JP6761596B2 - Cutting tool made of composite material - Google Patents
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この発明は、複合材料からなる切削工具に関し、特に、鉄鋼系材料基体の表面の一部または全部に、その表面形状を大きく変化させることなく、肉盛によるＷＣ基超硬合金付加層を設けた複合材料からなる切削性能のすぐれた切削工具に関する。 The present invention relates to a cutting tool made of a composite material , and in particular, a WC-based cemented carbide additional layer by overlay is provided on a part or all of the surface of a steel-based material substrate without significantly changing the surface shape thereof. Related to cutting tools with excellent cutting performance made of composite materials .
鋼や鋳鉄の切削加工用工具としては、ＷＣ基超硬合金が広く利用されているが、希少金属であるタングステンの使用量を削減するために、従来から、各種の提案がなされている。 WC-based cemented carbide is widely used as a tool for cutting steel and cast iron, but various proposals have been made in order to reduce the amount of tungsten, which is a rare metal.
例えば、特許文献１には、切削用材料として炭化タングステンを使用することは、よく知られているが、鑞付けにより、炭化タングステン製インサートを、切削工具に取
り付けるのに適したプロセスではないとの観点から、結合剤がコバルト、硬質材料が炭化タングステンであるような前記硬質材料を含む混合物を鋼帯の縁部に被着させ鋼帯の一部分を融解させるために、前記移動可能な鋼帯を放射線ビームで照射し、前記硬質材料及び結合剤元素を含む前記混合物を前記鋼帯の融解部分に供給し、硬質材料により被覆された鋼帯から個々のブレードを形成するブレードの製造方法が提案されている。
For example, Patent Document 1 states that the use of tungsten carbide as a cutting material is well known, but it is not a suitable process for attaching a tungsten carbide insert to a cutting tool by brazing. From the viewpoint, the movable steel strip is provided in order to apply a mixture containing the hard material such that the binder is cobalt and the hard material is tungsten carbide to the edge of the steel strip to melt a part of the steel strip. A method for producing a blade by irradiating with a radiation beam, supplying the mixture containing the hard material and the binder element to the molten portion of the steel strip, and forming individual blades from the steel strip coated with the hard material has been proposed. ing.
また、例えば、特許文献２には、複合材料からなる切削工具インサートとして、基体（台金）にＷＣ成分の含有量が１０ｍａｓｓ％以下であるＴｉ基サーメットを採用し、その基体の刃先となる部分にのみ、ＷＣと結合相形成成分（例えば、Ｃｏ，Ｎｉ，Ｆｅ）を主成分とし、該結合相の面積割合が８〜３０面積％であるＷＣ基超硬合金を刃先材料として形成し、一方、基体と刃先材料との界面側のＴｉ基サーメットの結合相（例えば、Ｃｏ，Ｎｉ，Ｆｅからなる結合相）の含有量を１０〜４０面積％とすることによって、タングステン使用量の低減を図り得るばかりか、密着強度不足による欠損や変形を生じることもなく、かつ、すぐれた耐摩耗性を発揮するＷＣ基超硬合金製切削工具インサートを得ること、さらに、刃先材料を溶射膜として構成した場合には、Ｔｉ基サーメットの結合相富化層の下部に結合相量が少なく、硬質層が富化した層が形成されており、ＷＣ成分の含有量が１０ｍａｓｓ％以下であり、また、適正な結合相分布が形成されているために、溶射膜との熱膨張係数差が制御され、それによる適度な残留圧縮応力が付与されることにより、より一段と密着強度にすぐれるとともに、剥離、欠損等の異常損傷を発生することもなく、すぐれた耐摩耗性を発揮するタングステン使用量を低減したＷＣ基超硬合金製切削工具インサートを得ることが提案されている。 Further, for example, in Patent Document 2, as a cutting tool insert made of a composite material, a Ti-based cermet having a WC component content of 10 mass% or less is adopted for a substrate (base metal), and a portion serving as a cutting edge of the substrate. A WC-based cemented carbide containing WC and a bonding phase forming component (for example, Co, Ni, Fe) as a main component and having an area ratio of the bonding phase of 8 to 30 area% is formed as a cutting edge material. By setting the content of the bonding phase of the Ti-based cermet on the interface side between the substrate and the cutting edge material (for example, the bonding phase composed of Co, Ni, Fe) to 10 to 40 area%, the amount of tungsten used can be reduced. A WC-based cemented carbide cutting tool insert that not only obtains, does not cause chipping or deformation due to insufficient adhesion strength, and exhibits excellent wear resistance, and further, the cutting edge material is configured as a cermet film. In the case, a layer having a small amount of bonded phase and an enriched hard layer is formed under the bonded phase enriched layer of the Ti-based cermet, and the content of the WC component is 10 mass% or less, which is appropriate. Since the bond phase distribution is formed, the difference in thermal expansion coefficient from the cermet film is controlled, and by applying an appropriate residual compressive stress, the adhesion strength is further improved, and peeling and chipping are performed. It has been proposed to obtain a WC-based cemented carbide cutting tool insert that exhibits excellent wear resistance and uses a reduced amount of tungsten without causing abnormal damage such as.
なお、特許文献３には、金属部材表面に硬質領域を形成する方法として、処理される金属部材よりも硬質で拡散・注入しようとする元素を含んでなる硬質粒子を金属部材に対して高速で打ち込み、次いで、打ち込まれた硬質粒子と金属部材との接触界面から拡散・注入しようとする元素を金属部材へと拡散させる硬質粒子打ち込みによる金属部材への元素の拡散・注入方法が提案されており、この方法によれば、金属部材最外層は、硬質粒子が打ち込まれるため加工硬化を生じ、また、硬質粒子は鋭角面を先端として楔状に深く打ち込まれるため安定であって、脱離することはなく、金属部材との密着性にすぐれるとされている。 In Patent Document 3, as a method of forming a hard region on the surface of a metal member, hard particles that are harder than the metal member to be treated and contain an element to be diffused / injected are emitted at high speed with respect to the metal member. A method has been proposed in which the elements to be diffused / injected from the contact interface between the driven hard particles and the metal member are diffused into the metal member, and then the elements are diffused / injected into the metal member by driving the hard particles. According to this method, the outermost layer of the metal member is work-hardened because hard particles are driven in, and the hard particles are stable and cannot be detached because they are deeply driven in a wedge shape with a sharp angle surface as the tip. It is said that it has excellent adhesion to metal members.
