JP5743585B2 - Cutting tools - Google Patents
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- JP5743585B2 JP5743585B2 JP2011028719A JP2011028719A JP5743585B2 JP 5743585 B2 JP5743585 B2 JP 5743585B2 JP 2011028719 A JP2011028719 A JP 2011028719A JP 2011028719 A JP2011028719 A JP 2011028719A JP 5743585 B2 JP5743585 B2 JP 5743585B2
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Description
本発明は切削工具に関し、特に耐塑性変形性に優れた超硬合金からなる切削工具に関する。 The present invention relates to a cutting tool, and more particularly to a cutting tool made of a cemented carbide excellent in plastic deformation resistance.
従来から金属の切削加工に広く用いられている超硬合金は、ＷＣを主体とする硬質相と、Ｃｏ等の鉄族金属の結合相からなるＷＣ−Ｃｏ系合金に周期表第４、５、６族金属の炭化物、窒化物、炭窒化物等の固溶相を分散せしめた系が知られている。この超硬合金は、切削工具として、主に炭素鋼、合金鋼等の切削加工に利用されているが、高速・強断続加工に対応する切削工具が要求されている。 Conventionally, cemented carbide widely used for metal cutting is a WC-Co alloy composed of a hard phase mainly composed of WC and a binding phase of an iron group metal such as Co. A system in which a solid solution phase such as a carbide, nitride, carbonitride or the like of a Group 6 metal is dispersed is known. Although this cemented carbide is mainly used for cutting of carbon steel, alloy steel, etc. as a cutting tool, a cutting tool corresponding to high-speed and strong interrupted processing is required.
例えば、特許文献１では、焼成条件を工夫して、ＴａまたはＮｂを含有する斑点状析出物を１個以下にした超硬合金が開示されている。また、特許文献２では、Ｚｒが多い芯部と、ＴａおよびＮｂを含む外周部とからなるＢ１型固溶体を備えた超硬合金が開示されている。さらに、特許文献３では、Ｔｉを主成分とする硬質相とＺｒを主成分とする硬質相との２種類の固溶体相を分散させた超硬合金が開示されている。 For example, Patent Document 1 discloses a cemented carbide in which the firing conditions are devised to reduce the number of spotted precipitates containing Ta or Nb to one or less. Patent Document 2 discloses a cemented carbide including a B1-type solid solution composed of a core portion rich in Zr and an outer peripheral portion containing Ta and Nb. Further, Patent Document 3 discloses a cemented carbide in which two types of solid solution phases, a hard phase mainly composed of Ti and a hard phase mainly composed of Zr, are dispersed.
しかしながら、特許文献１に記載されているようにＢ１型固溶相が析出しない超硬合金の場合、高速加工の断続切削のような切刃が高温となりかつ強い衝撃を受ける切削加工では耐塑性変形性が不十分であり、切刃が変形して加工精度が低下したり、加工面が粗くなるという問題があった。 However, as described in Patent Document 1, in the case of a cemented carbide in which a B1 type solid solution phase does not precipitate, the plastic blade is deformed in a cutting process where the cutting edge is subjected to a high temperature and a strong impact such as intermittent cutting in high-speed processing. However, the cutting edge is deformed and machining accuracy is lowered, and the machining surface becomes rough.
また、特許文献２のようにＢ１型固溶相が有芯構造からなる超硬合金でも、高速・断続切削加工に要求される耐塑性変形性を満足するには不十分であった。 Further, even a cemented carbide having a B1 type solid solution phase having a cored structure as in Patent Document 2 is insufficient to satisfy the plastic deformation resistance required for high-speed / intermittent cutting.
さらに、特許文献３のようにＴｉを主成分とする硬質相とＺｒを主成分とする硬質相との２種類の硬質相（Ｂ１型固溶体相）を含む超硬合金でも、高速・断続の切削加工に要求される耐塑性変形性が十分であるとは言えなかった。そのため、切刃が高温になり衝撃を受ける切削のような高速・断続切削加工においては切刃が塑性変形し、塑性変形からの異常摩耗および膜剥離が生じて工具寿命が短くなるという問題があった。 Further, even in a cemented carbide containing two types of hard phases (B1 type solid solution phase) of a hard phase mainly composed of Ti and a hard phase mainly composed of Zr as in Patent Document 3, high-speed, intermittent cutting is performed. It could not be said that the plastic deformation resistance required for processing was sufficient. Therefore, in high-speed / intermittent cutting such as cutting where the cutting edge becomes hot and impacted, the cutting edge is plastically deformed, causing abnormal wear and film peeling from the plastic deformation, resulting in a short tool life. It was.
