JPH0343112A - Drill made of sintered hard alloy - Google Patents
Drill made of sintered hard alloyInfo
- Publication number
- JPH0343112A JPH0343112A JP17611189A JP17611189A JPH0343112A JP H0343112 A JPH0343112 A JP H0343112A JP 17611189 A JP17611189 A JP 17611189A JP 17611189 A JP17611189 A JP 17611189A JP H0343112 A JPH0343112 A JP H0343112A
- Authority
- JP
- Japan
- Prior art keywords
- cutting edge
- dispersed phase
- drill
- hard dispersed
- less
- 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.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 20
- 239000000956 alloy Substances 0.000 title claims abstract description 20
- 238000005520 cutting process Methods 0.000 claims abstract description 62
- 239000011195 cermet Substances 0.000 claims abstract description 25
- 239000002184 metal Substances 0.000 claims abstract description 22
- 229910052751 metal Inorganic materials 0.000 claims abstract description 22
- 239000000203 mixture Substances 0.000 claims abstract description 13
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 6
- 230000000737 periodic effect Effects 0.000 claims abstract description 4
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 3
- 239000010941 cobalt Substances 0.000 claims abstract description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims description 23
- 239000010936 titanium Substances 0.000 claims description 10
- 239000010419 fine particle Substances 0.000 claims description 9
- 239000011362 coarse particle Substances 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 150000002739 metals Chemical class 0.000 claims description 4
- 150000001247 metal acetylides Chemical class 0.000 claims description 2
- 150000004767 nitrides Chemical class 0.000 claims description 2
- 238000005304 joining Methods 0.000 abstract description 3
- 238000005299 abrasion Methods 0.000 abstract description 2
- 238000005336 cracking Methods 0.000 abstract description 2
- 230000008878 coupling Effects 0.000 abstract 2
- 238000010168 coupling process Methods 0.000 abstract 2
- 238000005859 coupling reaction Methods 0.000 abstract 2
- 230000000052 comparative effect Effects 0.000 description 11
- 239000000843 powder Substances 0.000 description 10
- 239000000463 material Substances 0.000 description 8
- 229910000997 High-speed steel Inorganic materials 0.000 description 7
- 238000009826 distribution Methods 0.000 description 6
- 238000005245 sintering Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000005553 drilling Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000002093 peripheral effect Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000005219 brazing Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000010730 cutting oil Substances 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000001746 injection moulding Methods 0.000 description 1
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
Landscapes
- Drilling Tools (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
この発明は、主として鋼の穿孔加工に供されるドリルの
構造に関し、特に耐摩耗性や靭性に優れ、高い品質を有
する焼結硬質合金製ドリルの構造に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to the structure of a drill mainly used for drilling steel, and in particular to a drill made of a high-quality sintered hard alloy with excellent wear resistance and toughness. This concerns the structure of the drill.
［従来の技術］
ドリルは、鋼材などの穿孔加工に用いられる切削工具の
１つである。その−例としてツイストドリルの構造が第
１図に示されている。ツイストドリルは、穿孔加工に供
される切刃部１と、切削に関与せず、主として切屑の排
出と、ボール盤などの切削機械のチャック部などに装着
するためのシャンク部２とから構成される。[Prior Art] A drill is one of the cutting tools used for drilling holes in steel materials and the like. As an example, the structure of a twist drill is shown in FIG. The twist drill consists of a cutting blade part 1 used for drilling, and a shank part 2 that does not participate in cutting but mainly serves to discharge chips and is attached to a chuck part of a cutting machine such as a drill press. .
従来より、−殻内にドリルの材質は高速度鋼（ハイス）
および超硬合金である。高速度鋼は、靭性に富むが、耐
摩耗性が低く、高速切削に不適である。一方、超硬合金
は耐摩耗性や工具としての精度特性に優れる半面、脆い
性質を有し、たとえば剛性の低い工作機械に使用される
と折損する場合があった。Conventionally, the material of the drill inside the shell is high-speed steel (HSS).
and cemented carbide. Although high-speed steel has high toughness, it has low wear resistance and is unsuitable for high-speed cutting. On the other hand, although cemented carbide has excellent wear resistance and precision characteristics as a tool, it is brittle and may break when used in, for example, machine tools with low rigidity.
これらの改良として、高速度鋼の切刃部に硬質のＴｉＮ
をコーティングする構造、あるいは切刃部を超硬合金に
し、ろう付けする構造などが考えられできた。As an improvement to these, hard TiN was added to the cutting edge of high-speed steel.
A structure in which the cutting edge is made of cemented carbide and brazed to it has been considered.
