JPH0551267A - Sintering material for tool - Google Patents
Sintering material for toolInfo
- Publication number
- JPH0551267A JPH0551267A JP3209635A JP20963591A JPH0551267A JP H0551267 A JPH0551267 A JP H0551267A JP 3209635 A JP3209635 A JP 3209635A JP 20963591 A JP20963591 A JP 20963591A JP H0551267 A JPH0551267 A JP H0551267A
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- Prior art keywords
- binder phase
- volume
- cbn
- tool
- hard
- Prior art date
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、焼入鋼や超硬合金等の
高硬度材料或いは耐熱合金等の切削加工や塑性加工の際
に用いられる工具用焼結材料に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a sintered material for tools used in cutting and plastic working of high hardness materials such as hardened steel and cemented carbide or heat resistant alloys.
【０００２】[0002]
【従来の技術】焼入鋼或いはニッケル基耐熱合金やコバ
ルト基耐熱合金等の高硬度材料を加工する場合、一般に
はタングステン等の高融点金属の炭化物粉末を鉄やコバ
ルトやニッケル等の鉄系金属で焼結結合させた超硬合金
が利用されて来た。近年、上述した超硬合金が工具とし
てではなく、加工対象物として採用されつつあることに
加え、加工条件に対する厳しい要求に対応するため、よ
り高性能な工具として焼結ダイヤモンドや立方晶窒化硼
素（以下、ＣＢＮと記述する）焼結体等を用いたものが
開発されている。焼結ダイヤモンドは、ダイヤモンドの
粉粒を超硬合金を結合剤として高温高圧下で焼結したも
のであるが、炭素との親和力が強い鋼等の加工には根本
的に不向きである。この点、ダイヤモンドに次ぐ硬度の
ＣＢＮ焼結体は鉄系金属との反応が少ないことから、ダ
イヤモンド以外のあらゆる加工対象物、特に焼入鋼や超
硬合金等の高硬度材料の他にニッケル基耐熱合金やコバ
ルト基耐熱合金等の加工に有効である。2. Description of the Related Art When processing hardened steel or high hardness materials such as nickel-base heat-resistant alloys and cobalt-base heat-resistant alloys, generally, carbide powder of refractory metal such as tungsten is used for iron-based metals such as iron, cobalt and nickel. Cemented carbide cemented by sinter has been used. In recent years, the above-mentioned cemented carbide is being adopted not as a tool but as an object to be processed, and in order to meet severe requirements for processing conditions, sintered diamond and cubic boron nitride ( Hereinafter, those using a sintered body or the like will be developed. Sintered diamond is obtained by sintering diamond powder particles under high temperature and high pressure using cemented carbide as a binder, but is fundamentally unsuitable for processing steel or the like having a strong affinity with carbon. In this respect, the CBN sintered body, which has the second highest hardness after diamond, has little reaction with iron-based metals, so it can be applied to all processed objects other than diamond, especially hardened materials such as hardened steel and cemented carbide, as well as nickel-based materials. It is effective for processing heat-resistant alloys and cobalt-based heat-resistant alloys.
【０００３】従来のＣＢＮ焼結体は、ＣＢＮの粉粒に結
合相となる炭化チタンや窒化チタン等のセラミックスを
単独で混ぜ、焼結性の改善のため金属成分を添加してこ
れらを高温高圧下で焼結したものがほとんどである。結
合相の材料としては、上記の他に硅素やジルコニウムの
炭化物或いは硅素やジルコニウムの窒化物、更にはアル
ミニウムとチタンとの金属間化合物やアルミニウムとジ
ルコニウムとの金属間化合物等が知られている。In a conventional CBN sintered body, ceramics such as titanium carbide and titanium nitride, which serve as a binder phase, are mixed alone with CBN powder particles, and a metal component is added to improve the sinterability, and these are mixed at high temperature and high pressure. Most are sintered below. As the material of the binder phase, in addition to the above, carbides of silicon or zirconium, nitrides of silicon or zirconium, intermetallic compounds of aluminum and titanium, intermetallic compounds of aluminum and zirconium, and the like are known.
【０００４】[0004]
【発明が解決しようとする課題】従来のＣＢＮ焼結体を
用いた工具では、高温領域下で結合相の硬度低下が発生
するため、工具自体が高温となるような加工の際には、
結合相からのＣＢＮの粉粒の脱落が起こり易く、耐摩耗
性の低下を招来するものが多い。又、このような工具を
長時間の自動運転を行う加工機械に組込む場合、突発的
な工具欠損が発生することは、加工機械等の損傷や設備
稼動率の低下等の点で絶対に避けるべきであるが、従来
のこの種のＣＢＮ焼結体は高い耐摩耗性を追求するあま
り、靱性が充分なものとは云えなかった。In the tool using the conventional CBN sintered body, the hardness of the binder phase is lowered in the high temperature region. Therefore, when the tool itself is heated to a high temperature,
The powder particles of CBN tend to fall off from the binder phase, often leading to a decrease in wear resistance. In addition, when such a tool is incorporated into a processing machine that performs automatic operation for a long time, it is absolutely necessary to avoid sudden tool loss from damage to the processing machine or a decrease in equipment operating rate. However, the conventional CBN sintered body of this kind has not been sufficiently tough enough to pursue high wear resistance.
【０００５】本発明はこのような事情に鑑み、結合相の
ＣＢＮ等の硬質粉粒の担持能力を向上させ、特に高温時
での耐摩耗性を改善した工具用焼結材料を提供すること
を目的とする。In view of such circumstances, the present invention provides a sintered material for a tool, which has an improved ability to carry hard powder particles such as CBN in the binder phase and which has improved wear resistance particularly at high temperatures. To aim.