本発明の目的は、高速かつ断続切削加工によって発生する塑性変形を抑えて、優れた耐摩耗性、耐欠損性を発揮することができる切削工具を提供することにある。 An object of the present invention is to provide a cutting tool capable of exhibiting excellent wear resistance and fracture resistance by suppressing plastic deformation caused by high-speed and intermittent cutting.
本発明の切削工具は、ＷＣを８０〜９４質量％、Ｃｏを５〜１５質量％、Ｔｉを炭化物換算量で０.１〜５質量％、Ｎｂを炭化物換算量で０.１〜１０質量％、ＴｉおよびＮｂを除く周期表第４、５および６族金属の群から選ばれる少なくとも１種の炭化物（ＷＣを除く）を０〜１０質量％の割合で含有して、ＷＣ相と、Ｂ１型固溶相と、前記Ｃｏを主体とする結合相とからなり、かつ前記Ｂ１型固溶相は単一構造からなるとともに前記Ｔｉと前記Ｎｂの濃度が最高となる位置が異なる超硬合金からなる。 In the cutting tool of the present invention, WC is 80 to 94% by mass, Co is 5 to 15% by mass, Ti is 0.1 to 5% by mass in terms of carbide, and Nb is 0.1 to 10% by mass in terms of carbide. , Containing at least one carbide (excluding WC ) selected from the group of metals of Group 4, 5 and 6 of the periodic table excluding Ti and Nb in a proportion of 0 to 10% by mass, and B1 type It consists of a solid solution phase and a binder phase mainly composed of Co, and the B1-type solid solution phase is made of a cemented carbide having a single structure and different positions where the concentrations of Ti and Nb are highest. .
ここで、前記超硬合金の表面から５〜１０μｍの深さにわたって前記Ｂ１型固溶相が存在しない表面領域が存在するとともに、該表面領域よりも内側においては、前記Ｂ１型固溶相が５〜２０面積％の割合で存在してもよい。 Here, there is a surface region where the B1 type solid solution phase does not exist over a depth of 5 to 10 μm from the surface of the cemented carbide, and the B1 type solid solution phase is 5 inside the surface region. It may be present at a rate of ˜20 area%.
本発明の切削工具によれば、Ｂ１型固溶相中の組成がランダムに分布している構成からなるために、高温での応力やクラックの進展に対する変形や破壊の向きがランダムであり、総合的にＢ１型固溶相の高温での硬度と耐変形性をともに高めることができて、Ｂ１型固溶相がクラックの進展を抑制できるとともに超硬合金の変形を抑制できる結果、超硬合金の耐塑性変形性を向上できる。 According to the cutting tool of the present invention, since the composition in the B1 type solid solution phase is randomly distributed, the direction of deformation and fracture with respect to the stress and crack progress at high temperature is random, As a result, both the hardness and deformation resistance of the B1 type solid solution phase at a high temperature can be improved, and the B1 type solid solution phase can suppress the progress of cracks and the deformation of the cemented carbide. The plastic deformation resistance of can be improved.
本発明の切削工具を構成する超硬合金は、ＷＣ相、結合相、Ｂ１型固溶相から形成されている。そして、ＷＣを８０〜９４質量％、Ｃｏを５〜１５質量％、Ｔｉを炭化物換算量で０．１〜５質量％、Ｎｂを炭化物換算量で０．１〜１０質量％、ＴｉおよびＮｂを除く周期表第４、５および６族金属の群から選ばれる少なくとも１種の炭化物（ＷＣを除く）、窒化物および炭窒化物のうちの少なくとも１種を０〜１０質量％の割合で含有する。そして、この超硬合金は、ＷＣ相と、Ｂ１型固溶相と、前記Ｃｏを主体とする結合相とからなり、前記Ｂ１型固溶相は有芯構造ではなくて単一構造からなるとともに、前記Ｔｉと前記Ｎｂの濃度が最高となる位置が異なっている。 The cemented carbide constituting the cutting tool of the present invention is formed of a WC phase, a binder phase, and a B1 type solid solution phase. And WC is 80-94 mass%, Co is 5-15 mass%, Ti is 0.1-5 mass% in carbide conversion amount, Nb is 0.1-10 mass% in carbide conversion amount, Ti and Nb. Excluding at least one of carbides (excluding WC), nitrides and carbonitrides selected from the group of metals of Group 4, 5 and 6 of the periodic table excluding 0 to 10% by mass . The cemented carbide is composed of a WC phase, a B1 type solid solution phase, and a bonded phase mainly composed of Co. The B1 type solid solution phase is not a cored structure but a single structure. The positions where the concentrations of Ti and Nb are highest are different.