さらに近年では、耐摩耗性および靭性の向上などを意図
して、異なる月質の超硬合金同士（Ｐ２ＯとＤ３０）を
ろう付けした構造（実開昭５８−１４３１１５号）ある
いは冶金学的に一体化接合した構造（実公昭６２−４６
４８９号）、さらに、ドリルの中心部と外周部との要求
される特性の違いに着目し、その中心部と外周部との超
硬合金の材質を異ならせた二重構造に成形したもの（特
開昭６２−２１８０１０号）、あるいはこの二重構造を
射出成形で形成する方法（特開昭６３−３８５０１号、
３８５０２号）などが考案されている。Furthermore, in recent years, with the intention of improving wear resistance and toughness, structures in which cemented carbide of different quality (P2O and D30) are brazed together (Utility Model Application Publication No. 58-143115) or metallurgically integrated have been introduced. Structure that is bonded (Jikko 62-46)
489), and by focusing on the difference in required characteristics between the center and outer periphery of the drill, we developed a double-structured drill with different cemented carbide materials for the center and outer periphery (No. 489). JP-A No. 62-218010), or a method of forming this double structure by injection molding (JP-A No. 63-38501,
No. 38502), etc. have been devised.
また、ドリルの耐凝着性の向上のために、ドリルの材質
をサーメットで構成した構造（特開昭６２−２９２３０
７号）などがある。In addition, in order to improve the adhesion resistance of the drill, we have developed a structure in which the drill is made of cermet (Japanese Patent Laid-Open No. 62-29230
7) etc.
［発明が解決しようとする課題］
ドリルの切刃部およびシャンク部は各々異なった負荷状
態で使用される。そのため、ドリルの各部に要求される
特性は異なる。たとえば、切刃部の刃先部では耐摩耗性
や耐凝着性などが要求され、シャンク部では工具として
の強度を保持するための靭性が要求される。また、切刃
部の刃先部についても、その中心部と外周部とでは切削
速度が大きく異なるため、要求される特性も異なる。[Problems to be Solved by the Invention] The cutting edge portion and the shank portion of a drill are used under different load conditions. Therefore, the characteristics required for each part of the drill are different. For example, the cutting edge of the cutting edge requires wear resistance and adhesion resistance, and the shank requires toughness to maintain the strength of the tool. Further, since the cutting speed of the cutting edge portion of the cutting edge portion is greatly different between the center portion and the outer peripheral portion, the characteristics required are also different.
このようなドリルに備えられるべき特性に対する複雑な
要求に応えるため、その対策として切刃部にコーティン
グを施したものがあるが、これは、通常使用されるよう
にドリルの再研削を実施すると、少なくとも前退面側の
コーティング層が除去されてしまい、コーティングの効
果の大半が失われてしまうという欠点を有していた。ま
た、切刃部に超硬合金をろう付けする構造のものは、ろ
う付は自体が本質的に熱的強度や機械的強度に劣る方法
であり、難削材の深穴加工には適用できないという欠点
を有していた。さらに、近年、ドリルのシャンク部の靭
性を向上させる目的で、超硬合金の粗粒化や高結合相化
を行なったものは、逆に材料の強度を低下させたり、あ
るいは弾性限界の歪を低下させ、披削材のブレや切削機
械の不安定な回転などにより、穴あけ加工中においてシ
ャンク部が折損してしまうという問題があった。In order to meet these complex requirements for the characteristics that a drill should have, there are some products that have been coated on the cutting edge. This has the disadvantage that at least the coating layer on the front and rear surfaces is removed, and most of the coating effect is lost. In addition, for those with a structure in which cemented carbide is brazed to the cutting edge, brazing itself is a method that inherently has inferior thermal and mechanical strength, and cannot be applied to deep hole machining of difficult-to-cut materials. It had the following drawback. Furthermore, in recent years, in order to improve the toughness of the shank of a drill, cemented carbide has been made coarser grained or has a higher bonding phase, but this has conversely reduced the strength of the material or caused strain at the elastic limit. There was a problem in that the shank part could break during drilling due to vibration of the material to be cut or unstable rotation of the cutting machine.
そこで、この発明は上記のような問題点を解決するため
になされたもので、ドリルの切刃部において優れた耐摩
耗性、耐凝着性を有し、かつシャンク部は耐折損性とし
ての必要十分な靭性を有する焼結硬質合金で構成される
ドリルを提供することを目的とする。Therefore, this invention was made to solve the above problems.The cutting edge of the drill has excellent wear resistance and adhesion resistance, and the shank has excellent breakage resistance. It is an object of the present invention to provide a drill made of a sintered hard alloy having sufficient toughness.
