JP4569981B2 - Hard coating tool - Google Patents
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- JP4569981B2 JP4569981B2 JP28866499A JP28866499A JP4569981B2 JP 4569981 B2 JP4569981 B2 JP 4569981B2 JP 28866499 A JP28866499 A JP 28866499A JP 28866499 A JP28866499 A JP 28866499A JP 4569981 B2 JP4569981 B2 JP 4569981B2
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
- C23C28/044—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material coatings specially adapted for cutting tools or wear applications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/40—Coatings including alternating layers following a pattern, a periodic or defined repetition
- C23C28/42—Coatings including alternating layers following a pattern, a periodic or defined repetition characterized by the composition of the alternating layers
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- Engineering & Computer Science (AREA)
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
Description
【０００１】
【発明が属する技術分野】
本発明は、金属材料等の切削加工に使用される硬質皮膜被覆工具に関するものである。
【０００２】
【従来の技術】
従来はＴｉＮ、ＴｉＣＮ等を被覆した切削工具が汎用的かつ一般的であった。ＴｉＮは比較的耐酸化性に優れるため、切削時の発熱によって生じる工具のすくい面摩耗に対して、優れた耐摩耗性を示すだけでなく、基体との密着性も良好であることが特長である。また、ＴｉＣＮは、ＴｉＮに比べ高硬度かつ被加工物から排出される切り粉との接触抵抗が低いため工具表面の発熱が抑制される。このことから、被削材との機械的な擦り摩耗によって工具逃げ面に生じるフランク摩耗が抑制することができる。しかしながら、金属加工の高能率化を目的とした切削速度の高速化傾向に対し、上記硬質皮膜では、十分な耐酸化性、耐摩耗性を示さなくなった。この様な背景から、皮膜の耐酸化性、耐摩耗性をより向上させる研究がなされ、その結果、特開平８−１７０１６７号に代表されるＴｉＡｌＮ皮膜およびＴｉＡｌＳｉＣＮ皮膜が開発され切削工具に適用されている。
【０００３】
【発明が解決しようとする課題】
ＴｉＡｌＮ皮膜は、その皮膜中に含有するＴｉとＡｌの成分比率またはＳｉやＣの皮膜中の含有量により異なるものの、概略２３００〜２８００のビッカース硬さを有すだけではなく、耐酸化性が、前記ＴｉＮ、ＴｉＣＮに比べ著しく優れるため、刃先が高温に達する切削条件下においては、切削工具の性能をめざましく向上させる。また、ＴｉＡｌＳｉＣＮ皮膜は、ＴｉＡｌＮ皮膜よりもさらに耐酸化性を向上させようとＳｉを添加させたものである。しかしながら、近年では切削速度が更に高速化する傾向に加え、従来使用されていた湿式での切削加工が環境問題上重要視されるなかで、乾式での切削加工が注目され、切削工具の使用環境はますます苛酷なものとなってきている。
【０００４】
本発明者等の研究によれば、大気中におけるＴｉＡｌＮ皮膜の酸化開始温度は、ＴｉＮの４５０℃に対し、Ａｌの添加量に依存して７５０〜９００℃に向上する。しかしながら、前述の乾式高速切削加工においては、使用する工具の刃先温度が９００℃以上の高温に達するため、前記ＴｉＡｌＮ皮膜では、十分な工具寿命が得られないのが現状である。
【０００５】