【０００６】[0006]
【課題を解決するための手段】前記目的を達成するため
に種々検討を重ねた結果、結合相として、窒化チタンを
主成分とすると共に酸化アルミニウムに酸化ジルコニウ
ム、窒化アルミニウム及び炭化硅素の針状結晶を一定比
率で添加した混合粉粒を副成分としたものを用い、さら
に立方晶窒化硼素の粉粒に結合相成分と同一、あるいは
各結合相成分の金属元素の他の化合物の被膜を施すこと
により、結合相のＣＢＮ粉粒の担持能力が上昇し、耐摩
耗性、耐欠損性が向上することを知見した。また、結合
相成分と同一、あるいは各結合相成分の金属元素の他の
化合物の被膜を施すことにより、耐摩耗性、耐欠損性が
向上するという効果は、ＣＢＮ粉粒の他、ダイヤモンド
粉粒などの硬質粉粒と、金属元素の窒化物、硼化物、炭
化物、及びこれらの複合物から選ばれた結合相とからな
る工具用焼結材料において発現することを知見した。本
発明はかかる知見に基づいてなされたものであり、本発
明に係る工具用焼結材料は、立方晶窒化硼素、ダイヤモ
ンドなどの硬質粉粒と、金属元素の窒化物、硼化物、炭
化物、及びこれらの複化物から選ばれた結合相とからな
る工具用焼結材料において、上記硬質粉粒に結合相成分
と同一、あるいは各結合相成分の金属元素の他の化合物
の被膜を施したことを特徴とし、また、立方晶窒化硼素
の粉粒４０〜７０体積％と、結合相の主成分となる窒化
チタン１５〜４５体積％と、結合相の副成分となる酸化
アルミニウム、酸化ジルコニウム、窒化アルミニウム及
び炭化硅素の針状結晶との混合粉粒１５〜３５体積％と
からなる組成を有し、且つ上記結合相の副成分の組成が
酸化アルミニウム５０〜６５体積％、酸化ジルコニウム
１〜５体積％、窒化アルミニウム２０〜４０体積％及び
炭化硅素の針状結晶５〜１５体積％の比率となる工具用
焼結材料であって、立方晶窒化硼素の粉粒に結合相成分
と同一、あるいは各結合相成分の金属元素の他の化合物
の被膜を施したことを特徴とする。[Means for Solving the Problems] As a result of various studies to achieve the above object, needle crystals of zirconium oxide, aluminum nitride and silicon carbide containing titanium nitride as a main component and aluminum oxide as a binder phase. Using a mixed powder grain added as a sub-component at a fixed ratio, and further coating the cubic boron nitride powder grain with the same as the binder phase component or other compound of the metal element of each binder phase component. It was found that, by this, the capability of supporting CBN powder particles in the binder phase is increased, and the wear resistance and fracture resistance are improved. Further, the effect of improving wear resistance and fracture resistance by applying a coating of the same compound as the binder phase component or another compound of the metal element of each binder phase component is that diamond powder grains as well as CBN powder grains are effective. It has been found that it is developed in a sintered material for tools, which is composed of hard powder particles such as the above and a binder phase selected from nitrides of metal elements, borides, carbides, and composites thereof. The present invention has been made based on such findings, the sintered material for a tool according to the present invention, cubic boron nitride, hard powder particles such as diamond, nitride of metal elements, boride, carbide, and In a sintered material for tools comprising a binder phase selected from these compounds, the hard powder particles are coated with the same binder component as the binder phase, or with a coating of another compound of a metal element of each binder phase component. Characteristically, 40 to 70% by volume of cubic boron nitride powder particles, 15 to 45% by volume of titanium nitride which is the main component of the binder phase, and aluminum oxide, zirconium oxide and aluminum nitride which are the minor components of the binder phase. And 15 to 35% by volume of mixed powder particles with acicular crystals of silicon carbide, and the composition of the auxiliary components of the binder phase is 50 to 65% by volume of aluminum oxide and 1 to 5% by volume of zirconium oxide. , A sintered material for a tool having a ratio of 20 to 40% by volume of aluminum nitride and 5 to 15% by volume of needle crystals of silicon carbide, which is the same as the binder phase component in the powder particles of cubic boron nitride, or each binder phase. It is characterized in that a film of another compound of a metal element as a component is applied.
【０００７】なお、本発明において、硬質粉粒に施す被
膜は、例えばＣＶＤ法で形成すればよい。また、ＣＢＮ
粉粒に施す被膜は、特にＴｉＮX （ｘ＝0.９〜1.１）の
組成が好ましい。In the present invention, the coating applied to the hard powder particles may be formed by, for example, the CVD method. Also, CBN
The composition applied to the powder particles is preferably TiN x (x = 0.9 to 1.1).
【０００８】ここで、本発明を、従来のＣＢＮ焼結工具
と比較しつつ説明する。The invention will now be described in comparison with conventional CBN sintering tools.
