 μm
Below, the abrasion resistance is insufficient, and if it is 2 μm or more, crystal grains may grow and adversely affect impact resistance and peeling resistance.
【００１９】上記硬質被膜は、まず、前述した所望の基
体上に公知の気相成長法、例えば熱ＣＶＤ、ＲＦプラズ
マＣＶＤ、マイクロ波ＣＶＤ、ＥＣＲプラズマＣＶＤ等
のＣＶＤ法、イオンビーム法、スパッタ法等のＰＶＤ法
等によって母材に接する下地層としてＴｉＮ層さらに該
ＴｉＮ層より外側にＣＶＤ法によりＡｌ2Ｏ3層を形成す
ることにより得ることができる。この際、該ＴｉＮ層を
Ａｌ2Ｏ3層よりも厚く設けることにより効果を得られ
る。The hard coating is first formed on the desired substrate by a known vapor phase growth method, for example, a CVD method such as thermal CVD, RF plasma CVD, microwave CVD, or ECR plasma CVD, an ion beam method, or a sputtering method. It can be obtained by forming a TiN layer as an underlayer in contact with the base material by a PVD method or the like and further forming an Al 2 O 3 layer outside the TiN layer by a CVD method. At this time, the effect can be obtained by providing the TiN layer thicker than the Al 2 O 3 layer.
【００２０】また、硬質被膜の表面粗さ、およびＡｌ2
Ｏ3層の粒径を制御して表面粗さの最大高さ（Ｒｙ）を
５μｍ以下、Ａｌ2Ｏ3層の結晶粒径を０．１乃至３．０
μｍとすることによりさらに望ましい効果が得られる。Also, the surface roughness of the hard coating and the Al 2
By controlling the grain size of the O 3 layer, the maximum height (Ry) of the surface roughness is set to 5 μm or less, and the crystal grain size of the Al 2 O 3 layer is set to 0.1 to 3.0.
A more desirable effect can be obtained by setting the thickness to μm.
【００２１】上記硬質被膜の表面粗さ、およびＡｌ2Ｏ3
層の粒径の制御はＡｌ2Ｏ3層成膜中のガス流量比、成膜
温度、添加ガスなどを適宜調整することによって行うこ
とができる。たとえば、成膜温度を低くする、あるいは
核生成工程の反応ガス流量比を増やすことなどで上記制
御を行うことができる。The surface roughness of the hard coating and Al 2 O 3
The particle size of the layer can be controlled by appropriately adjusting the gas flow ratio, the film forming temperature, the added gas, and the like during the formation of the Al 2 O 3 layer. For example, the above control can be performed by lowering the film forming temperature or increasing the reaction gas flow ratio in the nucleation step.
【００２２】[0022]
【実施例】以下、本発明を次の例で説明する。The present invention will be described below with reference to the following examples.
【００２３】一般的な超硬合金母材の製法として原料粉
末を混合粉砕後、ＣＮＭＧ１２０４０８形状に成形して
１．３３３２２Ｐａ以下の真空中で、１７７３Kで１時
間焼成し、単一組成のＩＳＯ Ｍ２０の超硬合金母材を
得た。また、硬質被膜の成膜法として通常の化学蒸着装
置を用い、表１および２に示す構成・膜厚のサンプルを
作製した。As a general method of manufacturing a cemented carbide base material, raw material powders are mixed and pulverized, then molded into a CNMG120408 shape, and baked at 1,773 K in a vacuum of 1.3332 Pa or less at 1773 K for 1 hour to obtain a single composition ISO M20. A cemented carbide base material was obtained. In addition, samples having the configurations and film thicknesses shown in Tables 1 and 2 were produced using a conventional chemical vapor deposition apparatus as a method for forming a hard film.
【００２４】[0024]
【表１】 [Table 1]
【００２５】[0025]
【表２】 [Table 2]
【００２６】一般的な成膜条件としてＴｉＮ層の成膜に
はＴｉＣｌ4：５．４％、Ｎ2：３０％、Ｈ2：残り（流
量モル比）総流量：４５リットル、基体温度：９００
℃、反応容器内圧力：２６，６６４．２Ｐａの条件で行
った。As general film forming conditions, TiCl 4 : 5.4%, N 2 : 30%, H 2 : balance (flow molar ratio), total flow rate: 45 liter, substrate temperature: 900 for TiN layer film formation
C., pressure in the reaction vessel: 26, 664.2 Pa.
【００２７】また、Ａｌ2Ｏ3層の成膜にはＡｌＣｌ3：
３％、ＣＯ2：７％、Ｈ2：残り（流量モル比）総流量：
５０リットル、基体温度１０００℃、反応容器内圧力：
８，６６５．９３Ｐａの条件で行った。For the formation of the Al 2 O 3 layer, AlCl 3 :
3%, CO 2 : 7%, H 2 : remaining (flow molar ratio)
50 liter, substrate temperature 1000 ° C., pressure inside reaction vessel:
The test was performed under the condition of 8,665.93 Pa.