本発明はこうした事情に鑑みなされたものであって、従来のＴｉＡｌＮ皮膜、もしくはＴｉＡｌＳｉＣＮ皮膜の耐摩耗性ならびに密着性を犠牲にすること無く更に耐酸化性を改善し、切削加工の乾式化、高速化に対応する硬質皮膜被覆工具を提供することが目的である。
【０００６】
【課題を解決するための手段】
本発明者等は、硬質皮膜の耐酸化性、耐摩耗性、母材との密着性に及ぼす、様々な元素との影響および皮膜の最適な層構造について鋭意研究を重ねた結果、金属成分が、Ｔｉを含まず、ＳｉとＡｌで構成される窒化物、炭窒化物、酸窒化物、酸炭窒化物のいずれかである酸化保護膜であるａ層と、金属成分がＡｌとＴｉで構成される窒化物、炭窒化物、酸窒化物、酸炭窒化物のいずれかである耐摩耗性皮膜であるｂ層とを、物理蒸着法で、それぞれ２層以上交互に積層被覆し、該ａ層は、該ＳｉとＡｌの合金製ターゲットを用い、且つ、最表層に被覆したことで、乾式の高速切削加工において、切削工具の性能が極めて良好となることを発見し本発明に到達した。
【０００７】
【発明の実施の形態】
はじめに請求項１記載のａ層に関して、その構成要件について詳しく述べる。
一般にＴｉＡｌＮ皮膜は、大気中で酸化テストを行う（特開平１１−１３１２１６号公報）と、皮膜表面近傍のＡｌが最表面に向かって外向拡散し、Ａｌ２Ｏ３層を形成する。この現象によりその後の皮膜内への酸素の進入が抑制される。本発明者らの研究によれば、このことが耐酸化性向上の理由と考えられるが、この時、最表層に形成されるＡｌ２Ｏ３層直下には、Ａｌを含有しない非常にポーラスなＴｉ酸化物が形成する。静的な酸化テストにおいては、最表面に形成されたＡｌ２Ｏ３層が、酸化の進行である酸素の内向拡散に対し、酸化保護膜として機能するものの、動的な切削においては、最表面のアルミナ層は、その直下のポーラスなＴｉ酸化物層より容易に剥離してしまい、酸化の進行に対し十分な効果を発揮しない。また、ＴｉＡｌＳｉＣＮ膜についても従来のＴｉＡｌＮ膜にＳｉを添加させることで耐酸化性を若干良好にさせるが、前述同様、酸化物に対する生成自由エネルギーの差から表面の酸化保護膜のＡｌ２Ｏ３層直下にポーラスなＴｉの酸化物を形成してしまい、結果、切削中の皮膜剥離をもたらす。
【０００８】
しかしながら、ＳｉとＡｌの合金製ターゲットから構成される請求項１記載の窒化物等は、皮膜自体の耐酸化性が、従来のＴｉとＡｌの窒化物よりも優れることを見出した。本発明者等は、各種元素の酸化物に対する自由生成エネルギーの観点から鋭意研究を重ねた結果、本発明硬質皮膜の酸化機構は、まず最表層にＡｌ２Ｏ３層を形成し、Ａｌ２Ｏ３層直下には非常に緻密なＳｉＯ層が形成される機構をもつことを発見した。本発明者等の研究によれば、Ａｌ２Ｏ３層直下の緻密なＳｉＯ層の形成により、動的な切削における上記記載のＴｉとＡｌの窒化物等のときに見られた剥離現象がなくなり、最表層のＡｌ２Ｏ３層が酸化の進行、いわば酸素の内向拡散に対し十分に効果を発揮することを確認した。このように、従来の皮膜に対し著しく耐酸化性が向上し切削加工中の皮膜剥離現象がなくなるＳｉとＡｌの合金製ターゲットから構成される窒化物等は皮膜中のＳｉ含有量が金属成分のみの原子％で８％越え８５％以下に調整することが重要である。Ｓｉ量を設定した理由については、その量が１５原子％以下では、皮膜の結晶形態がウルツ鉱型となり、優れた耐酸化性は得られても、皮膜自身が軟質化するため十分に満足のいく耐摩耗性を発揮することができない。また、８５原子％を越えると、非常に高硬度な皮膜が得られる反面、皮膜の残留圧縮応力が大きくなり密着性を阻害し皮膜剥離の因子となるからである。
【０００９】
上記ａ層は、静的および動的条件下において優れた耐酸化性を有すものの、皮膜自身がもつ残留圧縮応力が大きいため母材との密着性においては十分でない。そのため、基体表面直上には、密着性、耐摩耗性、耐酸化性等をバランス良く適度に有す皮膜、ＴｉＡｌ系窒化物等である請求項中に記載のｂ層を被覆することが好ましい。ＴｉＡｌ系窒化物等の皮膜であるｂ層におけるＡｌの役割は、皮膜の耐摩耗性および耐酸化性を向上させることである。そのため、密着性、耐摩耗性、耐酸化性をバランス良く得るためには、好ましくはｂ層のＡｌ含有量を、皮膜の金属成分のみの原子％で、３０％越え７５％以下に調整することが重要である。ｂ層における好ましいＡｌの含有量を設定した理由については、その量が３０原子％を越えたときに耐酸化性が著しく向上し始めるためである。また、７５原子％以下に調整する理由は、耐酸化性が向上しても、皮膜硬度が著しく低下し耐摩耗性が劣化してしまうためである。
【００１０】