【０００９】まず、従来のＣＢＮ焼結工具の摩耗状況を
図面を参照しながら説明する。図５（ａ），（ｂ）は焼
入鋼を切削したときのＣＢＮ焼結工具の逃げ面及びすく
い面の摩耗状況を模式的に示すものである。両図に示す
ように、切削過程において、工具刃先部１０のＣＢＮ粒
１１が結合相１２から脱落し、脱落したＣＢＮ粒１１が
被削材１３と逃げ面１０ａとの境界を通過する際に、逃
げ面１０ａに条痕ａが残こされ、この条痕ａが逃げ面摩
耗幅（ＶB ）、すなわち耐摩耗性を決めていると考えら
れる。なお、図中、１０ｂはすくい面を示す。そして、
このＣＢＮ粒１１の脱落は、該ＣＢＮ粒１１を担持する
機能を有する刃先部の結合相１２の被削材１３に接して
いる部位が摩耗により後退し、外力（切削力、熱応力
等）がＣＢＮ粒１１を担持する力を越えた段階で、ＣＢ
Ｎ粒１１と結合相１２との粒界での剥離、あるいは結合
相１２の切損によりＣＢＮ粒が刃先部１０から脱落する
と考えられる。また、このようなことから、ＣＢＮ焼結
工具では、ＣＢＮ粒は切刃として、また、結合相はその
切刃の担持体としての機能を有するものと考えられる。First, the wear condition of a conventional CBN sintering tool will be described with reference to the drawings. FIGS. 5 (a) and 5 (b) schematically show the wear condition of the flank and rake face of the CBN sintering tool when the hardened steel is cut. As shown in both figures, in the cutting process, when the CBN grains 11 of the tool edge portion 10 fall off from the binder phase 12, and the dropped CBN grains 11 pass through the boundary between the work material 13 and the flank 10a, It is considered that the ridge a is left on the flank 10a, and the ridge a determines the flank wear width (V B ), that is, the wear resistance. In the figure, 10b indicates a rake face. And
When the CBN grains 11 come off, the portion of the bonding phase 12 of the cutting edge portion having the function of supporting the CBN grains 11 in contact with the work material 13 recedes due to abrasion, and external force (cutting force, thermal stress, etc.) When the force for supporting the CBN grains 11 is exceeded, CB
It is considered that the CBN grains fall off from the cutting edge portion 10 due to the separation of the N grain 11 and the binder phase 12 at the grain boundary or the breakage of the binder phase 12. Further, from the above, it is considered that in the CBN sintering tool, the CBN grains have a function as a cutting edge and the binder phase has a function as a carrier for the cutting edge.
【００１０】このような見地から、本発明による工具用
焼結材料でＣＢＮ焼結工具を作製した場合のＣＢＮ粒と
結合相との機能を考えてみる。まず、切刃としてのＣＢ
Ｎ粒は、ダイヤモンドに次ぐ硬さを有し、且つダイヤモ
ンドの欠点とされる鉄族金属との反応性も低いので、高
い耐摩耗性を有することが期待でき、切刃として要求さ
れる機能を充分に満たしていると考えられる。From this point of view, let us consider the functions of the CBN grains and the binder phase when a CBN sintered tool is produced from the sintered material for a tool according to the present invention. First, CB as a cutting edge
Since N grains have hardness second only to diamond and have low reactivity with iron group metals, which are the drawbacks of diamond, they can be expected to have high wear resistance and have the functions required for a cutting edge. It is considered to be fully satisfied.
【００１１】一方、結合相は、上述した摩耗機構から考
えると、次の４つの特性を有する必要があると考えられ
る。すなわち、結合相の耐摩耗性を高くして摩耗による
刃先の結合相の後退速度を低く抑えるために、 切削時切刃温度における硬度が高いこと、 切削時切刃温度における被削材（鋼，鉄族金属な
ど）との反応性が低いこと、 が要求される。また、ＣＢＮ粒と結合相との粒界での剥
離による脱落が起こりにくくするために、 ＣＢＮ粒との間で相互に拡散，反応し、強固に接着
すること、さらに、結合相が焼結体として健全であるた
めに、 焼結性が良好で（低い焼結温度で緻密化する）、強
度、靱性が高いこと、が要求される。On the other hand, considering the above-mentioned wear mechanism, it is considered that the binder phase needs to have the following four characteristics. That is, in order to increase the wear resistance of the binder phase and suppress the receding speed of the binder phase of the cutting edge due to wear to be low, the hardness at the cutting edge temperature during cutting is high, and the work material (steel, Low reactivity with iron group metals) is required. Further, in order to prevent the CBN grains and the binder phase from coming off due to delamination at the grain boundary, the CBN grains diffuse and react with each other to firmly adhere to each other, and further, the binder phase is a sintered body. Therefore, it is required that the sinterability be good (becomes densified at a low sintering temperature), and that the strength and toughness be high.
【００１２】したがって、このような各特性について本
発明に係る結合相を考察してみる。図１はＣＢＮ焼結工
具の各種結合相の硬度を示すものであるが、一般に周期
率表第４ａ，５ａ，６ａ族遷移金属の炭化物、硼化物、
窒化物の硬度が高い。本発明に用いる窒化チタン（以
下、ＴｉＮと表記する）はこれらに含まれて硬度が高
く、また、酸化アルミニウム（以下、アルミナ又はＡl2
Ｏ3 と表記する）は、切削時刃先温度における硬度が高
い値を示しているので、本発明における結合相は上述し
たの特性は満足すると考えられる。Therefore, let us consider the binder phase according to the present invention with respect to each of these characteristics. FIG. 1 shows the hardness of various binder phases of a CBN sintered tool. Generally, the periodic table 4a, 5a, 6a group transition metal carbides, borides,
High hardness of nitride. Titanium nitride (hereinafter referred to as TiN) used in the present invention is contained in these and has high hardness, and aluminum oxide (hereinafter referred to as alumina or Al 2
(Denoted as O 3 ) has a high hardness at the cutting edge temperature during cutting, and therefore the binder phase in the present invention is considered to satisfy the above-mentioned characteristics.
【００１３】図２は、各種結合相の切削時刃先温度にお
ける鋼に対する生成自由エネルギ（ΔＧT °）を示す。
かかる生成自由エネルギを、鋼等との反応性の指標とす
ると、周期率表第４ａ，５ａ，６ａ族遷移金属の炭化
物、窒化物、すなわち本発明に用いるＴｉＮ、窒化アル
ミニウム（以下、ＡｌＮと表記する）並びに本発明に用
いるアルミナ、酸化ジルコニウム（以下、ＺｒＯ2 又は
ジルコニアと表記する）などの酸化物は反応性が低いも
のと推測され、本発明に用いる結合相は上述したの特
性を満足すると考えられる。FIG. 2 shows the free energy of formation (ΔG T °) for steel at the cutting edge temperature during cutting of various binder phases.