【００２８】なお、Ａｌ2Ｏ3層成膜中のガス流量比、成
膜温度、添加ガスなどによって結晶粒径を制御した。こ
こでいうＡｌ2Ｏ3層の平均結晶粒径の測定は、走査型電
子顕微鏡のより撮影された被膜断面あるいは研磨後のエ
ッチング写真において、一定視野内に見える結晶粒径を
測定することによって行う。個々のサンプルに対し、下
記切削条件にて切削評価を行った。 チップ形状 ＣＮＭＧ１２０４０８ 被削材 ＳＵＳ（ステンレス）３０４ 切削速度 Ｖ＝２００ｍ／ｍｉｎ 送り ｆ＝０．３ｍｍ／ｒｅｖ 切込み ｄ＝２ｍｍ 切削油 有り（水溶性） 切削時間 １パス当り１２秒を２５回繰り返し（５分） また、この試験では硬質被膜の耐摩耗性の評価としてフ
ランク摩耗を測定するとともに、母材との密着性（耐剥
離性能）および被膜の耐欠損性（耐衝撃性能）について
の観察評価を行った。The crystal grain size was controlled by the gas flow ratio during the Al 2 O 3 layer formation, the film formation temperature, the additive gas and the like. The measurement of the average crystal grain size of the Al 2 O 3 layer here is performed by measuring the crystal grain size that can be seen within a certain visual field in the coating cross section photographed by a scanning electron microscope or the etched photograph after polishing. . Each sample was evaluated for cutting under the following cutting conditions. Chip shape CNMG120408 Work material SUS (stainless steel) 304 Cutting speed V = 200 m / min Feed f = 0.3 mm / rev Depth of cut d = 2 mm Cutting oil Yes (water-soluble) Cutting time Repeat 12 seconds per pass 25 times (5 In addition, in this test, the flank wear was measured as an evaluation of the wear resistance of the hard coating, and the observation and evaluation of the adhesion to the base material (peeling resistance) and the fracture resistance (impact resistance) of the coating were performed. went.
【００２９】これらの結果を上記表１および２に示す。The results are shown in Tables 1 and 2 above.
【００３０】表１からも分かるように試料Ｎｏ．１、２
および３の本発明品は耐摩耗性を保持すると同時に耐剥
離性・耐衝撃性に優れていることが分かる。なお、上記
条件の切削においてフランク摩耗が０．２５ｍｍ以下で
ある場合に実用的な耐摩耗性を有していると判断した。As can be seen from Table 1, the sample No. One, two
It can be seen that the products of the present invention of Nos. 3 and 3 retain the abrasion resistance and at the same time have excellent peeling resistance and impact resistance. When the flank wear was 0.25 mm or less in the cutting under the above conditions, it was determined that the material had practical wear resistance.
【００３１】一方、総膜厚が１３μmと厚い試料Ｎｏ.４
の比較例は耐摩耗性には優れるものの、ＴｉＮ層の厚み
をＡｌ2Ｏ3層よりも大としたにもかかわらず、耐剥離性
・耐衝撃性ともに低下する。また、母材に接する下地Ｔ
ｉＮ膜がＡｌ2Ｏ3層よりも薄い膜構成とした試料Ｎｏ．
５の比較例では膜厚が１０μm以下であるにもかかわら
ず、膜の剥離が見られた。On the other hand, Sample No. 4 having a thick total film thickness of 13 μm
Although Comparative Example 2 is excellent in abrasion resistance, both the peeling resistance and the impact resistance are reduced even though the thickness of the TiN layer is larger than that of the Al 2 O 3 layer. Also, the base material T in contact with the base material
Sample No. 1 in which the iN film was thinner than the Al 2 O 3 layer.
In Comparative Example 5, peeling of the film was observed even though the film thickness was 10 μm or less.
【００３２】また、表２に示すように試料Ｎｏ．１、
２、３、６および７の本発明品は耐剥離性・耐衝撃性に
優れていることが分かる。As shown in Table 2, the sample No. 1,
It can be seen that 2, 3, 6 and 7 of the present invention are excellent in peeling resistance and impact resistance.