以上のように本発明においては、基体との密着性、皮膜自体の耐摩耗性および耐酸化性をバランス良く有すｂ層を基体表面直上に被覆し、その上に著しく耐酸化性に優れるａ層を被覆することが極めて重要であり、その結果、乾式の高速切削に対応する切削工具を得ることが可能となる。
また、基体表面直上にｂ層を被覆した後、ａ層ならびにｂ層をそれぞれ交互に積層した多層皮膜によっても同様の効果が得られる。また、各層は必要に応じて窒化物、炭窒化物、酸窒化物、酸炭窒化物のいずれかに調整でき、それらを被覆した工具についても同様の効果が得られる。
【００１１】
本発明の物理蒸着法は、被覆基体への熱影響、工具の疲労強度、皮膜の密着性等を考慮した場合、比較的低温で被覆でき、被覆した皮膜に圧縮応力が残留するアーク放電方式イオンプレーティングもしくはスパッタリングが望ましい。以下、本発明を実施例に基づいて説明する。
【００１２】
【実施例】
（実施例１）
小型アークイオンプレーティング装置を用い、金属成分の蒸発源である各種合金製ターゲット、ならびに反応ガスであるＮ２ガス、ＣＨ４ガス、Ａｒ／Ｏ２混合ガスから目的の皮膜が得られるものを選択し、被覆基体温度４００℃、反応ガス圧力３．０Ｐａの条件下にて、被覆基体である超硬合金製エンドミルおよび超硬合金製インサートに−１５０Ｖの電位を印加させ、全皮膜の厚みが４μｍとなるように被覆を行った。
得られた硬質皮膜被覆エンドミルおよびインサートを用い、次に示す乾式の高速切削条件にて、刃先の欠けないしは摩耗等により工具が切削不能となるまで加工を行い、その時の切削長を工具寿命とした。表１に本発例および比較例に関する硬質皮膜の詳細およびその切削結果を示す。
【００１３】
（エンドミル切削条件）
工具 ：超硬合金製６枚刃エンドミル
外径 ：８ｍｍ
切削方法 ：側面切削（ダウンカット）
被削材 ：ＳＫＤ１１（ＨＲＣ６０）
切り込み ：Ａｄ１２ｍｍ×Ｒｄ０．４ｍｍ
切削速度 ：１５０ｍ／ｍｉｎ
１刃送り量：０．０３ｍｍ／刃
切削油 ：なし（エアーブロー）
【００１４】
（インサート切削条件）
工具 ：正面フライス
インサート形状：ＳＥＥ４２ＴＮ特殊形状
切削方法 ：センターカット方式
被削材形状：巾１００ｍｍ×長さ２５０ｍｍ
被削材 ：ＳＫＤ６１（ＨＲＣ４５）
切り込み ：２．０ｍｍ
切削速度 ：１６０ｍ／ｍｉｎ
１刃送り量：０．１５ｍｍ／刃
切削油 ：なし
【００１５】
【表１】
表１より、本発明例１〜１５は、従来例と比べて、工具寿命が著しく向上しており、乾式高速切削加工に十分対応できることがわかる。特に、ＳｉおよびＡｌで構成されるうちのＳｉの含有量を皮膜の金属成分のみで８原子％越え、８５％以内の皮膜は優れた工具性能を示した。これは、請求項記載の皮膜構成についてバランス良く被覆するために鋭意研究を重ねた結果である。更に、例えば本発明例１の様な４層でも、本発明例１０の様な積層（８０層）においても、優れた切削性能を示す。また０．０４ミクロンの薄いａ層を積層させた本発明例１０では、ａ層が切削中の酸化の進行を止めるバリヤー層となり、ｂ層のみの単層膜、例えば従来例２３に比較して約３倍の寿命を示した。また、本発明皮膜の成膜に使用した導入ガスについても同時に検討を行った結果、著しく優れた耐酸化性を保つためには、請求項記載の元素に対しての窒化物、酸化物、酸窒化物として被覆されることが望ましいが、工具の発熱ならびに被削材との摩擦を考慮した場合、成膜時に上記記載膜を製造する上で必要となる窒素、酸素を含むガスの他に本発明例４等のように炭素を含むガスを導入し請求項記載の元素の炭窒化物、炭酸窒化物を被覆しても十分に優れた工具性能を発揮する。更には、従来例１６、ＴｉＡｌＳｉＣＮ膜の様にＴｉとＳｉを含有する皮膜では、切削中の酸化により酸化保護膜のＡｌ２Ｏ３層直下にポーラスなＴｉの酸化物を形成し切削中の皮膜剥離が生じたため本発明例に比較しエンドミルでは１／４程度の切削長さで寿命となった。
【００１７】
【発明の効果】
以上の如く、本発明の硬質皮膜被覆工具は、従来の被覆工具に比べ優れた耐酸化性、耐摩耗性を有すことから、乾式高速切削加工において著しく長い工具寿命が得られ、切削加工における生産性の向上に極めて有効である。[0001]
[Technical field to which the invention belongs]
The present invention relates to a hard film-coated tool used for cutting a metal material or the like.