When such free energy of formation is used as an index of reactivity with steel or the like, carbides and nitrides of transition metals of Groups 4a, 5a and 6a of the periodic table, that is, TiN and aluminum nitride used in the present invention (hereinafter referred to as AlN) It is assumed that the oxides such as alumina and zirconium oxide (hereinafter, referred to as ZrO 2 or zirconia) used in the present invention have low reactivity, and that the binder phase used in the present invention satisfies the above-mentioned characteristics. Conceivable.
【００１４】また、結合相とＣＢＮ粒との反応性を、指
標として同様に生成自由エネルギを用いて評価した場
合、焼結温度（１４００〜１８００℃）で反応する可能
性があるのは、周期率表第４ａ，５ａ，６ａ族遷移金属
の炭化物、硼化物、窒化物の中でも、ＴｉＮ、ＡｌＮ、
窒化ニオブ（以下、ＮｂＮと表記する）の他、数種に限
られる。したがって、本発明は結合相の主成分としてＴ
ｉＮ副成分の一成分としてＡｌＮを含むので、上述した
の特性も有すると考えられる。When the reactivity between the binder phase and the CBN grains is similarly evaluated using the free energy of formation as an index, it is possible that the reaction occurs at the sintering temperature (1400 to 1800 ° C.) Among the carbides, borides, and nitrides of transition metals of the 4a, 5a, and 6a groups of the index table, TiN, AlN,
In addition to niobium nitride (hereinafter referred to as NbN), it is limited to several kinds. Therefore, the present invention uses T
Since AlN is contained as one component of the iN subcomponent, it is considered that the above-mentioned characteristics are also possessed.
【００１５】次に、焼結体の健全性に関する上述した
の特性を調べるため、ＴｉＮのみを結合相とするＣＢＮ
焼結工具を製作して切削試験を行った。製作したＣＢＮ
焼結工具は、粒径１〜３μｍのＣＢＮ粒５０体積％と、
粒径0.５〜２μｍのＴｉＮ粉末５０体積％とをボールミ
ルで混合し、後述する従来公知の超高圧発生装置を用い
て圧力５０キロバール（以下、Ｋｂと表記する）、焼結
温度１４００〜１７５０℃、焼結時間0.５〜３０分の条
件で超高圧焼結し、これを工具形状に刃付したものであ
る。これを切削試験〔被削材ＳＵＪ２（硬度ＨRC６２以
上）、切削速度１００ｍ／min 、送り0.１min ／rev 、
切込み0.１mm〕に供したところ、焼結温度、焼結時間等
の条件によらず、従来のＣＢＮ焼結工具の耐摩耗性、耐
欠損性には及ばなかった。また、かかるＣＢＮ焼結工具
の破断面を顕微鏡観察したところ、ＴｉＮ粒界で破断し
ていることが観察された。Next, in order to investigate the above-mentioned characteristics concerning the soundness of the sintered body, CBN containing only TiN as a binder phase.
A sintering tool was manufactured and a cutting test was performed. CBN made
The sintering tool comprises 50% by volume of CBN particles having a particle size of 1 to 3 μm,
50% by volume of TiN powder having a particle size of 0.5 to 2 μm was mixed in a ball mill, and a pressure of 50 kbar (hereinafter, referred to as Kb) was used and a sintering temperature of 1400 to 1750 using a conventionally known ultrahigh pressure generator described later. Ultra high pressure sintering was carried out under the conditions of ℃ and sintering time of 0.5 to 30 minutes, and this was bladed into a tool shape. This is subjected to a cutting test [workpiece SUJ2 (hardness H RC 62 or more), cutting speed 100 m / min, feed 0.1 min / rev,
When subjected to a cutting depth of 0.1 mm], it did not reach the wear resistance and fracture resistance of the conventional CBN sintering tool regardless of the conditions such as sintering temperature and sintering time. Further, when the fracture surface of the CBN sintered tool was observed under a microscope, it was observed that the fracture occurred at the TiN grain boundary.
【００１６】本発明では焼結性が高く、且つ上述した特
性，も合せ持つアルミナをＴｉＮに添加し、さらに
，の特性を持ち、焼結時に高い活性を有するＡｌＮ
を添加することにより、健全性の高い焼結体を得てい
る。また、アルミナに微量のジルコニアを添加すること
により、焼結性を向上させ、さらに炭化硅素の針状結晶
（以下、ＳｉＣ針状結晶と表記する）を添加することに
より靱性を向上させている。In the present invention, AlN having a high sinterability and having the above-mentioned characteristics, added to TiN, has the following characteristics and has a high activity during sintering.
Is added to obtain a sintered body with high soundness. Further, by adding a small amount of zirconia to alumina, the sinterability is improved, and further, toughness is improved by adding a needle crystal of silicon carbide (hereinafter referred to as a SiC needle crystal).
【００１７】さらに、結合相成分であるＴｉＮはＣＢＮ
と直接には反応しにくいが、本発明の被膜を施すことに
より、ＣＢＮ粒のＴｉＮ被膜と結合相成分であるＴｉＮ
の焼結が容易に行なえるため、大巾に焼結性が向上し、
の特性が満足されている。Further, TiN which is a binder phase component is CBN.
It is difficult to react directly with, but by applying the coating of the present invention, the TiN coating of CBN grains and TiN which is a binder phase component.
Can be easily sintered, greatly improving the sinterability,
The characteristics of are satisfied.