【００３３】ただし、試料Ｎｏ．１、２および３のよう
に硬質被膜の表面粗さの最大高さ（Ｒｙ）を5μｍに、
Ａｌ2Ｏ3層の結晶粒径が０．１乃至３．０μｍの範囲内
に制御したものは、上記表面粗さの最大高さ（Ｒｙ）が
５μｍより大きい試料Ｎｏ．７やＡｌ2Ｏ3層の結晶粒径
が３μｍより大きい試料Ｎｏ．６および７に比べて耐摩
耗性(フランク摩耗量)が大きく向上している。However, the sample No. The maximum height (Ry) of the surface roughness of the hard coating is set to 5 μm as in 1, 2, and 3,
In the case where the crystal grain size of the Al 2 O 3 layer was controlled in the range of 0.1 to 3.0 μm, the sample No. having the maximum surface roughness (Ry) of more than 5 μm was used. Sample No. 7 or the sample No. 7 in which the crystal grain size of the Al 2 O 3 layer is larger than 3 μm. The wear resistance (flank wear amount) is greatly improved as compared with 6 and 7.
【００３４】[0034]
【発明の効果】以上に記したように本発明の切削工具
は、超硬合金基体表面に、母材に接する下地層としてＴ
ｉＮ層さらに該ＴｉＮ層より外側にＡｌ2Ｏ3層を形成
し、この際、複層硬質被膜の厚みを１〜１０μｍに設定
において、該ＴｉＮ層をＡｌ2Ｏ3層よりも厚く設けるこ
とにより耐衝撃性・耐剥離性に優れた被覆超硬合金を得
ることができる。As described above, according to the cutting tool of the present invention, as a base layer in contact with the base metal,
An iN layer and an Al 2 O 3 layer are further formed outside the TiN layer. At this time, by setting the thickness of the multilayer hard coating to 1 to 10 μm, the TiN layer is provided to be thicker than the Al 2 O 3 layer. A coated cemented carbide having excellent impact resistance and peeling resistance can be obtained.
【００３５】また、これに加えて硬質被膜の表面粗さお
よびＡｌ2Ｏ3層の粒径を制御することにより、耐衝撃性
・耐剥離性を損なうことなく硬質被膜本来の効果である
耐摩耗性を向上させることができる。In addition, by controlling the surface roughness of the hard coating and the particle diameter of the Al 2 O 3 layer, the wear resistance, which is the original effect of the hard coating, can be obtained without impairing the impact resistance and peeling resistance. Performance can be improved.
Claims (2)
６ａ族元素の炭化物、窒化物、炭窒化物の群から選ばれ
る少なくとも１種の硬質相成分と、鉄族元素の少なくと
も１種からなる結合相から構成される超硬合金母材の表
面に硬質被膜を形成してなる切削工具であって、前記硬
質被膜は少なくとも前記母材と接するＴｉＮ層と該Ｔｉ
Ｎ層より外側にＡｌ2Ｏ3層を被覆した、膜厚が１乃至１
０μｍの複層で構成されるとともに、前記母材と接する
ＴｉＮ層の厚みが前記Ａｌ2Ｏ3層よりも大であることを
特徴とする切削工具。1. A periodic table 4a, 5a,
The surface of a cemented carbide base material composed of at least one hard phase component selected from the group consisting of carbides, nitrides and carbonitrides of Group 6a elements and a binder phase composed of at least one type of iron group element A cutting tool having a coating formed thereon, wherein the hard coating comprises at least a TiN layer in contact with the base material and the TiN layer.
An Al 2 O 3 layer is coated outside the N layer, and the film thickness is 1 to 1
A cutting tool comprising a plurality of layers having a thickness of 0 μm, wherein a thickness of a TiN layer in contact with the base material is larger than that of the Al 2 O 3 layer.
ｙ)が５μｍ以下であり、かつ、前記Ａｌ2Ｏ3層の結晶
粒径が０．１乃至３．０μｍであることを特徴とする請
求項１記載の切削工具。2. The maximum height (R) of the surface roughness of the hard coating.
2. The cutting tool according to claim 1, wherein y) is 5 μm or less, and a crystal grain size of the Al 2 O 3 layer is 0.1 to 3.0 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000329631A JP2002137103A (en) | 2000-10-27 | 2000-10-27 | Cutting tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000329631A JP2002137103A (en) | 2000-10-27 | 2000-10-27 | Cutting tool |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2002137103A true JP2002137103A (en) | 2002-05-14 |
Family
ID=18806274
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2000329631A Withdrawn JP2002137103A (en) | 2000-10-27 | 2000-10-27 | Cutting tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2002137103A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004223711A (en) * | 2003-01-24 | 2004-08-12 | Sandvik Ab | Cutting tool insert |
| JP5414883B2 (en) * | 2010-02-24 | 2014-02-12 | 京セラ株式会社 | Cutting tools |
-
2000
- 2000-10-27 JP JP2000329631A patent/JP2002137103A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004223711A (en) * | 2003-01-24 | 2004-08-12 | Sandvik Ab | Cutting tool insert |
| JP5414883B2 (en) * | 2010-02-24 | 2014-02-12 | 京セラ株式会社 | Cutting tools |
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