前記特許文献１、２に示す、超硬合金と鉄鋼材料、あるいは、超硬合金とサーメットからなる複合材料においては、希少金属であるタングステンの使用量の低減は図られるものの、この複合材料から形成した切削工具を、切れ刃に高負荷が作用する切削条件で使用した場合には、超硬合金の硬度が不十分であるため、満足できる耐摩耗性を発揮することができず、また、超硬合金からなる厚い肉盛層が形成されるため、工具として用いるに際しては、所定の工具形状に整形・加工する必要があった。
そこで、希少金属であるタングステンの使用量を低減し得るとともに、すぐれた硬度を有し、さらに、肉盛による表面形状変化（肉盛による厚さの増加）が少ないＷＣ基超硬合金と鉄鋼系材料からなる複合材料が望まれる。
In the composite material composed of cemented carbide and steel material or cemented carbide and cermet shown in Patent Documents 1 and 2, although the amount of tungsten used as a rare metal can be reduced, it is formed from this composite material. When the cutting tool is used under cutting conditions where a high load acts on the cutting edge, the hardness of the cemented carbide is insufficient, so that satisfactory wear resistance cannot be exhibited, and the cemented carbide cannot exhibit satisfactory wear resistance. Since a thick overlay layer made of cemented carbide is formed, it is necessary to shape and process it into a predetermined tool shape when it is used as a tool.
Therefore, the amount of tungsten, which is a rare metal, can be reduced, and the WC-based cemented carbide and steel-based alloy have excellent hardness and little surface shape change (thickness increase due to overlay) due to overlay. A composite material composed of materials is desired.
本発明者等は、上述のような観点から、タングステン使用量の低減を図るとともに、すぐれた硬度を有し、かつ、肉盛による表面形状変化（肉盛による厚さの増加）が少ないＷＣ基超硬合金と鉄鋼系材料からなる複合材料について鋭意検討したところ、鉄鋼系材料表面の一部または全部をレーザー照射により融解し、該融解箇所にＷＣ基超硬合金粉末を投射することにより、鉄鋼系材料表面上にＷＣ基超硬合金付加層を有する複合材料を作製するにあたり、レーザー照射条件（レーザー出力、レーザースポット径、走査速度）を適切にコントロールするとともに、鉄鋼系材料の温度、冷却までの時間をコントロールすることにより、鉄鋼系材料への肉盛による表面形状変化（厚さの増加）を抑制しつつ、鉄鋼系材料表面へＷＣ基超硬合金粒子を含有させることができ、これによって、鉄鋼系材料表面にＷＣ基超硬合金付加層からなる硬化層を形成し得ることを見出したのである。
そして、前記複合材料によって切削工具を構成することにより、この切削工具は、高硬度を有するため、長期の使用にわたって、すぐれた切削性能を発揮することを見出したのである。
From the above viewpoints, the present inventors have reduced the amount of tungsten used, have excellent hardness, and have little surface shape change (increase in thickness due to overlay) due to overlay. A diligent study of a composite material consisting of cemented carbide and a steel-based material revealed that a part or all of the surface of the steel-based material was melted by laser irradiation, and WC-based cemented carbide powder was projected onto the melted portion to make steel. In producing a composite material having a WC-based cemented carbide additional layer on the surface of the system material, the laser irradiation conditions (laser output, laser spot diameter, scanning speed) are appropriately controlled, and the temperature and cooling of the steel-based material are also achieved. By controlling the time, it is possible to contain WC-based cemented carbide particles on the surface of the steel-based material while suppressing the change in surface shape (increase in thickness) due to overlaying on the steel-based material. , They have found that a hardened layer composed of a WC-based cemented carbide addition layer can be formed on the surface of a steel-based material.
Then, by constructing a cutting tool with the composite material, it has been found that this cutting tool has high hardness and therefore exhibits excellent cutting performance over a long period of use.
本発明は、上記知見に基づいてなされたものであって、
「（１）鉄鋼系材料の表面の一部または全部にＷＣ基超硬合金付加層が設けられている複合材料からなる切削工具であって、
（ａ）前記ＷＣ基超硬合金付加層には、少なくとも、ＷＣ粒子が凝集する凝集組織が形成されており、
（ｂ）前記凝集組織は、前記ＷＣ基超硬合金付加層表面を含む任意の縦断面を観察した場合、（長径＋短径）／２で表される凝集組織の直径が１０μm以上６０μm以下、かつ、長径と短径の比率が１〜２の円形状の組織であり、前記凝集組織の占める面積割合は、前記ＷＣ基超硬合金付加層の面積の２０面積％以上５０面積％以下であり、
（ｃ）前記ＷＣ基超硬合金付加層を設ける以前の前記鉄鋼系材料の表面を基準面とした場合、前記ＷＣ基超硬合金層の最大侵入深さが前記鉄鋼系材料の基準面から内部へ２０μｍ以上２００μｍ以下に形成されている複合材料からなることを特徴とする切削工具。
（２）前記切削工具において、前記ＷＣ基超硬合金付加層の最大厚さは、前記最大浸入深さの１〜１．５倍であることを特徴とする前記（１）に記載の切削工具。
（３）前記切削工具において、前記ＷＣ基超硬合金付加層の結合相は、Ｆｅを２０原子％以上５０原子％以下およびＣｏを５０原子％以上８０原子％以下含有し、
前記ＷＣ基超硬合金付加層の表面のビッカース硬さＨＶは１０００以上１５００以下であることを特徴とする前記（１）または（２）に記載の切削工具。
（４）前記（１）乃至（３）のいずれかに記載の切削工具において、鉄鋼系材料が高速度工具鋼またはダイス鋼であることを特徴とする切削工具。」
を特徴とするものである。
The present invention has been made based on the above findings.
"(1) A cutting tool made of a composite material in which a WC-based cemented carbide additional layer is provided on a part or all of the surface of a steel-based material.
(A) At least an agglomerated structure in which WC particles aggregate is formed in the WC-based cemented carbide addition layer.
(B) When observing an arbitrary vertical cross section including the surface of the WC-based cemented carbide additional layer , the aggregated structure represented by (major axis + minor axis) / 2 has a diameter of 10 μm or more and 60 μm or less. In addition, it is a circular structure with a major axis to minor axis ratio of 1 to 2, and the area ratio occupied by the aggregated structure is 20 area% or more and 50 area% or less of the area of the WC-based cemented carbide additional layer. ,
(C) When the surface of the steel-based material before the WC-based cemented carbide additional layer is provided as a reference surface, the maximum penetration depth of the WC-based cemented carbide layer is inside the reference surface of the steel-based material. cutting tool, characterized in that it consists of double coupling material that is formed in 20μm or 200μm or less to.
(2) in the cutting tool, cutting tool according to (1), wherein the maximum thickness of the WC-based cemented carbide additional layer is 1 to 1.5 times the maximum penetration depth ..
( 3 ) In the cutting tool , the bonding phase of the WC-based cemented carbide additional layer contains 20 atomic% or more and 50 atomic% or less of Fe and 50 atomic% or more and 80 atomic% or less of Co.