【００１８】図３に本発明の工具用焼結材料の組織を模
式的に示し、図中１はＣＢＮ粉粒、２はＴｉＮ被膜、３
は結合相を示す。FIG. 3 schematically shows the structure of the sintered material for a tool of the present invention, in which 1 is CBN powder, 2 is TiN coating, and 3 is.
Indicates a bonded phase.
【００１９】ＣＢＮは工具用焼結材料としての主体をな
すものであり、これが４０体積％未満ではＣＢＮ自体の
硬度を反映させることが困難となり、充分な耐摩耗性を
得られない。逆に、このＣＢＮが９０体積％を越える
と、焼結時にその一部が六方晶に相転位を起こして焼結
性が悪化するため、靱性の低下により微小なチッピング
や欠損が発生する。CBN is mainly used as a sintered material for tools, and if it is less than 40% by volume, it becomes difficult to reflect the hardness of CBN itself, and sufficient wear resistance cannot be obtained. On the contrary, if the CBN content exceeds 90% by volume, a part of the CBN undergoes a phase transition in the hexagonal crystal during the sintering to deteriorate the sinterability, so that minute chipping or chipping occurs due to the decrease in toughness.
【００２０】一方、結合相の主成分となるＴｉＮは、高
融点、高硬度で、鋼との反応性が低いという特性を有
し、且つ硬度については通常の焼入鋼の精密切削条件で
の刃先温度において最も高い値を示す材料の１つであ
る。また、ＴｉＮは１０００℃付近から急激な硬度低下
を示して焼結温度（１４００℃）以上の高温域では軟質
化して流動し易い状態になるものと考えられる。したが
って、焼結時にはＣＢＮ粒間へＴｉＮの流動が可能にな
り、焼結体の緻密化に効果的であることが推測できる。
さらに、ＴｉＮはＣＢＮ粒にＴｉＮが被膜として施され
ているので良好な焼結性が期待でき結合相とＣＢＮ粒と
が強固に接着し、健全性が高く特性の良好な焼結体が得
られる。On the other hand, TiN, which is the main component of the binder phase, has the characteristics of high melting point, high hardness, and low reactivity with steel, and the hardness is in the precision cutting conditions of ordinary hardened steel. It is one of the materials that shows the highest value at the cutting edge temperature. Further, it is considered that TiN shows a rapid decrease in hardness from around 1000 ° C., and is softened in a high temperature region above the sintering temperature (1400 ° C.) to easily flow. Therefore, it can be inferred that TiN can flow between CBN grains during sintering, which is effective for densifying the sintered body.
Further, since TiN is formed by coating TiN on CBN particles, good sinterability can be expected, and the binder phase and CBN particles are firmly bonded to each other, and a sintered body having high soundness and good characteristics can be obtained. ..
【００２１】また、結合相の副成分であるアルミナは、
高融点、高硬度で、鋼との反応性が低い特性を有し、上
述した通り結合相の材料成分としてＴｉＮと並ぶ優れた
特性を有するが、ＣＢＮ粒との反応性が期待できない。
したがって、アルミナは結合相の主成分として使用する
場合にはＣＢＮ粒との反応性を改善するために金属成分
等の添加が必要となるが、本発明では、焼結時に高い活
性を有するＡｌＮを添加することにより、焼結性を大幅
に改善している。これによりＣＢＮ焼結材料としての健
全性が向上し、工具材料として耐摩耗性、耐欠損性の高
い材料が提供できる。本発明においてアルミナとＡｌＮ
は、ＣＢＮ粒とＴｉＮ粒とからなるＣＢＮ焼結材料の主
構成要素の隙間を満たすように添加、焼結されるもので
あり、ＴｉＮ粒とＴｉＮ粒との粒間では両者を接着する
役割を果たす。Alumina, which is a subcomponent of the binder phase, is
It has high melting point, high hardness, low reactivity with steel, and excellent properties along with TiN as a material component of the binder phase as described above, but reactivity with CBN grains cannot be expected.
Therefore, when alumina is used as the main component of the binder phase, it is necessary to add a metal component or the like in order to improve the reactivity with the CBN grains, but in the present invention, AlN having high activity during sintering is used. By adding it, the sinterability is greatly improved. Thereby, the soundness as a CBN sintered material is improved, and a material having high wear resistance and chipping resistance can be provided as a tool material. In the present invention, alumina and AlN
Is added and sintered so as to fill the gap between the main constituent elements of the CBN sintered material composed of CBN grains and TiN grains, and has a role of adhering the TiN grains and the TiN grains to each other. Fulfill
【００２２】また、アルミナのこのような役割から考え
て、アルミナ自体の焼結性についても良好であることが
不可欠であり、さらに靱性の向上が必要であるが、本発
明ではアルミナにジルコニア及び炭化硅素の針状結晶を
添加した組成を結合相の副成分とすることにより、その
焼結性及び靱性の向上を図っている。Considering the role of alumina, it is essential that the alumina itself has good sinterability, and further improvement of toughness is required. In the present invention, however, zirconia and carbonized alumina are used. By using a composition containing silicon needle crystals as an auxiliary component of the binder phase, the sinterability and toughness of the binder phase are improved.
【００２３】ここで副成分の組成について説明する。こ
れまでの説明に記したように、ＣＢＮ焼結材料の結合相
はそれ自体も耐摩耗性の高い工具であることが必要であ
る。したがって組成を任意に選べるのではなく、その組
成成分が重要となってくる。そこで組成成分を変えた結
合相のみの工具材料を試作し、切削試験で耐摩耗性を評
価した。条件は切削速度１７０ｍ／分，送り２０μｍ／
主軸回転，切り込み２０μｍ，被削材ＳＵＪ２（硬さＨ
RC６２）で行った。Here, the composition of the subcomponents will be described. As described in the above description, the binder phase of the CBN sintered material itself needs to be a tool having high wear resistance. Therefore, it is not possible to arbitrarily select the composition, but the composition component becomes important. Therefore, a tool material with only the binder phase with different composition components was prototyped, and wear resistance was evaluated by a cutting test. Conditions are cutting speed 170m / min, feed 20μm /
Spindle rotation, notch 20 μm, work material SUJ2 (hardness H
I went to RC 62).