上記構成により、Ｂ１型固溶相中に各元素がランダムに分布しているために、高温での応力やクラックの進展に対する変形や破壊の向きがランダムであり、総合的にＢ１型固溶相の高温での硬度と耐変形性をともに高めることができて、Ｂ１型固溶相がクラックの進展を抑制できるとともに超硬合金の変形を抑制できる結果、超硬合金の耐塑性変形性を向上できる。 With the above configuration, since each element is randomly distributed in the B1 type solid solution phase, the direction of deformation and fracture with respect to the stress and crack progress at high temperature is random, and the B1 type solid solution phase is comprehensively obtained. The B1 type solid solution phase can suppress the progress of cracks and the deformation of the cemented carbide, thereby improving the plastic deformation resistance of the cemented carbide. it can.
すなわち、Ｂ１型固溶相中の金属元素の分布が均一である場合には、高温での応力やクラックの進展に対する変形や破壊が大きくて超硬合金の変形が大きくなる。また、有芯構造からなるＢ１型固溶相では、高温での応力やクラックの進展に対する変形や破壊の向きが一様であるために、総合的にＢ１型固溶相の高温での硬度と耐変形性が十分でなく、超硬合金の耐塑性変形性が不十分となる。 That is, when the distribution of the metal element in the B1-type solid solution phase is uniform, deformation and destruction with respect to stress and crack growth at high temperatures are large, and deformation of the cemented carbide becomes large. In addition, in the B1 type solid solution phase having a cored structure, since the direction of deformation and fracture with respect to the stress and crack progress at high temperature is uniform, the hardness at high temperature of the B1 type solid solution phase is comprehensively determined. The deformation resistance is not sufficient, and the plastic deformation resistance of the cemented carbide becomes insufficient.
ここで、前記超硬合金の表面から５〜１０μｍの深さにわたって前記Ｂ１型固溶相が存在しない表面領域が存在するとともに、該表面領域よりも内側においては、前記Ｂ１型固溶相が５〜２０面積％の割合で存在することが、高温における耐塑性変形性を最適化する上で望ましい。 Here, there is a surface region where the B1 type solid solution phase does not exist over a depth of 5 to 10 μm from the surface of the cemented carbide, and the B1 type solid solution phase is 5 inside the surface region. It is desirable to exist at a ratio of ˜20 area% in order to optimize the plastic deformation resistance at high temperature.
なお、ＴｉとＮｂの濃度が最高となる位置が異なるとは、オージェ分光分析（ＡＥＳ）にてＢ１型固溶体相の各元素のマッピングをとって、ＴｉとＮｂの濃度が最高となる位置の差がＢ１型固溶体相の最大径に対して１０％以上離れている状態を指す。
また、超硬合金のＢ１型固溶相について有芯構造であるか否かを確認するには、走査型電子顕微鏡（ＳＥＭ）の反射電子像（ＢＥＩ）で鏡面加工された超硬合金の断面組織を観察し、観察される各Ｂ１型固溶相について均一な色調であるかどうかを確認することにより有芯構造をなしているかどうかを確認できる。
In addition, the position where the concentration of Ti and Nb becomes the highest is different from the position where the concentration of Ti and Nb becomes the highest by mapping each element of the B1 type solid solution phase by Auger spectroscopic analysis (AES). Indicates a state of being separated by 10% or more with respect to the maximum diameter of the B1 type solid solution phase.
In addition, in order to confirm whether or not the B1 type solid solution phase of the cemented carbide has a cored structure, the cross section of the cemented carbide mirror-finished with a backscattered electron image (BEI) of a scanning electron microscope (SEM). By observing the structure and confirming whether or not the observed B1 type solid solution phase has a uniform color tone, it can be confirmed whether or not a cored structure is formed.