［課題を解決するための手段］
この発明に従った焼結硬質合金製ドリルは、被削物を切
削するための（ａ）切刃部と、切削機械の所定位置に取
付けるための（ｂ）シャンク部とを備える。[Means for Solving the Problems] A sintered hard alloy drill according to the present invention includes (a) a cutting blade portion for cutting a workpiece, and (b) a cutting blade portion for attaching to a predetermined position of a cutting machine. and a shank part.
（ａ） 切刃部
切刃部は、サーメットより構成される。このサーメット
は、第１の硬質分散相と、第１の結合金属相とからなる
。第１の硬質分散相は、チタンと、チタンを除く周期律
表第ＩＶａ、ＶａおよびＶＩａ族金属の１種以上の炭化
物、窒化物および復炭窒化物のいずれかを主成分とする
。第１の結合金属相は、ニッケルとコバルトとを主成分
とする。第１の硬質分散相の組成は、（Ｔｉ ａＭｂ）
（ＣｃＮｄ）で表わされる。ＭはＴｉを除く周明律表第
１Ｖ ａ 。(a) Cutting Edge The cutting edge is made of cermet. This cermet consists of a first hard dispersed phase and a first bonded metal phase. The first hard dispersed phase is mainly composed of titanium and one or more carbides, nitrides, and polycarbonitrides of metals from groups IVa, Va, and VIa of the periodic table excluding titanium. The first bonding metal phase has nickel and cobalt as main components. The composition of the first hard dispersed phase is (Ti aMb)
(CcNd). M is the first V a of the Zhou Ming Table excluding Ti.
ＶａおよびＶＩａ族金属の１種以上である。ａ、ｂ。One or more of group Va and VIa metals. a, b.
ｃ、ｄはモル分率を示す。ａ、 ｂ、 ｃ、 ｄ
は、以下の関係式で規定される。c and d indicate the molar fraction. a, b, c, d
is defined by the following relational expression.
ａ＋ｂ嘩１
ｃ＋ｄｍ１
０．５≦ａ≦０．９５
０．１≦ｄ≦０． ７
第１の硬質分散相は、微粒子群と、粗粒子群とを少なく
とも備える。微粒子群の平均粒径は０゜２μｍ以上０．
６μｍ以下である。粗粒子群の平均粒径は１μｍ以上
３μｍ以下である。微粒子群の粗粒子群に対する体積比
は０．３以上３以下である。第１の結合金属相は、サー
メット中に占める割合が５重量％以上３０重量％以下で
ある。a+b fight 1 c+dm1 0.5≦a≦0.95 0.1≦d≦0. 7 The first hard dispersed phase includes at least a group of fine particles and a group of coarse particles. The average particle diameter of the fine particles is 0.2 μm or more.
It is 6 μm or less. The average particle diameter of the coarse particle group is 1 μm or more and 3 μm or less. The volume ratio of the fine particles to the coarse particles is 0.3 or more and 3 or less. The proportion of the first binding metal phase in the cermet is 5% by weight or more and 30% by weight or less.
（ｂ） シャンク部
シャンク部は、切刃部と一体に接合される。シャンク部
は、超硬合金より構成される。超硬合金は、ＷＣ粒子の
第２の硬質分散相とＣｏを含有する第２の結合金属相と
からなる。第２の硬質分散相の平均粒径は、０．７μｍ
以下である。第２の結合金属相は、超硬合金中に占める
割合が１３体積％以上３０体積％以下である。(b) Shank portion The shank portion is integrally joined to the cutting edge portion. The shank portion is made of cemented carbide. The cemented carbide consists of a second hard dispersed phase of WC particles and a second bonded metal phase containing Co. The average particle size of the second hard dispersed phase is 0.7 μm
It is as follows. The second binding metal phase occupies 13% by volume or more and 30% by volume or less in the cemented carbide.
［作用］
ドリルに要求される特性は、切刃部の耐摩耗性および耐
凝着性と、シャンク部の靭性に代表される耐折損性とに
大別される。これらのドリルに要求される特性のうち、
特に耐摩耗性および耐凝着性の向上に着目して、本願発
明者等はチタン（Ｔｉ）を主成分とした窒素含有サーメ
ットを刃先部に適用することが必須であると着想した。[Function] The properties required of a drill are broadly divided into wear resistance and adhesion resistance of the cutting edge, and breakage resistance represented by toughness of the shank. Among the characteristics required for these drills,
In particular, with a focus on improving wear resistance and adhesion resistance, the inventors of the present invention came up with the idea that it is essential to apply a nitrogen-containing cermet containing titanium (Ti) as a main component to the cutting edge.
そこで種々のサーメットの組成に対し実験を行ない、多
くの有効な知見を得た。また、一方、靭性および強度が
要求されるドリルのシャンク部にＷＣ系超硬合金を適用
することが好ましいとの知見も得た。Therefore, we conducted experiments on various cermet compositions and obtained many useful findings. On the other hand, it has also been found that it is preferable to apply WC-based cemented carbide to the shank portion of a drill, which requires toughness and strength.