【００２４】まず成分をアルミナと窒化アルミニウムに
限定して組成成分を調べたところ、アルミナの体積％に
対する窒化アルミニウムの体積％が１／３以下ではアル
ミナのもろさが現われ逃げ面摩耗幅が７０μｍ以上とな
り、また、同様に４／５以上では窒化アルミニウムの硬
度の低くさが現われ、逃げ面摩耗幅が７０μｍ以上とな
ることがわかった。この検討から副成分のアルミナと窒
化アルミニウムは３：１〜５：４（体積％比）の範囲で
混合する必要があることがわかった。First, when the compositional components were investigated by limiting the components to alumina and aluminum nitride, when the volume% of aluminum nitride with respect to the volume% of alumina was 1/3 or less, the brittleness of alumina appeared and the flank wear width became 70 μm or more. Also, similarly, it was found that when the hardness was 4/5 or more, the hardness of aluminum nitride was low, and the flank wear width was 70 μm or more. From this study, it was found that alumina and aluminum nitride, which are subcomponents, need to be mixed in the range of 3: 1 to 5: 4 (volume% ratio).
【００２５】次に、上記適正な範囲に混合された２成分
系に対するＳｉＣ針状結晶の添加量についても、同様な
実験から５体積％未満ではその添加の効果が現れず、１
５体積％以上では焼結性が低下してかえって靱性の低下
を招くことが認められた。Next, regarding the amount of addition of SiC needle crystals to the two-component system mixed in the above-mentioned appropriate range, from the same experiment, if the addition amount is less than 5% by volume, the effect of addition does not appear.
It was confirmed that if the content is 5% by volume or more, the sinterability is lowered and the toughness is rather lowered.
【００２６】さらに、上記２成分にＳｉＣ針状結晶を添
加した３成分系へのジルコニアの添加量を変化させその
影響を見た。試験の結果を図４に示すが、ジルコニアを
１体積％未満添加した場合にはその添加の効果が表われ
ず、一方、５体積％を越えて添加した場合には焼結性が
相対的に不良で、耐摩耗性が低下することが認められ
た。なお、ここでの耐摩耗性の評価は、前出と同じ条件
で行った。Further, the effect was examined by changing the amount of zirconia added to the three-component system in which SiC needle crystals were added to the above two components. The results of the test are shown in FIG. 4. When zirconia is added in an amount of less than 1% by volume, the effect of the addition does not appear, while when added in an amount of more than 5% by volume, the sinterability is relatively high. It was found that the abrasion resistance was low due to the poor quality. The evaluation of wear resistance here was carried out under the same conditions as described above.
【００２７】次に、ＣＢＮ粒及び、結合相の主成分、副
成分の組成（配合比率）について説明する。ＣＢＮ粒と
結合相の主成分とを混合した際に生じる隙間に、副成分
（アルミナ５０〜６５体積％とジルコニア１〜５体積％
と、ＡｌＮ２０〜４０体積％，ＳｉＣ針状結晶５〜１５
体積％の混合粉末）が充填され、且つその副成分が焼結
後にＣＢＮ粒及び結合相の主成分の隙間を充たすと共
に、副成分の焼結体が焼結体中で網目状の連結した構造
となるためには、副成分は理論的に１５体積％以上の添
加が必要であると考えられる。Next, the composition (blending ratio) of the CBN grains and the main and subcomponents of the binder phase will be described. Secondary components (alumina 50 to 65% by volume and zirconia 1 to 5% by volume) are present in the gaps generated when the CBN particles and the main component of the binder phase are mixed.
And AlN 20 to 40% by volume, SiC needle crystals 5 to 15
(Volume% mixed powder), the secondary component fills the gaps between the CBN grains and the main component of the binder phase after sintering, and the sintered compact of the secondary component is connected in a mesh in the sintered body. Therefore, it is considered that it is theoretically necessary to add the auxiliary component in an amount of 15% by volume or more.
【００２８】また、ＣＢＮ粒と結合相主成分との配合比
率について考えると、上述したようにＣＢＮ粒の最小含
有量は４０体積％が望ましく、結合相の副成分が最小量
（１５体積％）のときに主成分の比率が最大となる。し
たがって、結合相主成分の配合比率の最大は４５体積％
となる。一方、副成分と同様に結合相の主成分自体が網
目状の連結した構造とするためには、主成分も１５体積
％以上添加する必要がある。Considering the mixing ratio of the CBN grains and the main component of the binder phase, as described above, the minimum content of the CBN grains is preferably 40% by volume, and the subcomponent of the binder phase is the minimum amount (15% by volume). When, the ratio of the main components becomes maximum. Therefore, the maximum proportion of the binder phase main component is 45% by volume.
Becomes On the other hand, it is necessary to add not less than 15% by volume of the main component in order to make the main component of the binder phase itself have a network-like structure like the sub-component.
【００２９】さらに、結合相において副成分の添加量が
主成分の添加量を越えると、本来の耐摩耗性が損われる
ため、副成分の最大比率は３５体積％となる。Further, when the amount of the subcomponent added in the binder phase exceeds the amount of the main component added, the original wear resistance is impaired, so that the maximum proportion of the subcomponent becomes 35% by volume.