The cutting tool according to (1) or (2) above, wherein the Vickers hardness HV of the surface of the WC-based cemented carbide addition layer is 1000 or more and 1500 or less.
( 4 ) The cutting tool according to any one of (1) to ( 3 ) above, wherein the steel-based material is high-speed tool steel or die steel . "
It is characterized by.
次に、この発明について、詳細に説明する。 Next, this invention will be described in detail.
図１に、本発明複合材料の縦断面概略模式図を示す。
図２（ａ）には、本発明複合材料の一つの具体例の縦断面ＳＥＭ像を示し、また、図２（ｂ）には、図２（ａ）の部分拡大図を示す。
本発明の複合材料は、図１および図２（ａ）に示すように、鉄鋼系材料の表面の一部または全部に、ＷＣ基超硬合金付加層が設けられている。
また、前記ＷＣ基超硬合金付加層には、図２（ｂ）に示すように、ＷＣ粒子が凝集する凝集組織が形成されている。該凝集組織は、走査型電子顕微鏡による５００倍の二次電子像において、白色系のコントラストを有する画像として特定される。なお、ＷＣ粒子は白色系のコントラストを有し、ＷＣ基超硬合金付加層が設けられた基材である鉄鋼系材料は灰色系の色調を有することから、ＷＣ粒子が凝集する凝集組織を識別することができる。
なお、本発明の複合材料を構成する鉄鋼系材料としては、特段の制限はないが、高速度工具鋼、ダイス鋼を用いることが好適である。
FIG. 1 shows a schematic vertical cross-sectional view of the composite material of the present invention.
FIG. 2 (a) shows a vertical cross-sectional SEM image of one specific example of the composite material of the present invention, and FIG. 2 (b) shows a partially enlarged view of FIG. 2 (a).
As shown in FIGS. 1 and 2 (a), the composite material of the present invention is provided with a WC-based cemented carbide addition layer on a part or all of the surface of the steel-based material.
Further, as shown in FIG. 2B, an aggregated structure in which WC particles aggregate is formed in the WC-based cemented carbide addition layer. The aggregated structure is identified as an image having white contrast in a 500x secondary electron image by a scanning electron microscope. Since the WC particles have a white contrast and the steel-based material which is the base material provided with the WC-based cemented carbide additional layer has a gray color tone, the aggregated structure in which the WC particles aggregate is identified. can do.
The steel-based material constituting the composite material of the present invention is not particularly limited, but it is preferable to use high-speed tool steel or die steel.
前記凝集組織は、図２（ａ）、（ｂ）からもわかるように、ＷＣ基超硬合金付加層表面を含む任意の縦断面を観察した場合、直径１０μm以上６０μm以下、かつ、長径と短径の比率（長径／短径）が１〜２の円形状の組織である。
上記の直径及び長径−短径比を有する凝集組織は、後記するレーザー肉盛によって形成することができるが、直径が１０μｍ未満では凝集組織を形成することが難しくなることから、相対的に強度が低下することにより、脆化傾向を示し、一方、直径が６０μｍを超えると、凝集組織が粗大となり、凝集組織の脱落が生じやすくなることから、凝集組織の直径は１０μm以上６０μm以下とする。
As can be seen from FIGS. 2 (a) and 2 (b), the aggregated structure has a diameter of 10 μm or more and 60 μm or less, and a major axis and a short axis when an arbitrary vertical cross section including the surface of the WC-based cemented carbide additional layer is observed. It is a circular structure having a diameter ratio (major axis / minor axis) of 1 to 2.
The aggregated structure having the above diameter and major axis-minor axis ratio can be formed by laser overlay described later, but if the diameter is less than 10 μm, it becomes difficult to form the aggregated structure, so that the strength is relatively high. When the diameter exceeds 60 μm, the aggregated structure becomes coarse and the aggregated structure tends to fall off. Therefore, the diameter of the aggregated structure is set to 10 μm or more and 60 μm or less.
また、前記凝集組織の長径と短径の比率が２を超え、非円形状の形状になると、凝集組織が非等方的な性質をもった組織となり、ＷＣ基超硬合金付加層全体としての高硬度を担保するという観点からは望ましくないことから、凝集組織における長径と短径の比率（長径／短径）は２以下（即ち、１〜２）の円形状の組織とする。 Further, when the ratio of the major axis to the minor axis of the agglomerated structure exceeds 2 and the shape becomes a non-circular shape, the agglomerated structure becomes a structure having an isotropic property, and the WC-based cemented carbide additional layer as a whole becomes. Since it is not desirable from the viewpoint of ensuring high hardness, the ratio of the major axis to the minor axis (major axis / minor axis) in the aggregated structure is 2 or less (that is, 1 to 2) in a circular structure.
また、本発明の複合材料では、例えば、レーザーを用いた肉盛法により鉄鋼系材料の表面の一部または全部にＷＣ基超硬合金付加層を形成することにより、図１、図２に示すように、ＷＣ基超硬合金層の最大侵入深さが前記鉄鋼系材料の基準面から内部へ２０μｍ以上２００μｍ以下に形成する。
つまり、レーザー照射により鉄鋼系材料とＷＣ基超硬合金を溶融させ、鉄鋼系材料表面の一部または全部に鉄鋼系材料のプールを形成するとともに、該プール内にＷＣ基超硬合金粉末を投射して溶け込ませ、これを冷却することによって、ＷＣ基超硬合金付加層の最大浸入深さが鉄鋼系材料の基準面から２０μｍ〜２００μｍの深さとなるようＷＣ基超硬合金層を形成する。
ここで、鉄鋼系材料の基準面とは、ＷＣ基超硬合金付加層を設ける以前の鉄鋼系材料の表面をいう。
鉄鋼系材料の基準面からのＷＣ基超硬合金付加層の最大浸入深さが２０μｍ未満では、形成される鉄鋼系材料のプールの深さが浅く、鉄鋼系材料とＷＣ基超硬合金との溶け込み量が少なく、鉄鋼系材料に対するＷＣ基超硬合金付加層の密着効果が少ないため、複合部材に負荷が作用した場合、鉄鋼系材料とＷＣ基超硬合金付加層が剥離を発生しやすい。
一方、鉄鋼系材料の基準面からのＷＣ基超硬合金付加層の最大浸入深さが２００μｍを超える場合には、鉄鋼系材料の溶融量が大きいため、冷却時に割れを生じやすくなり、その結果、ＷＣ基超硬合金付加層の脱落が生じやすくなる。
したがって、鉄鋼系材料の基準面からのＷＣ基超硬合金付加層の最大浸入深さは、２０μｍ以上２００μｍ以下とする。
Further, in the composite material of the present invention, for example, by forming a WC-based cemented carbide additional layer on a part or all of the surface of the steel-based material by a build-up method using a laser, it is shown in FIGS. 1 and 2. As described above, the maximum penetration depth of the WC-based cemented carbide layer is formed to be 20 μm or more and 200 μm or less inward from the reference surface of the steel-based material.