[0002]
[Prior art]
Conventionally, a cutting tool coated with TiN, TiCN or the like has been widely used. TiN is relatively excellent in oxidation resistance, so it not only exhibits excellent wear resistance against tool rake face wear caused by heat generated during cutting, but also has good adhesion to the substrate. is there. Further, TiCN has higher hardness than TiN and has low contact resistance with the chips discharged from the workpiece, so that heat generation on the tool surface is suppressed. From this, it is possible to suppress flank wear that occurs on the tool flank due to mechanical rubbing wear with the work material. However, the hard coating does not exhibit sufficient oxidation resistance and wear resistance against the tendency to increase the cutting speed for the purpose of improving the efficiency of metal working. From such a background, studies have been made to further improve the oxidation resistance and wear resistance of the coating. As a result, TiAlN coating and TiAlSiCN coating typified by JP-A-8-170167 have been developed and applied to cutting tools. Yes.
[0003]
[Problems to be solved by the invention]
Although the TiAlN film differs depending on the component ratio of Ti and Al contained in the film or the content in the film of Si or C, it not only has a Vickers hardness of approximately 2300-2800, but also has oxidation resistance, Since it is remarkably superior to TiN and TiCN, the cutting tool performance is remarkably improved under cutting conditions where the cutting edge reaches a high temperature. Further, the TiAlSiCN film is obtained by adding Si so as to further improve the oxidation resistance as compared with the TiAlN film. However, in recent years, in addition to the tendency to further increase the cutting speed, wet cutting, which has been used in the past, is regarded as an important environmental issue, and dry cutting is attracting attention, and the usage environment of cutting tools Has become increasingly harsh.
[0004]
According to the study by the present inventors, the oxidation start temperature of the TiAlN film in the atmosphere is improved to 750 to 900 ° C. depending on the amount of Al added to 450 ° C. of TiN. However, in the above-described dry high-speed cutting, the cutting edge temperature of the tool to be used reaches a high temperature of 900 ° C. or higher, so that the sufficient tool life cannot be obtained with the TiAlN coating.
[0005]
The present invention has been made in view of such circumstances, and further improves the oxidation resistance without sacrificing the wear resistance and adhesion of the conventional TiAlN coating or TiAlSiCN coating, making the cutting process dry and high-speed. An object of the present invention is to provide a hard film-coated tool corresponding to the conversion.
[0006]
[Means for Solving the Problems]
The present inventors have conducted extensive research on the influence of various elements on the oxidation resistance, wear resistance, and adhesion to the base material of the hard film and the optimum layer structure of the film. A layer which is an oxidation protective film which is any of nitride, carbonitride, oxynitride and oxycarbonitride which does not contain Ti and is composed of Si and Al, and a metal component is composed of Al and Ti The layer b, which is a wear-resistant film that is any one of nitride, carbonitride, oxynitride, and oxycarbonitride, is laminated and coated alternately by two or more layers by physical vapor deposition, It was found that the performance of the cutting tool was extremely good in dry high-speed cutting by using the Si-Al alloy target and covering the outermost layer with the layer, and reached the present invention.
[000 7 ]
DETAILED DESCRIPTION OF THE INVENTION
First, the constituent requirements of the a layer according to claim 1 will be described in detail.
In general, when a TiAlN film is subjected to an oxidation test in the atmosphere (Japanese Patent Laid-Open No. 11-131216), Al in the vicinity of the film surface diffuses outward toward the outermost surface to form an Al 2 O 3 layer. This phenomenon suppresses the subsequent entry of oxygen into the film. According to the study by the present inventors, this is considered to be the reason for improving the oxidation resistance, but at this time, the Al 2 O 3 layer formed in the outermost layer is very porous not containing Al. Ti oxide is formed. In the static oxidation test, the Al 2 O 3 layer formed on the outermost surface functions as an oxidation protective film against inward diffusion of oxygen, which is the progress of oxidation, but in dynamic cutting, the outermost surface This alumina layer peels off more easily than the porous Ti oxide layer immediately below, and does not exhibit a sufficient effect on the progress of oxidation. Further, the TiAlSiCN film also has a slightly improved oxidation resistance by adding Si to the conventional TiAlN film. However, as described above, the Al 2 O 3 layer of the surface oxidation protective film is formed due to the difference in free energy of formation relative to the oxide. Porous Ti oxide is formed immediately below, resulting in film peeling during cutting.