本願発明は、これらの知見に基づいてなされたもので、
ドリルの切刃部に対して耐摩耗性、耐凝着性の優れたサ
ーメットを適用し、さらにシャンク部に対しては靭性に
優れたＷＣ系超硬合金を適用し、これらの両者を一体に
接合した構造を有するドリルを提供するものである。以
下、本発明に従った焼結硬質合金製ドリルにおいて組成
、粒径等の限定理由について説明する。The present invention was made based on these findings,
A cermet with excellent wear resistance and adhesion resistance is applied to the cutting edge of the drill, and a WC-based cemented carbide with excellent toughness is applied to the shank, both of which are integrated into one. A drill having a joined structure is provided. The reasons for limiting the composition, grain size, etc. in the sintered hard alloy drill according to the present invention will be explained below.
（ａ） 切刃部 ドリルにおける摩耗の発生状態は、第３図に示される。(a) Cutting edge part The state of wear in the drill is shown in FIG.
１１はドリル内周部の凝着摩耗が発生する部位（すくい
面）を示す。被削材とドリル材質の凝着によるすくい面
の摩耗が進行すると、切屑が付着し、ドリルか寿命に至
る。１２はドリル外周刃の摩耗部位（マージン）、１３
は刃先のチッピング発生部位（前透面）を示す。この発
明においては耐摩耗性および耐凝着性を向上させるため
に、硬質分散相の組成および粒径が限定されている。Reference numeral 11 indicates a portion (rake face) where adhesive wear occurs on the inner circumference of the drill. As the rake face wears down due to adhesion between the workpiece and the drill material, chips will adhere to it and the drill will reach the end of its life. 12 is the wear area (margin) of the drill peripheral cutting edge, 13
indicates the part where chipping occurs on the cutting edge (front transparent surface). In this invention, the composition and particle size of the hard dispersed phase are limited in order to improve wear resistance and adhesion resistance.
硬質分散相に含まれる金属原子群中のチタンの量はモル
分率で０． ５〜０．９５の範囲に限定される。０６５
未満では、耐摩耗性および耐凝着性が低下する。また、
０．９５を越えると、サーメット自体の焼結性が劣化す
る。The amount of titanium in the metal atom group contained in the hard dispersed phase is 0. It is limited to a range of 5 to 0.95. 065
If it is less than that, abrasion resistance and adhesion resistance will decrease. Also,
If it exceeds 0.95, the sinterability of the cermet itself deteriorates.
硬質分散相に含まれる非金属原子群中の窒素の割合がモ
ル分率で０，１〜０．７の範囲に限定される。０．１未
満では、窒素がサーメットの焼結時において硬質分散相
の粒成長を抑制するという効果が見られなくなる。また
、０．７を越えると、サーメット自体の焼結性が劣化す
る。The proportion of nitrogen in the nonmetallic atomic group contained in the hard dispersed phase is limited to a range of 0.1 to 0.7 in molar fraction. If it is less than 0.1, nitrogen will not have the effect of suppressing grain growth of the hard dispersed phase during sintering of cermet. Moreover, when it exceeds 0.7, the sinterability of the cermet itself deteriorates.
硬質分散相は、０．２〜０．６μｍの粒径を有する微粒
子群と、１〜３μｍの粒径を有する粗粒子群との混合体
からなる。微粒子群の粗粒子群に対する体積比は０．３
〜３の範囲に限定される。The hard dispersed phase consists of a mixture of fine particles having a particle size of 0.2 to 0.6 μm and coarse particles having a particle size of 1 to 3 μm. The volume ratio of fine particles to coarse particles is 0.3
-3.
この体積比率が０． ３未満においては、サーメット自
体の靭性が劣化し、ドリルの刃先部に、チッピングが発
生する。また、この体積比率が３．０を越えると、ドリ
ルの刃先に熱亀裂か発生する。This volume ratio is 0. If it is less than 3, the toughness of the cermet itself deteriorates and chipping occurs at the cutting edge of the drill. Moreover, if this volume ratio exceeds 3.0, thermal cracks will occur at the cutting edge of the drill.
結合金属相の量は５〜３０重量％の範囲に限定される。The amount of bound metal phase is limited to a range of 5-30% by weight.
５重量％未満においては、サーメット自体の靭性が不足
し、ドリルの刃先にチッピングが発生する。また、３０
重量％を越えると、耐摩耗性が不足し、刃先の透面やマ
ージン部に大きな摩耗が発生する。If it is less than 5% by weight, the toughness of the cermet itself will be insufficient and chipping will occur on the cutting edge of the drill. Also, 30
If it exceeds this weight percent, wear resistance will be insufficient and large wear will occur on the transparent surface and margin of the cutting edge.