（製造方法）
上述した本発明の切削工具を構成する超硬合金の製造方法の一例について説明する。まず、ＷＣ（ＷＣ）粉末を８０〜９４質量％と、金属Ｃｏ（Ｃｏ）粉末を５〜１５質量％と、Ｂ１型固溶相を形成するための化合物粉末として、ＮｂＣ粉末を０．１〜１０質量％、ＴｉＣ粉末を０．１〜５質量％、他のＢ１型固溶相を形成するための化合物粉末を１０質量％以下の比率で調合する。このとき、Ｂ１型固溶相を形成するための化合物原料粉末であるＴｉＣ粉末の平均粒径を０．５〜２μｍ、ＮｂＣ粉末の平均粒径を０．５〜２μｍ、ＷＣ粉末の平均粒径を０．５〜１０μｍ、金属Ｃｏ粉末の平均粒径を１．０〜２．０μｍと調整するとともに、下記混合、焼成工程によって、本発明の切削工具を形成する超硬合金を作製することができる。
(Production method)
An example of the manufacturing method of the cemented carbide which comprises the cutting tool of this invention mentioned above is demonstrated. First, 80 to 94% by mass of WC (WC) powder, 5 to 15% by mass of metal Co (Co) powder, and 0.1 to NbC powder as a compound powder for forming a B1-type solid solution phase. 10% by mass, 0.1% by mass to 5% by mass of TiC powder, and other compound powders for forming a B1-type solid solution phase are prepared at a ratio of 10% by mass or less. At this time, the average particle diameter of the TiC powder, which is the compound raw material powder for forming the B1 type solid solution phase, is 0.5 to 2 μm, the average particle diameter of the NbC powder is 0.5 to 2 μm, and the average particle diameter of the WC powder. Is adjusted to 0.5 to 10 μm, and the average particle size of the metal Co powder is adjusted to 1.0 to 2.0 μm, and the cemented carbide forming the cutting tool of the present invention is manufactured by the following mixing and firing process. it can.
この調合した粉末に溶媒を加えて、所定時間混合・粉砕してスラリーとする。この際、ＮｂＣ粉末およびＴｉＣ粉末以外の原料を先行して５〜２０時間混合・粉砕した後、ＮｂＣ粉末およびＴｉＣ粉末を投入して０．５〜２時間混合・粉砕する。このスラリーにバインダを添加してさらに混合し、スプレードライヤー等を用いてスラリーを乾燥しながら混合粉末の造粒を行う。次に、造粒された顆粒を用いてプレス成形により切削工具形状に成形を行う。その後、焼成炉にて脱脂を行った後、焼成炉の温度を１３８０〜１４５０℃の焼成温度に上げて１〜１．５時間焼成して超硬合金を作製することができる。 A solvent is added to the prepared powder and mixed and pulverized for a predetermined time to form a slurry. At this time, raw materials other than NbC powder and TiC powder are mixed and pulverized for 5 to 20 hours in advance, and then NbC powder and TiC powder are added and mixed and pulverized for 0.5 to 2 hours. A binder is added to the slurry and further mixed, and the mixed powder is granulated while drying the slurry using a spray dryer or the like. Next, the granulated granules are molded into a cutting tool shape by press molding. Then, after degreasing in a firing furnace, the temperature of the firing furnace is raised to a firing temperature of 1380 to 1450 ° C. and fired for 1 to 1.5 hours, whereby a cemented carbide can be produced.
ここで、上記工程において、原料として用いるＮｂＣ粉末とＴｉＣ粉末の粉砕時間が２時間を超える場合、または焼成温度が１５００℃を超える場合には、Ｂ１型固溶体相中のＴｉ元素とＮｂ元素の最高濃度位置が一致する。 Here, in the above process, when the pulverization time of the NbC powder and TiC powder used as raw materials exceeds 2 hours, or when the firing temperature exceeds 1500 ° C., the highest of Ti element and Nb element in the B1 type solid solution phase Concentration positions match.