【００３０】以上説明した本発明の工具用焼結材料は、
従来から公知の超高圧焼結装置を使用して製造できる。
すなわち、まず、ＣＢＮ粉粒と結合相の主成分、副成分
とを所定の混合比率でボールミル等で混合して均一な混
合粉末とする。次いで、圧粉成形プレス等で混合粉末を
圧粉成形し、これをジルコニウムなどの高融点金属製の
容器内に充填する。その後、例えばニューセラミックス
（１９８８）、Vol.１，No.6，Ｐ４３に記載の超高圧焼
結技術により、温度を１４００〜１８００℃、圧力を４
０〜６０Ｋｂとし、この圧力、温度で、0.５〜３０分間
保持した後、冷却して圧力を除き、焼結体を製造する。The sintered material for tools of the present invention described above is
It can be manufactured using a conventionally known ultra-high pressure sintering apparatus.
That is, first, the CBN powder particles and the main component and subcomponents of the binder phase are mixed in a predetermined mixing ratio by a ball mill or the like to obtain a uniform mixed powder. Next, the mixed powder is compacted by a compacting press or the like, and this is filled in a container made of a high melting point metal such as zirconium. After that, for example, by the ultrahigh pressure sintering technique described in New Ceramics (1988), Vol. 1, No. 6, P43, the temperature is 1400 to 1800 ° C and the pressure is 4
The pressure is set to 0 to 60 Kb, and the pressure and temperature are maintained for 0.5 to 30 minutes, followed by cooling to remove the pressure to produce a sintered body.
【００３１】[0031]
【実施例】以下、本発明を実施例に基づいて説明する。EXAMPLES The present invention will be described below based on examples.
【００３２】（実施例１）無触媒法で合成された１から
３マイクロメートル（以下、μｍと表記する）の範囲の
粒径のＣＢＮにＣＶＤ法でＴｉＮの被膜を施した。処理
は原料ガスとしてＴｉＣl4，Ｎ2 ，ＣＨ4 を用い、圧力
６００torrで、温度９１０℃，２時間で行った。膜の厚
みは、板状の単結晶ＣＢＮへの成膜速度から0.１〜0.５
μｍと考えられる。(Example 1) A TiN coating film was applied to a CBN having a particle diameter in the range of 1 to 3 micrometers (hereinafter referred to as μm) synthesized by a non-catalytic method by a CVD method. The treatment was carried out at a pressure of 600 torr and a temperature of 910 ° C. for 2 hours using TiCl 4 , N 2 and CH 4 as raw material gases. The thickness of the film is 0.1 to 0.5 depending on the film formation rate on the plate-shaped single crystal CBN.
It is considered to be μm.
【００３３】次に被膜を施したＣＢＮ粒と結合相成分を
混合した。結合相成分は平均粒径が0.５〜1.５μｍのＴ
ｉＮと、平均粒径が0.３μｍのアルミナとジルコニアと
ＡｌＮ、及びＳｉＣ針状結晶との混合粉末（５７：３：
３０：１０体積比）とからなり且つこれらの体積比を４
５：３０：２５（＝ＣＢＮ：ＴｉＮ：Ａl2Ｏ3 ／ＺｒＯ
2 ，ＡｌＮ、及びＳｉＣ針状結晶）に調整した混合物
を、炭化タングステン（以下、ＷＣと表記する）基超硬
合金で内張りした小形の遊星運動型ミル内に装入し、更
にこれらの混合を促進する目的でこれら粉粒の総体積の
３５％に相当する量のメチルアルコールをミル内に加
え、蓋をしてこれを３時間混練した。そして、不活性ガ
ス雰囲気にてミルの蓋を取り、ミルを１２０℃に加熱し
てメチルアルコールを蒸発させ、混練された原料粉体の
乾燥を行った。一方、塩化ナトリウム（以下、これをＮ
ａＣｌと表記する）の粉粒を内径８ミリメートル、長さ
１０ミリメートルの円筒状に加圧成形してなるＮａＣｌ
製の容器本体に、同様にして作成したＮａＣｌ製の下蓋
を一体的に取付け、これらの内面に厚さ２０μｍのジル
コニウム箔を張り付け、更にこの中に直径7.８ミリメー
トル、厚さ２ミリメートルのＷＣ基超硬合金製の円板を
載置したものを用意しておく。Next, the coated CBN grains and the binder phase component were mixed. The binder phase component is T having an average particle size of 0.5 to 1.5 μm.
A mixed powder of iN, alumina having an average particle size of 0.3 μm, zirconia, AlN, and SiC needle crystals (57: 3:
30:10 volume ratio) and these volume ratios are 4
5:30:25 (= CBN: TiN: Al 2 O 3 / ZrO
2 , AlN, and SiC needle crystals) are charged into a small planetary motion mill lined with tungsten carbide (hereinafter referred to as WC) -based cemented carbide, and the mixture is further mixed. For the purpose of accelerating, an amount of methyl alcohol corresponding to 35% of the total volume of these powder particles was added to the inside of the mill, covered with a lid, and kneaded for 3 hours. Then, the lid of the mill was removed in an inert gas atmosphere, the mill was heated to 120 ° C. to evaporate methyl alcohol, and the kneaded raw material powder was dried. On the other hand, sodium chloride (hereinafter referred to as N
NaCl, which is formed by press-molding powder particles of (aCl) into a cylindrical shape having an inner diameter of 8 mm and a length of 10 mm.
A lower lid made of NaCl made in the same manner is integrally attached to a container body made of the same, and a zirconium foil having a thickness of 20 μm is attached to the inner surface thereof, and further, a 7.8 mm diameter and 2 mm thick Prepare a disc on which a WC-based cemented carbide disc is placed.