（ｂ） シャンク部
この発明のドリルのシャンク部には、硬質分散相として
平均粒径が０．７μｍ以下のＷＣ粒子を含むＷＣ系超硬
合金が用いられる。高速度鋼等を用いると、その熱膨張
係数が大きいため、切刃部のサーメットとの熱膨張差に
起因した切刃部の切刃部が発生しやすい。また、高速度
鋼のヤング率はＷＣ系超硬合金の約１７３であり、切削
時の耐振性が悪いため、切刃部の摩耗、欠損を助長する
ことになる。(b) Shank Part For the shank part of the drill of the present invention, a WC-based cemented carbide containing WC particles with an average particle size of 0.7 μm or less as a hard dispersed phase is used. When high-speed steel or the like is used, since its coefficient of thermal expansion is large, a cutting edge is likely to occur in the cutting edge due to a difference in thermal expansion between the cutting edge and the cermet. Furthermore, the Young's modulus of high-speed steel is about 173 compared to that of WC-based cemented carbide, which has poor vibration resistance during cutting, which promotes wear and chipping of the cutting edge.
硬質分散相の平均粒径が０．７μｍを越えると、ドリル
のシャンク部としての強度が耐折損性を満足し得るよう
には発揮されない。結合金属相の量が１３体積％以下に
なると、靭性が低下し、３０体積％を越えると、塑性変
形を示し、好ましくない。If the average particle size of the hard dispersed phase exceeds 0.7 μm, the strength of the shank portion of the drill will not be sufficient to satisfy the breakage resistance. If the amount of the bonding metal phase is less than 13% by volume, the toughness will decrease, and if it exceeds 30% by volume, plastic deformation will occur, which is not preferable.
［実施例］ 以下、この発明の実施例について説明する。[Example] Examples of the present invention will be described below.
本発明における焼結硬質合金製ドリルは、切刃部にサー
メット合金を用い、シャンク部にＷＣ超硬合金を用いて
、粉体の成形プレス時に接合し、焼結することにより形
成される。切刃部を構成するサーメット合金は、硬質分
散相の組成、結合相の組成および硬質分散相の粒度存在
比が、焼結後において第１表に示される数値となるよう
に、各種粉末を調合することによって作製された。シャ
ンク部を構成する超硬合金は、平均粒径０，５μｍのＷ
Ｃ粉末およびＣｏ粉末を、結合金属（体積％）、硬質分
散相平均粒径（μｍ）が、焼結後において第１表に示さ
れる数値となるように、調合することによって作製され
た。このとき、粒成長抑制成分としてＶＣ粉末を少量配
合した。The sintered hard alloy drill according to the present invention is formed by using a cermet alloy for the cutting edge part and a WC cemented carbide for the shank part, joining them during powder forming press, and sintering them. The cermet alloy that constitutes the cutting edge is prepared by mixing various powders so that the composition of the hard dispersed phase, the composition of the binder phase, and the particle size abundance ratio of the hard dispersed phase become the values shown in Table 1 after sintering. It was created by The cemented carbide forming the shank part is W with an average grain size of 0.5 μm.
It was produced by blending C powder and Co powder so that the binding metal (volume %) and hard dispersed phase average particle size (μm) became the values shown in Table 1 after sintering. At this time, a small amount of VC powder was added as a grain growth inhibiting component.
なお、第２図は、ドリルの切刃部を構成するサーメット
合金において、硬質分散相の粒度分布を示す。Ａは、微
粒子の存在度数分布を示し、Ｂは粗粒子の存在度数分布
を示す。微粒子群の粗粒子群に対する体積比はＡ／Ｂで
第１表に表わされている。Note that FIG. 2 shows the particle size distribution of the hard dispersed phase in the cermet alloy that constitutes the cutting edge of the drill. A shows the frequency distribution of fine particles, and B shows the frequency distribution of coarse particles. The volume ratio of the fine particles to the coarse particles is expressed in Table 1 as A/B.
切刃部を構成するサーメット合金粉末と、シャンク部を
構成する超硬合金粉末とを、粉体の成形プレス時におい
て接合した。具体的には、静水圧プレスを用いて、いわ
ゆるＣＩＰ（Ｃｏｌｄ ｌ５ｏｓｔａｔｉｃ Ｐｒ
ｅｓｓｉｎｇ）によって焼結前において各合金粉末を接
合した。その後、得られた成形体を焼結することにより
サーメット合金と超硬合金とが一体に接合された焼結硬
質合金を作製した。各試料に研削加工を施すことによっ
て１０ｍｍφのドリルが得られた。The cermet alloy powder constituting the cutting edge portion and the cemented carbide powder constituting the shank portion were joined during the powder forming press. Specifically, using a hydrostatic press, so-called CIP (Cold l5ostatic Pr)
Each alloy powder was bonded before sintering. Thereafter, the obtained compact was sintered to produce a sintered hard alloy in which the cermet alloy and the cemented carbide were integrally joined. A drill with a diameter of 10 mm was obtained by grinding each sample.