That is, the steel-based material and the WC-based cemented carbide are melted by laser irradiation to form a pool of the steel-based material on a part or all of the surface of the steel-based material, and the WC-based cemented carbide powder is projected into the pool. The WC-based cemented carbide layer is formed so that the maximum penetration depth of the WC-based cemented carbide additional layer is 20 μm to 200 μm from the reference plane of the steel-based material.
Here, the reference surface of the steel-based material refers to the surface of the steel-based material before the WC-based cemented carbide addition layer is provided.
When the maximum penetration depth of the WC-based cemented carbide additional layer from the reference plane of the steel-based material is less than 20 μm, the depth of the pool of the formed steel-based material is shallow, and the steel-based material and the WC-based cemented carbide Since the amount of penetration is small and the effect of the WC-based cemented carbide additional layer on the steel-based material is small, when a load is applied to the composite member, the steel-based material and the WC-based cemented carbide additional layer are likely to peel off.
On the other hand, when the maximum penetration depth of the WC-based cemented carbide additional layer from the reference plane of the steel-based material exceeds 200 μm, the amount of melting of the steel-based material is large, so that cracks are likely to occur during cooling, resulting in , The WC-based cemented carbide additional layer is likely to fall off.
Therefore, the maximum penetration depth of the WC-based cemented carbide addition layer from the reference plane of the steel-based material is set to 20 μm or more and 200 μm or less.
なお、鉄鋼系材料の基準面からのＷＣ基超硬合金付加層の最大浸入深さは、走査型電子顕微鏡により取得した画像において、ＷＣ基超硬合金付加層を形成する以前の鉄鋼系材料の表面を基準面とし、該基準面からＷＣ基超硬合金付加層を横断する線分を引き、該線分から、鉄鋼系材料とＷＣ基超硬合金付加層の界面への垂直な距離を測定し、その最大距離をＷＣ基超硬合金付加層の最大浸入深さとして求めることができる。 The maximum penetration depth of the WC-based cemented carbide additional layer from the reference plane of the steel-based material is the maximum penetration depth of the steel-based material before forming the WC-based cemented carbide additional layer in the image acquired by the scanning electron microscope. With the surface as the reference plane, a line crossing the WC-based cemented carbide additional layer is drawn from the reference plane, and the vertical distance from the line to the interface between the steel-based material and the WC-based cemented carbide additional layer is measured. , The maximum distance can be obtained as the maximum penetration depth of the WC-based cemented carbide additional layer.
本発明のＷＣ基超硬合金付加層は、主として、ＷＣ基超硬合金の硬質成分であるＷＣ粒子の凝集組織によってその高硬度を発現するが、前記ＷＣ基超硬合金付加層の縦断面観察において、該層中に占めるＷＣ粒子の凝集組織の面積割合が２０面積％未満では、十分な高硬度、耐摩耗性を発揮することができないことから、一方、ＷＣ基超硬合金付加層に占めるＷＣ粒子の凝集組織の面積割合が５０面積％を超えると、凝集組織同士が隣接し、凝集組織の脱落が生じやすくなることから、ＷＣ基超硬合金付加層の縦断面に占めるＷＣ粒子の凝集組織の面積割合は２０面積％以上５０面積％以下とすることが望ましい。 The WC-based cemented carbide additional layer of the present invention exhibits its high hardness mainly due to the aggregated structure of WC particles, which is a hard component of the WC-based cemented carbide, and the vertical cross-sectional observation of the WC-based cemented carbide additional layer is observed. In the above, if the area ratio of the aggregated structure of the WC particles in the layer is less than 20 area%, sufficient high hardness and abrasion resistance cannot be exhibited. Therefore, the WC-based cemented carbide additional layer is occupied. When the area ratio of the agglomerated structure of the WC particles exceeds 50 area%, the agglomerated structures are adjacent to each other and the agglomerated structures are likely to fall off. Therefore, the agglomeration of the WC particles in the vertical cross section of the WC-based cemented carbide addition layer It is desirable that the area ratio of the tissue is 20 area% or more and 50 area% or less.
本発明の複合材料において、ＷＣ基超硬合金付加層の最大厚さは、前記ＷＣ基超硬合金付加層の最大浸入深さの１〜１．５倍とすることが望ましい。
ここで、ＷＣ基超硬合金付加層の最大厚さとは、走査型電子顕微鏡およびオージェ電子分光装置を用いて、ＷＣ基超硬合金付加層と鉄鋼系材料との接合部近傍の縦断面観察をし、ＷＣ基超硬合金付加層側からみて、ＷＣ粒子が観察される臨界位置を界面とし、ＷＣ基超硬合金付加層を設ける以前の鉄鋼系材料の表面に垂直方向に、前記界面からＷＣ基超硬合金付加層表面までの最大距離をＷＣ基超硬合金付加層の最大厚さという（図１参照）。
ＷＣ基超硬合金付加層の最大厚さを、最大浸入深さの１〜１．５倍とするのは、ＷＣ基超硬合金付加層の最大厚さが最大浸入深さの１倍未満であるような場合には、ＷＣ基超硬合金付加層の生成量が少なすぎるため、硬さ向上効果が少なく、一方、ＷＣ基超硬合金付加層の最大厚さが最大浸入深さの１．５倍を超えるような場合には、ＷＣ基超硬合金付加層の鉄鋼系材料の基準面からの突出高さが大きくなりすぎ、当初の鉄鋼系材料の表面形状が大幅に変更されることになるからである。
鉄鋼系材料表面への上記最大厚さのＷＣ基超硬合金付加層は、例えば、後記するレーザー肉盛法によって形成することができる。
In the composite material of the present invention, it is desirable that the maximum thickness of the WC-based cemented carbide additional layer is 1 to 1.5 times the maximum penetration depth of the WC-based cemented carbide additional layer.
Here, the maximum thickness of the WC-based cemented carbide additional layer is the vertical cross-sectional observation of the vicinity of the joint between the WC-based cemented carbide additional layer and the steel-based material using a scanning electron microscope and an Auger electron spectroscope. However, when viewed from the WC-based cemented carbide additional layer side, the critical position where WC particles are observed is set as the interface, and the WC is WC from the interface in the direction perpendicular to the surface of the steel-based material before the WC-based cemented carbide additional layer is provided. The maximum distance to the surface of the basic cemented carbide additional layer is called the maximum thickness of the WC basic cemented carbide additional layer (see FIG. 1).