そして、作製された超硬合金について、所望によって超硬合金の表面を研磨加工したり、切刃部にホーニング加工を施したりする。さらに、所望によって、超硬合金の表面に化学気相蒸着（ＣＶＤ）法や、物理気相蒸着（ＰＶＤ）法によって、公知の硬質被覆層を成膜して切削工具としてもよい。特にＣＶＤ法によって成膜した場合には、超硬合金からなる基体に塑性変形が生じることがないので、硬質被覆層が超硬合金からなる基体の塑性変形量に追従できずに超硬合金と硬質被覆層との界面から剥離してしまうこともなく、耐摩耗性・耐欠損性とも優れるものとなる。 And about the produced cemented carbide alloy, the surface of a cemented carbide alloy is grind | polished as needed, or a honing process is given to a cutting blade part. Furthermore, if desired, a known hard coating layer may be formed on the surface of the cemented carbide by a chemical vapor deposition (CVD) method or a physical vapor deposition (PVD) method to form a cutting tool. In particular, when the film is formed by the CVD method, plastic deformation does not occur in the substrate made of cemented carbide, so the hard coating layer cannot follow the amount of plastic deformation of the substrate made of cemented carbide and It does not peel off from the interface with the hard coating layer, and is excellent in wear resistance and fracture resistance.
表１に示す平均粒径のＷＣ（ＷＣ）粉末、金属Ｃｏ（Ｃｏ）粉末および表１に示す化合物粉末を表１に示す比率で調合して、これに有機溶剤を加えて混合・粉砕した後、保形剤を添加してさらに混合し、できたスラリーをスプレードライヤーに投入して造粒粉末を作製した。次に、この造粒粉末を用いて、プレス成形により切削工具形状（ＣＮＭＧ１２０４０８ＰＳ）に成形を行い、焼成炉にて４５０℃で３時間脱脂を行った後、表１に示す温度および時間で保持して焼成前の熱処理を行い、その後に表１に示す条件で焼成して超硬合金を作製した。 After preparing the WC (WC) powder, the metal Co (Co) powder having the average particle size shown in Table 1 and the compound powder shown in Table 1 in the ratio shown in Table 1, adding an organic solvent to this and mixing and grinding The shape-retaining agent was added and further mixed, and the resulting slurry was put into a spray dryer to produce a granulated powder. Next, using this granulated powder, it was molded into a cutting tool shape (CNMG120408PS) by press molding, degreased at 450 ° C. for 3 hours in a firing furnace, and then held at the temperature and time shown in Table 1. Then, heat treatment was performed before firing, followed by firing under the conditions shown in Table 1 to produce a cemented carbide.
そして、上記ＣＮＭＧ１２０４０８ＰＳの略平板形状の超硬合金の表面に対して、両主面を研磨加工し、さらに切刃部にホーニング加工を施した。さらに、この加工した超硬合金の表面に化学気相蒸着（ＣＶＤ）法によって、０．５μｍの窒化Ｔｉ（ＴｉＮ）膜、５．０μｍの柱状の結晶構造をなす炭窒化Ｔｉ（ＴｉＣＮ）膜、２．０μｍのα型酸化アルミニウム（Ａｌ２Ｏ３）膜、１．０μｍの窒化Ｔｉ（ＴｉＮ）膜を順次成膜した。 And both main surfaces were grind | polished with respect to the surface of the said substantially plate-shaped cemented carbide alloy of said CNMG120408PS, and also the honing process was given to the cutting-blade part. Further, a 0.5 μm Ti nitride (TiN) film, a 5.0 μm columnar crystal structure Ti (TiCN) film is formed on the surface of the cemented carbide by chemical vapor deposition (CVD), A 2.0 μm α-type aluminum oxide (Al 2 O 3 ) film and a 1.0 μm Ti nitride (TiN) film were sequentially formed.
得られた工具について、鏡面加工された超硬合金の断面組織をオージェ分光分析（ＡＥＳ）および透過型電子顕微鏡（ＴＥＭ）観察にてＴｉとＮｂの分布状態を確認した。また、超硬合金の破面について走査型電子顕微鏡（ＳＥＭ）の反射電子像（ＢＥＩ）で観察し、観察される各Ｂ１型固溶相について均一な色調であるかどうかを確認することにより有芯構造をなしているかどうかを確認した。 About the obtained tool, the distribution state of Ti and Nb was confirmed by the Auger spectroscopic analysis (AES) and the transmission electron microscope (TEM) observation of the cross-sectional structure of the mirror-finished cemented carbide. Also, the fracture surface of the cemented carbide is observed with a backscattered electron image (BEI) of a scanning electron microscope (SEM), and it is confirmed by confirming whether or not each observed B1 type solid solution phase has a uniform color tone. It was confirmed whether the core structure was made.