また、比較品として、第１表に示されるように粉末の粒
度および配合比を変化させることによって上記と同様の
方法で１０ｍｍφのドリルを作製した。In addition, as a comparison product, a 10 mm diameter drill was manufactured in the same manner as above by changing the particle size and blending ratio of the powder as shown in Table 1.
第１表には、本発明の焼結硬質合金製ドリルおよび比較
のために作製されたドリルの硬質合金の組成および粒度
分布などが示されている。第１表において、比較品りは
、＊で示されるように切刃部の硬質分散相の組成および
粒度存在比が本発明の範囲から外れるように作製された
ものである。Table 1 shows the composition and particle size distribution of the hard alloy of the sintered hard alloy drill of the present invention and a drill prepared for comparison. In Table 1, the comparative products were manufactured so that the composition and particle size abundance ratio of the hard dispersed phase in the cutting edge were outside the range of the present invention, as indicated by *.
また、比較品Ｅは、シャンク部を構成する硬質相の粒径
が本発明の範囲を外れるように作製されたものである。Comparative product E was manufactured so that the particle size of the hard phase constituting the shank portion was outside the range of the present invention.
さらに、比較品Ｆは、切刃部を構成する硬質分散相の粒
度存在比が本発明の範囲を外れるように作製されたもの
である。比較品Ｇは、切刃部とシャンク部との両者にお
いて結合金属相の量が本発明の範囲を外れるように作製
されたものである。比較品Ｈは、切刃部を構成する結合
金属相の量が本発明の範囲を外れるように作製されたも
のである。それぞれ本発明の範囲から外れている数値に
は＊が付されている。Furthermore, comparative product F was manufactured so that the particle size abundance ratio of the hard dispersed phase constituting the cutting edge portion was outside the range of the present invention. Comparative product G was manufactured so that the amount of the bonded metal phase in both the cutting edge portion and the shank portion was outside the range of the present invention. Comparative product H was manufactured so that the amount of the bonded metal phase constituting the cutting edge portion was outside the range of the present invention. Values outside the scope of the present invention are marked with *.
（以下余白）
ドリルの性能評価テストは以下に示される条件下で行な
われた。(Left below) Performance evaluation tests for the drill were conducted under the conditions shown below.
テスト条件
被削材： ５５０Ｃ（Ｈａ ＝２３０）切削速度：６０
ｍ／分、湿式（水溶性切削油）送り速度： ０． ２５
ｍｍ／ ｒ ｅ ｖ。Test conditions Work material: 550C (Ha = 230) Cutting speed: 60
m/min, wet (water-soluble cutting oil) feed rate: 0. 25
mm/rev.
深さ：２５ｍｍ
判定基準：寿命まで加工後、その刃先状況などを観察す
る。Depth: 25mm Judgment criteria: After machining to the end of its life, observe the condition of the cutting edge.
寿命：ａ常、外周前退面の摩耗量が０．２ｍｍ以上にな
ったときとする。Lifespan: (a) Defined when the amount of wear on the front and back surfaces of the outer periphery reaches 0.2 mm or more.
上記のドリル性能評価テストの結果は第２表に示される
。第２表を参照して、まず、本発明品Ａ〜Ｃと比較品り
との比較において、比較品りは、切刃部を構成するサー
メットの靭性が劣化し、刃先部にチッピングが生じた。The results of the above drill performance evaluation test are shown in Table 2. Referring to Table 2, first, in a comparison between products A to C of the present invention and the comparison product, the toughness of the cermet constituting the cutting edge portion of the comparison product deteriorated, and chipping occurred at the cutting edge portion. .
また、本発明品Ａ−Ｃと比較品Ｅとの比較において、比
較品Ｅはシャンク強度に劣り、シャンク部が折損した。Further, in a comparison between products A-C of the present invention and comparative product E, comparative product E was inferior in shank strength, and the shank portion was broken.
本発明品Ａ−Ｃと比較品Ｆ、 Ｇとの比較において、比
較品Ｆ、 Ｇはサーメットの靭性が不足し、ドリルの刃
先が欠けた。In a comparison between products A-C of the present invention and comparative products F and G, the toughness of the cermet in Comparative products F and G was insufficient, and the cutting edge of the drill was chipped.