[0008]
However, it has been found that the nitride according to claim 1 composed of an alloy target of Si and Al is superior in oxidation resistance of the coating itself to the conventional Ti and Al nitride. The present inventors, as a result of extensive research in view of the free energy of formation for oxides of various elements, the oxidation mechanism of the present invention the hard coating, the the Al 2 O 3 layer was formed first in the outermost layer, Al 2 O It has been discovered that a very dense SiO layer is formed immediately below the three layers. According to the study by the present inventors, the formation of a dense SiO layer immediately below the Al 2 O 3 layer eliminates the peeling phenomenon seen in the above-described Ti and Al nitrides in dynamic cutting. It was confirmed that the outermost Al 2 O 3 layer exhibited a sufficient effect on the progress of oxidation, in other words, inward diffusion of oxygen. In this way, nitrides composed of an alloy target of Si and Al that have significantly improved oxidation resistance compared to conventional films and eliminate the film peeling phenomenon during cutting work, the Si content in the film is only the metal component It is important to adjust the atomic% to 8% to 85% or less. Regarding the reason for setting the Si amount, if the amount is 15 atomic% or less, the crystal form of the film becomes a wurtzite type, and even though excellent oxidation resistance can be obtained, the film itself becomes soft, so that it is sufficiently satisfactory. It is not possible to demonstrate the high wear resistance. On the other hand, if it exceeds 85 atomic%, a very high hardness film can be obtained, but the residual compressive stress of the film becomes large and the adhesion is hindered, resulting in a film peeling factor.
[00 09 ]
Although the layer a has excellent oxidation resistance under static and dynamic conditions, the layer itself has a large residual compressive stress, so that the adhesion with the base material is not sufficient. For this reason, it is preferable to coat the b layer according to the claims, which is a film, TiAl-based nitride, or the like having an appropriate balance of adhesion, wear resistance, oxidation resistance, etc., just above the substrate surface. The role of Al in the b layer which is a film such as a TiAl-based nitride is to improve the wear resistance and oxidation resistance of the film. Therefore, in order to obtain a good balance of adhesion, wear resistance, and oxidation resistance, the Al content of the b layer is preferably adjusted to more than 30% and 75% or less in terms of atomic% of only the metal component of the film. is important. The reason why the preferable Al content in the b layer is set is that the oxidation resistance starts to be remarkably improved when the amount exceeds 30 atomic%. Moreover, the reason for adjusting to 75 atomic% or less is that even if the oxidation resistance is improved, the film hardness is remarkably lowered and the wear resistance is deteriorated.
[00 10 ]
As described above, in the present invention, the b layer having a good balance between adhesion to the substrate, wear resistance and oxidation resistance of the coating itself is coated directly on the substrate surface, and on the surface thereof, remarkably excellent oxidation resistance is obtained. It is very important to coat the layer, and as a result, it is possible to obtain a cutting tool corresponding to dry high-speed cutting.
A similar effect can be obtained by a multilayer coating in which the a layer and the b layer are alternately laminated after the b layer is coated directly on the substrate surface. Moreover, each layer can be adjusted to any of nitride, carbonitride, oxynitride, and oxycarbonitride as necessary, and the same effect can be obtained for a tool covering these layers.
[0011]
The physical vapor deposition method of the present invention is capable of coating at a relatively low temperature in consideration of the thermal effect on the coated substrate, tool fatigue strength, film adhesion, etc. Plating or sputtering is desirable. Hereinafter, the present invention will be described based on examples.
[0012]
【Example】
Example 1
Using a small arc ion plating device, select from various alloy targets that are the evaporation source of metal components, and those that can obtain the desired film from the reaction gas N 2 gas, CH 4 gas, Ar / O 2 mixed gas Then, under the conditions of the coated substrate temperature of 400 ° C. and the reaction gas pressure of 3.0 Pa, a potential of −150 V was applied to the cemented carbide end mill and cemented carbide insert, which were the coated substrate, and the total coating thickness was 4 μm. It coat | covered so that it might become.