The maximum thickness of the WC-based cemented carbide additional layer is 1 to 1.5 times the maximum penetration depth when the maximum thickness of the WC-based cemented carbide additional layer is less than 1 times the maximum penetration depth. In such a case, the amount of the WC-based cemented carbide additional layer produced is too small, so that the effect of improving the hardness is small, while the maximum thickness of the WC-based cemented carbide additional layer is the maximum penetration depth. If it exceeds 5 times, the protruding height of the WC-based cemented carbide additional layer from the reference plane becomes too large, and the surface shape of the original steel-based material is significantly changed. Because it becomes.
The WC-based cemented carbide addition layer having the maximum thickness on the surface of the steel-based material can be formed, for example, by the laser overlay method described later.
本発明の複合材料において、ＷＣ基超硬合金付加層における主たる硬質成分は、該層中において２０〜５０面積％を占めるＷＣ粒子の凝集組織であるが、従来から知られているＴｉ、Ｚｒ、Ｃｒ、Ｖ、ＮｂおよびＴａの炭化物、窒化物、炭窒化物、炭酸化物、窒酸化物および炭窒酸化物等からなる副硬質相成分を含有させることができる。
また、本発明では、前記ＷＣ基超硬合金付加層を構成する結合相成分として、２０〜５０原子％Ｆｅおよび５０〜８０原子％のＣｏを含有させる。
結合相成分のＦｅが２０原子％未満では、鉄鋼系材料との密着強度が不十分となり剥離する恐れがあり、一方、Ｆｅの含有量が５０原子％を超えると凝集組織の強度が低下し、クラックを生じやすくなることから、Ｆｅの含有量２０〜５０原子％、残部はＣｏ（即ち、Ｃｏ含有量は５０〜８０原子％）とすることが望ましい。
In the composite material of the present invention, the main hard component in the WC-based cemented carbide addition layer is an aggregated structure of WC particles occupying 20 to 50 area% in the layer, but conventionally known Ti, Zr, It can contain a sub-hard phase component composed of carbides of Cr, V, Nb and Ta, nitrides, carbonitrides, coal oxides, nitrogen oxides, carbon dioxide oxides and the like.
Further, in the present invention, 20 to 50 atomic% Fe and 50 to 80 atomic% Co are contained as the bonding phase components constituting the WC-based cemented carbide addition layer.
If the Fe content of the bonded phase component is less than 20 atomic%, the adhesion strength with the steel-based material becomes insufficient and there is a risk of peeling, while if the Fe content exceeds 50 atomic%, the strength of the aggregated structure decreases. It is desirable that the Fe content is 20 to 50 atomic% and the balance is Co (that is, the Co content is 50 to 80 atomic%) because cracks are likely to occur.
前記ＷＣ基超硬合金付加層の結合相におけるＦｅ含有量およびＣｏ含有量は、次のようにして求めることができる。
まず、鉄鋼系材料とＷＣ基超硬合金付加層との界面からＷＣ基超硬合金付加層側に、前記界面からＷＣ基超硬合金付加層表面に向けてＷＣ基超硬合金付加層を１０等分するように、前記鉄鋼系材料表面の基準面に平行に９本の線を引き、同線上で線分析を行い、結合相中のＦｅおよびＣｏの含有量を測定し、前記９本の線についてそれぞれ測定したＦｅおよびＣｏの含有量を平均化することによって、ＷＣ基超硬合金付加層の結合相におけるＦｅ含有量およびＣｏ含有量をそれぞれの平均値として求めることができる。
The Fe content and Co content in the bonded phase of the WC-based cemented carbide addition layer can be determined as follows.
First, 10 WC-based cemented carbide additional layers are provided from the interface between the steel-based material and the WC-based cemented carbide additional layer to the WC-based cemented carbide additional layer side, and from the interface toward the WC-based cemented carbide additional layer surface. Nine lines are drawn parallel to the reference plane on the surface of the steel-based material so as to divide them into equal parts, line analysis is performed on the same lines, and the contents of Fe and Co in the bonded phase are measured. By averaging the Fe and Co contents measured for each of the lines, the Fe content and the Co content in the bonded phase of the WC-based cemented carbide addition layer can be obtained as their respective average values.
また、本発明では、ＷＣ基超硬合金付加層の表面のビッカース硬さＨＶを１０００以上１５００以下とすることが望ましい。
ＷＣ基超硬合金付加層の表面のビッカース硬さＨＶが１０００未満では、ＷＣ基超硬合金付加層を形成したことによる硬さ向上効果が少なく、一方、ビッカース硬さＨＶが１５００を超えるような場合には、ＷＣ基超硬合金付加層の靱性が低下し、チッピングを生じやすくなることから、ビッカース硬さＨＶは１０００以上１５００以下とすることが望ましい。
Further, in the present invention, it is desirable that the Vickers hardness HV of the surface of the WC-based cemented carbide addition layer is 1000 or more and 1500 or less.
When the Vickers hardness HV of the surface of the WC-based cemented carbide additional layer is less than 1000, the hardness improving effect due to the formation of the WC-based cemented carbide additional layer is small, while the Vickers hardness HV exceeds 1500. In some cases, the Vickers hardness HV is preferably 1000 or more and 1500 or less because the toughness of the WC-based cemented carbide additional layer is lowered and chipping is likely to occur.
本発明の複合材料は、硬度にすぐれ、また、肉盛による鉄鋼系材料表面の形状変化が少ないことから、ＷＣ基超硬合金付加層を切れ刃として使用する切削工具や、局所的に硬度が必要となる工具シャンク等に好適である。
なお、ＷＣ基超硬合金付加層をそのまま切れ刃として切削加工に供することができるが、ＷＣ基超硬合金付加層表面に、従来から良く知られている硬質被覆層（例えば、Ｔｉ化合物層、ＴｉＡｌＮ層、Ａｌ２Ｏ３層等）を物理蒸着あるいは化学蒸着等により被覆形成することによって、表面被覆切削工具として使用することもできる。
Since the composite material of the present invention has excellent hardness and the shape change of the surface of the steel-based material due to overlay is small, the cutting tool using the WC-based cemented carbide additional layer as a cutting edge and the local hardness are high. Suitable for necessary tool shanks and the like.
The WC-based cemented carbide additional layer can be used as it is for cutting as a cutting edge, but a conventionally well-known hard coating layer (for example, Ti compound layer, etc.) is provided on the surface of the WC-based cemented carbide additional layer. TiAlN layer, by coating formed by physical vapor deposition or chemical vapor deposition or the like the Al 2 O 3 layer, etc.) can also be used as a surface-coated cutting tool.