本発明品Ａ−Ｃと比較品Ｈとの比較において、比較品Ｈ
は耐摩耗性か不足し、少ない穴あけ個数で刃先が所定の
摩耗量を示した。In a comparison between products A-C of the present invention and comparative product H, comparative product H
The wear resistance was insufficient, and the cutting edge showed a certain amount of wear even after a small number of holes were drilled.
さらに、参考のために現在使用されているコーティング
ハイスあるいはコーティング超硬ドリルも併せて本性能
試験が行なわれた。これらのドリルと本発明品Ａ−Ｃの
ドリルとの比較において、本発明品のドリルの性能か優
れていることは明らかである。Furthermore, for reference, the performance test was also conducted with coated high speed steel or coated carbide drills that are currently in use. In comparing these drills with drills A to C of the present invention, it is clear that the drills of the present invention have superior performance.
（以下余白）
［発明の効果］
以上のように、本発明においては、ドリルの刃先部に耐
摩耗性、耐凝着性あるいは耐熱亀裂性（耐チッピング性
）に優れる特定の組成を有するるサーメット合金を用い
、ドリルのシトンク部に靭性に富むＷＣ超硬合金を用い
て、これらの両者を一体接合させることによってドリル
を成形している。したがって、突発的な折損等が発生す
ることのない高い信頼性、長い寿命および高い品質を有
する焼結硬質合金製ドリルが提供され得る。(The following is a blank space) [Effects of the Invention] As described above, in the present invention, a cermet having a specific composition that has excellent wear resistance, adhesion resistance, or heat cracking resistance (chipping resistance) is used at the cutting edge of a drill. The drill is formed by using a WC cemented carbide, which has high toughness, in the seat part of the drill, and integrally joining these two together. Therefore, it is possible to provide a sintered hard alloy drill that is highly reliable, has a long lifespan, and has high quality without causing any accidental breakage.
第１図は、−殻内なツイストドリルを示す構造図である
。
第２図は、この発明に従ったドリルの切刃部を構成する
サーメット合金において硬質分散相の粒度分布を示す分
布図である。
第３図は、ドリルの代表的な損傷部位を示す図である。
図において、１は切刃部、２はシャンク部である。
第
図
第２図
２ニジ持コク香Ｐ
石更Ｖ方１ｙ木目華立魔］ア川）FIG. 1 is a structural diagram showing an in-shell twist drill. FIG. 2 is a distribution diagram showing the particle size distribution of the hard dispersed phase in the cermet alloy constituting the cutting edge portion of the drill according to the present invention. FIG. 3 is a diagram showing typical damaged parts of the drill. In the figure, 1 is a cutting edge portion, and 2 is a shank portion. Fig. 2 Fig. 2 Niji-rich incense P
Claims (1)
に取付けるためのシャンク部とを備えた焼結硬質合金製
ドリルにおいて、 前記切刃部は、 チタンと、チタンを除く周期律表第IVａ、ＶａおよびV
Iａ族金属の１種以上の炭化物、窒化物および複炭窒化
物のいずれかを主成分とする第１の硬質分散相と、ニッ
ケルとコバルトとを主成分とする第１の結合金属相とか
らなるサーメットより構成され、 前記第１の硬質分散相の組成が、（ＴｉａＭｂ）（Ｃｃ
Ｎｄ）［但し、ＭはＴｉを除く周期律表第IVａ、Ｖａお
よびVIａ族金属の１種以上であり、ａ、ｂ、ｃ、ｄはモ
ル分率を示し、ａ＋ｂ＝１、ｃ＋ｄ＝１、０．５≦ａ≦
０．９５、０．１≦ｄ≦０．７］で表わされ、前記第１
の硬質分散相は、その平均粒径が０．２μｍ以上０．６
μｍ以下の微粒子群と、その平均粒径が１μｍ以上３μ
ｍ以下の粗粒子群とを少なくとも備え、前記微粒子群の
前記粗粒子群に対する体積比が０．３以上３以下であり
、 前記第１の結合金属相は、前記サーメット中に占める割
合が５重量％以上３０重量％以下であり、前記シャンク
部は、 前記切刃部と一体に接合され、ＷＣ粒子の第２の硬質分
散相とＣｏを含有する第２の結合金属相とからなる超硬
合金より構成され、 前記第２の硬質分散相の平均粒径は、０．７μｍ以下で
あり、前記第２の結合金属相は、前記超硬合金中に占め
る割合が１３体積％以上３０体積％以下であることを特
徴とする、焼結硬質合金製ドリル。[Claims] A sintered hard alloy drill comprising a cutting edge for cutting a workpiece and a shank for attaching to a predetermined position of a cutting machine, the cutting edge being made of titanium. , Periodic Table IVa, Va and V excluding titanium
A first hard dispersed phase whose main component is one or more carbides, nitrides, or double carbonitrides of Group Ia metals; and a first bonded metal phase whose main components are nickel and cobalt. The composition of the first hard dispersed phase is (TiaMb) (Cc
Nd) [However, M is one or more metals from Groups IVa, Va, and VIa of the periodic table excluding Ti, a, b, c, and d indicate molar fractions, a+b=1, c+d=1, 0.5≦a≦
0.95, 0.1≦d≦0.7], and the first
The hard dispersed phase has an average particle size of 0.2 μm or more and 0.6
A group of fine particles of 1 μm or less and an average particle size of 1 μm or more and 3 μm