Using the obtained hard coating coated end mill and insert, under the following dry high-speed cutting conditions, processing was performed until the tool could not be cut due to chipping or abrasion of the blade edge, and the cutting length at that time was defined as the tool life . Table 1 shows the details of the hard coating and the cutting results for the present example and the comparative example.
[00 13 ]
(End mill cutting conditions)
Tool: Cemented carbide 6-flute end mill Outer diameter : 8mm
Cutting method: Side cut (down cut)
Work material: SKD11 (HRC60)
Cut: Ad12mm × Rd0 . 4mm
Cutting speed: 150 m / min
1-blade feed amount: 0 . 03mm / blade Cutting oil: None (Air blow)
[00 14 ]
(Insert cutting conditions)
Tool: Face mill Insert shape: SEE42TN special shape Cutting method: Center cut method Work material shape: Width 100mm x Length 250mm
Work material: SKD61 (HRC45)
Incision: 2 . 0mm
Cutting speed: 160 m / min
1-blade feed amount: 0 . 15 mm / blade Cutting oil: None [0015]
[Table 1]
From Table 1, it can be seen that Examples 1 to 15 of the present invention have significantly improved tool life as compared with the conventional examples, and can sufficiently cope with dry high-speed cutting. In particular, the content of Si out of Si and Al exceeded 8 atomic% with only the metal component of the film, and the film within 85% showed excellent tool performance. This is the result of extensive research to cover the coating composition described in the claims in a well-balanced manner. Further, for example, even in a four- layer structure as in Invention Example 1 and a laminate (80 layers) as in Invention Example 10, excellent cutting performance is exhibited. Further, in Example 10 of the present invention in which a thin a layer of 0.04 microns was laminated, the a layer became a barrier layer that stopped the progress of oxidation during cutting, and compared with a single layer film of only b layer, for example, Conventional Example 23 The lifetime was about 3 times. In addition, as a result of simultaneously examining the introduced gas used to form the film of the present invention, in order to maintain remarkably excellent oxidation resistance, nitrides, oxides, and acids for the elements described in the claims are used. It is desirable to be coated as a nitride, but considering the heat generation of the tool and the friction with the work material, in addition to the gas containing nitrogen and oxygen necessary for producing the above described film at the time of film formation, Even when carbon-containing gas is introduced as in Invention Example 4 and coated with the carbonitrides and carbonitrides of the elements described in the claims, sufficiently excellent tool performance is exhibited. Further, in the case of a film containing Ti and Si like the conventional example 16 TiAlSiCN film, a porous Ti oxide is formed immediately under the Al 2 O 3 layer of the oxidation protective film by oxidation during cutting, and the film being cut. Since peeling occurred, the end mill had a life with a cutting length of about 1/4 compared to the example of the present invention.
[00 17 ]
【The invention's effect】
As described above, since the hard coating coated tool of the present invention has superior oxidation resistance and wear resistance compared to conventional coated tools, a significantly long tool life can be obtained in dry high-speed cutting processing. It is extremely effective in improving productivity.
Claims (1)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28866499A JP4569981B2 (en) | 1999-10-08 | 1999-10-08 | Hard coating tool |
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| Application Number | Priority Date | Filing Date | Title |
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| JP28866499A JP4569981B2 (en) | 1999-10-08 | 1999-10-08 | Hard coating tool |
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| JP2001105205A JP2001105205A (en) | 2001-04-17 |
| JP4569981B2 true JP4569981B2 (en) | 2010-10-27 |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4340441B2 (en) * | 2003-01-15 | 2009-10-07 | 住友電工ハードメタル株式会社 | Wear resistant parts |
| JP5180221B2 (en) * | 2007-09-20 | 2013-04-10 | オーエスジー株式会社 | Hard laminate coating, hard laminate coating tool, and method for forming coating |
| DE102016108734B4 (en) * | 2016-05-11 | 2023-09-07 | Kennametal Inc. | Coated body and method of making the body |
| CN106591784B (en) * | 2016-11-12 | 2019-07-09 | 常州大学 | A kind of method that ion plating prepares TiAlSiCN coating |
| RU2720003C1 (en) * | 2019-09-16 | 2020-04-23 | федеральное государственное бюджетное образовательное учреждение высшего образования "Ульяновский государственный технический университет" | Method of producing multilayer coating for cutting tools |
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