本発明の複合材料は、例えば、レーザー肉盛法によって作製することができる。
まず、ＷＣ基超硬合金付加層を形成する鉄鋼系材料の所定位置に対してレーザー照射を行い、該位置の鉄鋼系材料を溶融させてプールを形成し、該プールに向けて所定成分組成のＷＣ基超硬合金粉末を吹きつけ、該プールにおいて溶融した鉄鋼系材料でＷＣ基超硬合金を希釈・溶融し、その後、これを冷却することにより、本発明で規定するＷＣ基超硬合金付加層（最大厚さ、ＷＣ粒子からなる所定形状の凝集組織、最大浸入深さ、凝集組織の面積割合、所定の結合相成分組成、硬さ）を、鉄鋼系材料の表面の一部または全部に設けた、すぐれた硬さを有する複合材料を作製することができる。
なお、レーザー照射に際して、鉄鋼系材料にクラックを発生させず、かつ、ＷＣ基超硬合金付加層を過度に厚くせず当初の鉄鋼系材料表面形状を維持するためには、大出力、大スポット径の照射は避けるべきであって、レーザー出力２００Ｗ以下、スポット径２ｍｍ以下、操作速度１０００ｍｍ／ｍｉｎ以上の低エネルギー高速走査速度のレーザー照射が望ましい。
The composite material of the present invention can be produced, for example, by a laser overlay method.
First, laser irradiation is performed on a predetermined position of the steel-based material forming the WC-based cemented carbide additional layer, the steel-based material at the position is melted to form a pool, and a predetermined component composition is directed toward the pool. By spraying WC-based cemented carbide powder, diluting and melting the WC-based cemented carbide with the steel-based material melted in the pool, and then cooling it, the WC-based cemented carbide specified in the present invention is added. A layer (maximum thickness, agglomerated structure of a predetermined shape composed of WC particles, a maximum penetration depth, an area ratio of the agglomerated structure, a predetermined bonded phase component composition, hardness) is applied to a part or all of the surface of a steel-based material. It is possible to produce a provided composite material having excellent hardness.
In order to maintain the initial surface shape of the steel-based material without causing cracks in the steel-based material and without making the WC-based cemented carbide additional layer excessively thick during laser irradiation, high output and large spots are required. Irradiation with a diameter should be avoided, and laser irradiation with a laser output of 200 W or less, a spot diameter of 2 mm or less, and an operation speed of 1000 mm / min or more with a low energy and high scanning speed is desirable.
本発明によれば、鉄鋼系材料の表面の一部または全部に、鉄鋼系材料の表面形状に大きな変化を与えることなく、高硬度を有するＷＣ基超硬合金付加層が設けられた複合材料を得ることができる。
そして、この複合材料は、そのすぐれた硬さを生かし、切削工具として好適に使用することができる。
According to the present invention, a composite material provided with a WC-based cemented carbide addition layer having high hardness on a part or all of the surface of the steel-based material without significantly changing the surface shape of the steel-based material. Obtainable.
Then, this composite material can be suitably used as a cutting tool by taking advantage of its excellent hardness.
以下、この発明を実施例に基づいて、具体的に説明する。 Hereinafter, the present invention will be specifically described with reference to Examples.
（ａ）表１に示す成分組成の鉄鋼系材料の表面に、表２に示す本発明条件にてレーザーを照射し、該レーザー照射箇所に向けて、表３に示す配合組成からなる造粒-仮焼したＷＣ基超硬合金粉末を表２に示す条件で投射し、鉄鋼系材料の表面の一部または全部にＷＣ基超硬合金付加層を形成することにより表４に示す本発明の複合材料１〜１２（本発明複合材料１〜１２という）を作製した。冷却機構を備えたステージに鉄鋼系材料を固定し、鉄鋼系材料を強制冷却しながらＷＣ基超硬合金付加層を形成した。
なお、レーザー照射条件は、いずれも、レーザー出力５０〜２００Ｗ、スポット径０．５〜４．０ｍｍ、操作速度５００〜２０００ｍｍ／ｍｉｎ、繰返し肉盛回数１〜３回の範囲内である。
なお、本発明複合材料１の縦断面組織を図２（ａ）に、また、ＷＣ基超硬合金付加層内の組織を図２（ｂ）に、それぞれ示す。
(A) The surface of the steel-based material having the composition shown in Table 1 is irradiated with a laser under the conditions of the present invention shown in Table 2, and the granulation having the composition shown in Table 3 is directed toward the laser irradiation site. The composite of the present invention shown in Table 4 is formed by projecting the calcined WC-based cemented carbide powder under the conditions shown in Table 2 and forming a WC-based cemented carbide additional layer on a part or all of the surface of the steel-based material. Materials 1-12 (referred to as composite materials 1-12 of the present invention) were prepared. A steel-based material was fixed to a stage equipped with a cooling mechanism, and a WC-based cemented carbide addition layer was formed while forcibly cooling the steel-based material.
The laser irradiation conditions are all within the range of a laser output of 50 to 200 W, a spot diameter of 0.5 to 4.0 mm, an operation speed of 500 to 2000 mm / min, and a number of repeated build-ups of 1 to 3.
The vertical cross-sectional structure of the composite material 1 of the present invention is shown in FIG. 2 (a), and the structure in the WC-based cemented carbide additional layer is shown in FIG. 2 (b).
本発明複合材料１〜１２について、走査型電子顕微鏡とオージェ電子分光装置を用いて、ＷＣ基超硬合金付加層と鉄鋼系材料との接合部近傍の縦断面を観察し、ＷＣ基超硬合金付加層側からみて、ＷＣ粒子が観察される臨界位置を界面とし、ＷＣ基超硬合金付加層を設ける以前の鉄鋼系材料の表面に垂直方向に、界面からＷＣ基超硬合金付加層表面までの距離を求め、そのうちの最大値をＷＣ基超硬合金付加層の最大厚さとして求めた。 For the composite materials 1 to 12 of the present invention, using a scanning electron microscope and an Auger electron spectroscope, the longitudinal cross section near the joint between the WC-based cemented carbide adhering layer and the steel-based material was observed, and the WC-based cemented carbide was observed. When viewed from the additional layer side, the critical position where WC particles are observed is the interface, and from the interface to the surface of the WC-based cemented carbide additional layer in the direction perpendicular to the surface of the steel-based material before the WC-based cemented carbide additional layer is provided. The maximum value of the distance was determined as the maximum thickness of the WC-based cemented carbide additional layer.
また、本発明複合材料１〜１２について、５００倍の走査型電子顕微鏡によりＷＣ基超硬合金付加層表面を含む任意の縦断面箇所の画像を取得し、画像全体の面積と、該画像中に存在するＷＣ粒子からなる凝集組織の長径、短径、合計面積を求め、この値から、ＷＣ基超硬合金付加層に占める凝集組織の直径（＝（長径＋短径）／２）、長径と短径の比、面積割合を算出した。 Further, for the composite materials 1 to 12 of the present invention, an image of an arbitrary vertical cross-sectional portion including the surface of the WC-based cemented carbide additional layer was acquired by a scanning electron microscope at a magnification of 500, and the area of the entire image and the image were included in the image. The major axis, minor axis, and total area of the aggregated structure consisting of the existing WC particles were obtained, and from this value, the diameter of the aggregated structure in the WC-based cemented carbide adhering layer (= (major axis + minor axis) / 2), major axis. The minor axis ratio and area ratio were calculated.