m or less, the volume ratio of the fine particles to the coarse particles is 0.3 or more and 3 or less, and the first binding metal phase accounts for 5% by weight in the cermet. % or more and 30% by weight or less, and the shank portion is integrally joined to the cutting edge portion and is a cemented carbide comprising a second hard dispersed phase of WC particles and a second bonding metal phase containing Co. The second hard dispersed phase has an average particle size of 0.7 μm or less, and the second binding metal phase accounts for 13% by volume or more and 30% by volume or less in the cemented carbide. A sintered hard alloy drill characterized by:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17611189A JPH0343112A (en) | 1989-07-07 | 1989-07-07 | Drill made of sintered hard alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17611189A JPH0343112A (en) | 1989-07-07 | 1989-07-07 | Drill made of sintered hard alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0343112A true JPH0343112A (en) | 1991-02-25 |
Family
ID=16007881
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17611189A Pending JPH0343112A (en) | 1989-07-07 | 1989-07-07 | Drill made of sintered hard alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0343112A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20100290849A1 (en) * | 2009-05-12 | 2010-11-18 | Tdy Industries, Inc. | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
| US8841005B2 (en) | 2006-10-25 | 2014-09-23 | Kennametal Inc. | Articles having improved resistance to thermal cracking |
| US8858870B2 (en) | 2008-08-22 | 2014-10-14 | Kennametal Inc. | Earth-boring bits and other parts including cemented carbide |
| US9016406B2 (en) | 2011-09-22 | 2015-04-28 | Kennametal Inc. | Cutting inserts for earth-boring bits |
| US9266171B2 (en) | 2009-07-14 | 2016-02-23 | Kennametal Inc. | Grinding roll including wear resistant working surface |
| JP2016030314A (en) * | 2014-07-29 | 2016-03-07 | 京セラ株式会社 | Blank for drill, method of manufacturing the same, and drill |
| US9643236B2 (en) | 2009-11-11 | 2017-05-09 | Landis Solutions Llc | Thread rolling die and method of making same |
| JPWO2018092187A1 (en) * | 2016-11-15 | 2019-10-10 | 住友電工ハードメタル株式会社 | Cutting tools |
-
1989
- 1989-07-07 JP JP17611189A patent/JPH0343112A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8841005B2 (en) | 2006-10-25 | 2014-09-23 | Kennametal Inc. | Articles having improved resistance to thermal cracking |
| US8858870B2 (en) | 2008-08-22 | 2014-10-14 | Kennametal Inc. | Earth-boring bits and other parts including cemented carbide |
| US20100290849A1 (en) * | 2009-05-12 | 2010-11-18 | Tdy Industries, Inc. | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
| US8272816B2 (en) * | 2009-05-12 | 2012-09-25 | TDY Industries, LLC | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
| US20120282051A1 (en) * | 2009-05-12 | 2012-11-08 | TDY Industries, LLC | Composite Cemented Carbide Rotary Cutting Tools and Rotary Cutting Tool Blanks |
| US8876443B2 (en) | 2009-05-12 | 2014-11-04 | Kennametal Inc. | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
| US9435010B2 (en) | 2009-05-12 | 2016-09-06 | Kennametal Inc. | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
| US9266171B2 (en) | 2009-07-14 | 2016-02-23 | Kennametal Inc. | Grinding roll including wear resistant working surface |
| US9643236B2 (en) | 2009-11-11 | 2017-05-09 | Landis Solutions Llc | Thread rolling die and method of making same |
| US9016406B2 (en) | 2011-09-22 | 2015-04-28 | Kennametal Inc. | Cutting inserts for earth-boring bits |
| JP2016030314A (en) * | 2014-07-29 | 2016-03-07 | 京セラ株式会社 | Blank for drill, method of manufacturing the same, and drill |
| JPWO2018092187A1 (en) * | 2016-11-15 | 2019-10-10 | 住友電工ハードメタル株式会社 | Cutting tools |
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