また、超硬合金の鏡面研磨加工面について走査型電子顕微鏡による３０００倍の観察を行い、任意３箇所に対して電子線マイクロアナライザ（ＥＰＭＡ）にて各金属元素の濃度分布を測定し、Ｂ１型固溶相の特定を行い、これをルーゼックスにより画像解析することによって、Ｂ１型固溶相の面積％を算出した。また、この測定データから、超硬合金の表面にＢ１型固溶相が存在しない表面領域の厚みを測定した。結果は表２に示した。 Further, the mirror polished surface of the cemented carbide is observed 3000 times with a scanning electron microscope, the concentration distribution of each metal element is measured with an electron beam microanalyzer (EPMA) at any three locations, and the B1 type The solid solution phase was specified, and this was subjected to image analysis with Luzex to calculate the area% of the B1 type solid solution phase. Further, from this measurement data, the thickness of the surface region where the B1-type solid solution phase does not exist on the surface of the cemented carbide was measured. The results are shown in Table 2.
そして、この工具を用いて下記の条件により、連続切削試験および強断続切削試験を行い、耐摩耗性および耐欠損性を評価した。 Then, using this tool, a continuous cutting test and a strong interrupted cutting test were performed under the following conditions to evaluate the wear resistance and fracture resistance.
（切込変動切削条件）
被削材 ：ＳＣＭ４３５
工具形状：ＣＮＭＧ１２０４０８ＰＳ
切削速度：３００ｍ／分
送り速度：０．３ｍｍ／ｒｅｖ
切り込み：２．０ｍｍ（３秒切削毎に切込変動）
切削時間：１５分
切削液 ：エマルジョン１５％＋水８５％混合液
評価項目：顕微鏡にて切刃を観察し、フランク摩耗量・先端摩耗量を測定
（強断続切削条件）
被削材 ：ＳＣＭ４４０ ４本溝入材
工具形状：ＣＮＭＧ１２０４０８ＰＳ
切削速度：３００ｍ／分
送り速度：０．３５ｍｍ／ｒｅｖ
切り込み：１．５ｍｍ
切削液 ：エマルジョン１５％＋水８５％混合液
評価項目：欠損に至る衝撃回数
衝撃回数１０００回時点で顕微鏡にて切刃の状態を観察
結果は表２に示した。
(Cutting variable cutting conditions)
Work material: SCM435
Tool shape: CNMG120408PS
Cutting speed: 300 m / min Feeding speed: 0.3 mm / rev
Cutting depth: 2.0mm (cutting fluctuation every 3 seconds cutting)
Cutting time: 15 minutes Cutting fluid: Mixture of 15% emulsion + 85% water Evaluation item: Observe the cutting edge with a microscope and measure the amount of flank wear and tip wear (strong interrupted cutting conditions)
Work Material: SCM440 Four Groove Tool Shape: CNMG120408PS
Cutting speed: 300 m / min Feed rate: 0.35 mm / rev
Cutting depth: 1.5mm
Cutting fluid: Mixture of 15% emulsion + 85% water Evaluation item: Number of impacts leading to defects
Table 2 shows the observation results of the state of the cutting edge with a microscope at the time of impact of 1000 times.
表１、２に示す結果より、Ｂ１型固溶体相が析出しない試料Ｎｏ．８では塑性変形が大きくて摩耗、欠損性能ともに悪いものであった。また、Ｂ１型固溶体相内のＴｉとＮｂの濃度が最高となる位置が異なる試料Ｎｏ．６、７でも、摩耗、欠損性能がともに悪かった。 From the results shown in Tables 1 and 2, Sample No. No B1 solid solution phase precipitated. In No. 8, plastic deformation was large and both wear and chipping performance were poor. In addition, the sample Nos. 1 and 2 in which the positions where the concentrations of Ti and Nb in the B1-type solid solution phase become maximum are different. 6 and 7 also had poor wear and chipping performance.
これに対して、Ｂ１型固溶相は単一構造からなるとともにＴｉとＮｂの濃度が最高となる位置が異なる試料Ｎｏ．１〜５では、切込変動切削においても、強断続切削においても塑性変形は発生せず、長寿命であり、硬質被覆層の剥離や欠損も発生せず耐摩耗性および耐欠損性とも優れた切削性能を有するものであった。 On the other hand, the B1 type solid solution phase has a single structure and the sample No. Nos. 1 to 5 show no plastic deformation, long life, no peeling or chipping of the hard coating layer, and excellent wear resistance and fracture resistance in both cutting variation cutting and strong interrupted cutting. It had cutting performance.
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