また、本発明複合材料１〜１２について、２０００倍の走査型電子顕微鏡を用いて、鉄鋼系材料とＷＣ基超硬合金付加層との界面近傍の画像を取得し、まず、鉄鋼系材料とＷＣ基超硬合金付加層との界面からＷＣ基超硬合金付加層側に、前記界面からＷＣ基超硬合金付加層表面に向けてＷＣ基超硬合金付加層を１０等分するように、前記鉄鋼系材料表面の基準面に平行に９本の線を引き、同線上で線分析を行い、結合相中のＦｅおよびＣｏの含有量を測定し、前記９本の線についてそれぞれ測定したＦｅおよびＣｏの含有量を平均化することによって、ＷＣ基超硬合金付加層の結合相におけるＦｅ含有量およびＣｏ含有量をそれぞれの平均値として求めた。 Further, for the composite materials 1 to 12 of the present invention, an image of the vicinity of the interface between the steel-based material and the WC-based cemented carbide adhering layer was acquired using a 2000x scanning electron microscope, and first, the steel-based material and WC were obtained. The WC-based cemented carbide additional layer is divided into 10 equal parts from the interface with the basic cemented carbide additional layer to the WC-based cemented carbide additional layer side and from the interface toward the surface of the WC-based cemented carbide additional layer. Nine lines are drawn parallel to the reference plane on the surface of the steel-based material, line analysis is performed on the same lines, the contents of Fe and Co in the bonded phase are measured, and Fe and the measured Fe and each of the nine lines are measured. By averaging the Co contents, the Fe content and the Co content in the bonded phase of the WC-based cemented carbide adhering layer were determined as their respective average values.
さらに、本発明複合材料１〜１２について、走査型電子顕微鏡により、鉄鋼系材料とＷＣ基超硬合金付加層との界面近傍の画像を取得し、該画像において、鉄鋼系材料の基準面（（ＷＣ基超硬合金付加層を設ける以前の鉄鋼系材料の表面））からＷＣ基超硬合金付加層を横断する線分を引き、該線分から、鉄鋼系材料とＷＣ基超硬合金付加層の界面までの垂直な距離を測定し、その最大距離をＷＣ基超硬合金付加層の最大浸入深さとして求めた。 Further, for the composite materials 1 to 12 of the present invention, an image of the vicinity of the interface between the steel-based material and the WC-based cemented carbide addition layer is acquired by a scanning electron microscope, and in the image, the reference plane of the steel-based material ((( A line crossing the WC-based cemented carbide additional layer is drawn from the surface of the steel-based material before the WC-based cemented carbide additional layer is provided)), and the steel-based material and the WC-based cemented carbide additional layer are separated from the line. The vertical distance to the interface was measured, and the maximum distance was determined as the maximum penetration depth of the WC-based cemented carbide additional layer.
表４に、上記で得た測定値、算出値を示す。 Table 4 shows the measured values and calculated values obtained above.
比較のため、表１に示す成分組成の鉄鋼系材料の表面に、表５に示す条件にてレーザーを照射し、該レーザー照射箇所に向けて、表３に示す配合組成からなる造粒-仮焼したＷＣ基超硬合金粉末を投射し、鉄鋼系材料の表面の一部または全部にＷＣ基超硬合金付加層を形成することにより表６に示す比較例の複合材料１〜１２（比較例複合材料１〜１２という）を作製した。
なお、レーザー照射条件は、いずれも、レーザー出力３０〜５００Ｗ、スポット径０．１〜１０．０ｍｍ、操作速度２００〜３０００ｍｍ／ｍｉｎ、繰返し肉盛回数１〜５回の範囲内である。
For comparison, the surface of the steel-based material having the composition shown in Table 1 is irradiated with a laser under the conditions shown in Table 5, and the granulation-provisional composition having the composition shown in Table 3 is directed toward the laser irradiation site. By projecting the baked WC-based cemented carbide powder and forming a WC-based cemented carbide additional layer on a part or all of the surface of the steel-based material, composite materials 1 to 12 of Comparative Examples shown in Table 6 (Comparative Examples). Composite materials 1-12) were prepared.
The laser irradiation conditions are all within the range of a laser output of 30 to 500 W, a spot diameter of 0.1 to 10.0 mm, an operation speed of 200 to 3000 mm / min, and a number of repeated build-ups of 1 to 5 times.
次いで、比較例複合材料１〜１２について、本発明複合材料１〜１２の場合と同様にして、ＷＣ基超硬合金付加層の最大厚さ、凝集組織の直径、凝集組織の長径と短径の比の値、面積割合を求めた。 Next, with respect to Comparative Examples Composite Materials 1 to 12, the maximum thickness of the WC-based cemented carbide additional layer, the diameter of the aggregated structure, and the major axis and the minor axis of the aggregated structure were obtained in the same manner as in the case of the composite materials 1 to 12 of the present invention. The ratio value and area ratio were calculated.
さらに、ＷＣ基超硬合金付加層の結合相中のＦｅおよびＣｏの含有量を求め、ＷＣ基超硬合金付加層の最大浸入深さを求めた。
表６に、これらの値を示す。
Further, the contents of Fe and Co in the bonded phase of the WC-based cemented carbide addition layer were determined, and the maximum penetration depth of the WC-based cemented carbide addition layer was determined.
Table 6 shows these values.
つぎに、上記本発明複合材料１〜１２および比較例複合材料１〜１２のＷＣ基超硬合金付加層の表面について、それぞれのマイクロビッカース硬さＨＶを測定した。
表４および表６に、その値を示す。
Next, the micro Vickers hardness HV of each of the surfaces of the WC-based cemented carbide addition layers of the composite materials 1 to 12 of the present invention and the composite materials 1 to 12 of Comparative Examples was measured.
The values are shown in Tables 4 and 6.
ついで、上記本発明複合材料１〜１２および比較例複合材料１〜１２から、ＷＣ基超硬合金付加層をそれぞれの切れ刃とする、本発明ドリル１〜１２、本発明エンドミル１〜１２、比較例ドリル１〜１２、比較例エンドミル１〜１２を作製した。
また、参考のため、表１に示される高速度工具鋼Ａ及び合金工具鋼Ｂから参考ドリルＡ、参考エンドミルＡ、参考ドリルＢ、参考エンドミルＢを作製した。
これらのドリル、エンドミルを切削試験に供することによって切削性能を調査した。
Next, from the composite materials 1 to 12 of the present invention and the composite materials 1 to 12 of the comparative example, the drills 1 to 12 of the present invention and the end mills 1 to 12 of the present invention, each of which uses a WC-based cemented carbide additional layer as a cutting edge, are compared. Example drills 1 to 12 and comparative example end mills 1 to 12 were prepared.
For reference, a reference drill A, a reference end mill A, a reference drill B, and a reference end mill B were manufactured from the high-speed tool steel A and the alloy tool steel B shown in Table 1.
Cutting performance was investigated by subjecting these drills and end mills to cutting tests.
なお、前記エンドミルは、いずれも、切刃部の直径×長さが１０ｍｍ×２０ｍｍの寸法、並びにねじれ角３０度の２枚刃スクエア形状のサイズ・形状をもち、また、前記ドリルは、いずれも、溝形成部の直径×長さがそれぞれ５ｍｍ×６３．５ｍｍの寸法、並びにねじれ角２７度の２枚刃形状をもつ。 All of the end mills have dimensions of a cutting edge portion diameter x length of 10 mm x 20 mm, and a two-blade square shape with a twist angle of 30 degrees, and all of the drills have a size and shape. , The diameter x length of the groove forming portion is 5 mm × 63.5 mm, respectively, and has a two-flute shape with a twist angle of 27 degrees.
前記の各ドリルについて、次に示す切削条件Ａで穴あけ加工試験条件を実施し、前記の各エンドミルについて、次に示す切削条件Ｂで側面切削加工試験を実施した。
［切削条件Ａ］
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・Ｓ２５Ｃの板材
回転速度：１５００ｍｉｎ．−１、
送り：０．１５ｍｍ／ｒｅｖ、
穴深さ：１５ｍｍ、
の条件での炭素鋼の湿式穴あけ切削加工試験を行い（水溶性切削油使用）、先端切刃面の逃げ面摩耗幅が０．３ｍｍに至るまでの穴あけ加工数を測定した。
［切削条件Ｂ］
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・Ｓ４５Ｃの板材、
切削速度：３１．４ｍ／ｍｉｎ、
回転速度：１０００ｍｉｎ．−１、
切り込み： ae１．５ｍｍ、ap１５ｍｍ、
送り速度（１刃当り）：０．０７５ｍｍ／ｔｏｏｔｈ、
切削長：２００ｍ、
の条件での炭素鋼の側面切削加工試験を実施し、切刃の逃げ面摩耗幅を測定した。
表７に、これらの試験結果を示す。
For each of the above drills, a drilling test condition was carried out under the following cutting condition A, and for each of the above end mills, a side cutting test was carried out under the following cutting condition B.
[Cutting condition A]
Work Material-Plane Dimension: 100 mm x 250 mm, Thickness: 50 mm JIS / S25C Plate Rotation Speed: 1500 min. -1 ,
Feed: 0.15 mm / rev,
Hole depth: 15 mm,
Wet drilling and cutting test of carbon steel was performed under the conditions of (using water-soluble cutting oil), and the number of drilling operations until the flank wear width of the tip cutting edge surface reached 0.3 mm was measured.
[Cutting condition B]
Work material-Plane size: 100 mm x 250 mm, thickness: 50 mm JIS / S45C plate material,
Cutting speed: 31.4 m / min,
Rotation speed: 1000 min. -1 ,
Notch: ae1.5mm, ap15mm,
Feed rate (per blade): 0.075 mm / tooth,
Cutting length: 200m,
A side cutting test of carbon steel was carried out under the conditions of, and the flank wear width of the cutting edge was measured.
Table 7 shows the results of these tests.
表７に示される結果から、本発明複合材料１〜１２は、硬度、切削性能ともに、優れていることがわかる。 From the results shown in Table 7, it can be seen that the composite materials 1 to 12 of the present invention are excellent in both hardness and cutting performance.
本発明の複合材料は、硬度に優れ、かつ、鉄鋼系材料の当初表面形状を大幅に変更することはないから、本発明複合材料により、例えば、切削工具を構成した場合には、長期の使用にわたってすぐれた耐摩耗性を発揮し、切削加工の省エネ化、低コスト化、高能率化に寄与するものである。
Since the composite material of the present invention has excellent hardness and does not significantly change the initial surface shape of the steel-based material, for example, when a cutting tool is constructed by the composite material of the present invention, it can be used for a long period of time. It exhibits excellent wear resistance over a long period of time, and contributes to energy saving, cost reduction, and high efficiency of cutting.
Claims (4)
（ａ）前記ＷＣ基超硬合金付加層には、少なくとも、ＷＣ粒子が凝集する凝集組織が形成されており、
（ｂ）前記凝集組織は、前記ＷＣ基超硬合金付加層表面を含む任意の縦断面を観察した場合、（長径＋短径）／２で表される凝集組織の直径が１０μm以上６０μm以下、かつ、長径と短径の比率が１〜２の円形状の組織であり、前記凝集組織の占める面積割合は、前記ＷＣ基超硬合金付加層の面積の２０面積％以上５０面積％以下であり、
（ｃ）前記ＷＣ基超硬合金付加層を設ける以前の前記鉄鋼系材料の表面を基準面とした場合、前記ＷＣ基超硬合金層の最大侵入深さが前記鉄鋼系材料の基準面から内部へ２０μｍ以上２００μｍ以下に形成されている複合材料からなることを特徴とする切削工具。 A cutting tool made of a composite material in which a WC-based cemented carbide additional layer is provided on a part or all of the surface of a steel-based material.
(A) At least an agglomerated structure in which WC particles aggregate is formed in the WC-based cemented carbide addition layer.
(B) When observing an arbitrary vertical cross section including the surface of the WC-based cemented carbide additional layer , the aggregated structure represented by (major axis + minor axis) / 2 has a diameter of 10 μm or more and 60 μm or less. In addition, it is a circular structure with a major axis to minor axis ratio of 1 to 2, and the area ratio occupied by the aggregated structure is 20 area% or more and 50 area% or less of the area of the WC-based cemented carbide additional layer. ,
(C) When the surface of the steel-based material before the WC-based cemented carbide additional layer is provided as a reference surface, the maximum penetration depth of the WC-based cemented carbide layer is inside the reference surface of the steel-based material. cutting tool, characterized in that it consists of double coupling material that is formed in 20μm or 200μm or less to.
前記ＷＣ基超硬合金付加層の表面のビッカース硬さＨＶは１０００以上１５００以下であることを特徴とする請求項１または２に記載の切削工具。 In the cutting tool , the bonding phase of the WC-based cemented carbide addition layer contains Fe in an amount of 20 atomic% or more and 50 atomic% or less.
The cutting tool according to claim 1 or 2 , wherein the Vickers hardness HV of the surface of the WC-based cemented carbide addition layer is 1000 or more and 1500 or less.
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