【００３４】そして、乾燥終了後の前記原料粉体をあら
かじめ粉末成形プレス等で６mmの厚みに圧粉成形し、こ
れを不活性ガス雰囲気にてこの容器本体内の前記円板上
に装入する。そして、更にこの上に前述したのと同一な
ＷＣ基超硬合金製の円板を載置し、又この上に厚さ２０
μｍのジルコニウム箔を重ねたのち、前述と同様にして
作成したＮａＣｌ製の上蓋を容器本体に嵌め込み、これ
ら容器本体と下蓋と上蓋とからなる容器内に原料粉末を
密封する。Then, the raw material powder after completion of the drying is preliminarily compacted to a thickness of 6 mm by a powder compacting press or the like, and the compact is compacted in an inert gas atmosphere onto the disc in the container body. .. Then, the same WC-based cemented carbide disc as described above is placed on top of this, and a thickness of 20
After stacking zirconium foils having a thickness of μm, an NaCl upper lid prepared in the same manner as described above is fitted into the container body, and the raw material powder is sealed in the container including the container body, the lower lid and the upper lid.
【００３５】次に、超高圧発生装置に上述した容器を取
付け、５０Ｋｂの圧力と１６５０℃の温度とを３０分間
保持し、原料粉末を焼結させて両端にＷＣ基超硬合金が
結合した円柱状の工具用焼結材料を得た。そして、この
工具用焼結材料を前記円板が結合した状態のまま切り出
してバイト用の切刃を仕上げ、これを予め用意しておい
た四角形のＷＣ基超硬合金製チップに銀ろうを介して固
定し、すくい角０度、逃げ角５度、ノーズ曲率半径が１
ミリメートルの切削工具を作成した。Next, the container described above was attached to the ultra-high pressure generator, the pressure of 50 Kb and the temperature of 1650 ° C. were maintained for 30 minutes, the raw material powder was sintered, and a circle in which WC-based cemented carbide was bonded to both ends. A columnar sintered material for tools was obtained. Then, the sintered material for a tool is cut out in a state where the discs are bonded to finish a cutting edge for a bite, and this is prepared in advance with a rectangular WC-based cemented carbide tip through silver brazing. Fixed, rake angle 0 degrees, clearance angle 5 degrees, nose radius of curvature 1
Created a millimeter cutting tool.
【００３６】この切削工具を用い、ロックウエル硬さが
６２の丸棒状をなす高炭素軸受鋼（ＳＵＪ２）に対して
切削速度が毎分１７０メートル、切込み量が２０μｍ、
バイトの送り速度が主軸一回転当り２０μｍとなるよう
にして１００メートルの長さに相当する距離だけ旋削し
た後、切刃の逃げ面の摩耗幅及びこの切刃を構成するＣ
ＢＮ焼結材料のビッカース硬さを、前記原料粉末を構成
する各粉粒の比率を変えて測定した。なお、この旋削加
工中には切削油を噴霧供給した。Using this cutting tool, a high carbon bearing steel (SUJ2) having a Rockwell hardness of 62 and having a round bar shape has a cutting speed of 170 meters per minute and a cutting depth of 20 μm.
After turning by a distance corresponding to a length of 100 meters so that the feed rate of the cutting tool is 20 μm per rotation of the main spindle, the wear width of the flank of the cutting edge and the C constituting this cutting edge
The Vickers hardness of the BN sintered material was measured by changing the ratio of each powder grain constituting the raw material powder. Note that cutting oil was spray-supplied during the turning process.
【００３７】これらの測定結果を表１に示すが、ちなみ
に窒化チタンに金属成分を添加した組成を結合相として
使用した市販のＣＢＮ焼結工具のビッカース硬さは２５
００、切刃の逃げ面の摩耗幅は４５μｍであった。また
ＴｉＮ被膜を施こさない、従来の焼結工具材料の特性を
比較のために示した。The results of these measurements are shown in Table 1. By the way, the Vickers hardness of a commercially available CBN sintering tool using a composition obtained by adding a metal component to titanium nitride as a binder phase is 25.
00, the wear width of the flank of the cutting edge was 45 μm. In addition, the characteristics of the conventional sintered tool material without the TiN coating are shown for comparison.
【００３８】[0038]
【表１】 [Table 1]
【００３９】表１に示す結果から明らかなように、ＣＢ
ＮにＴｉＮ被膜を施した場合には焼結性が向上するため
か逃げ面摩耗幅が小さくなり、耐摩耗性が向上している
ことが確認できた。As is clear from the results shown in Table 1, CB
It can be confirmed that when the TiN coating is applied to N, the flank wear width is reduced probably because the sinterability is improved, and the wear resistance is improved.
【００４０】（実施例２）実施例１と同様な方法で粒径
１〜３μｍのＣＢＮにＣＶＤ法で炭化チタン（後ＴｉＣ
と表記）の被膜を施こした。処理は原料ガスとしてＴｉ
Ｃｌ4 ，ＣＯ2 ，ＣＨ4 を用い、圧力６００torrで、温
度１０２５℃，２時間で行った。これを実施例１と同一
成分の結合相成分と混ぜ、超高圧焼結法で工具用焼結材
料とした。焼結条件は圧力５５Ｋｂ，温度１７５０℃と
した。これを刃付して工具として用い、高炭素軸受鋼
（ＳＵＪ２，ロックウエル硬さ６２）を被削材として切
削試験に供したところ、ほぼ実施例１と同じ結果が得ら
れた。これは結合相の主成分であるＴｉＮとコーティン
グ被膜として施したＴｉＣがともにＴｉの化合物であ
り、複合化合物であるＴｉＣＮを生成して結合したた
め、ＣＢＮと結合相の粒界が強化されたためと考えられ
る。Example 2 In the same manner as in Example 1, CBN having a particle size of 1 to 3 μm was formed by titanium carbide (post-TiC) by CVD.
(Notation) was applied. Ti is used as a raw material gas
Cl 4 , CO 2 and CH 4 were used, the pressure was 600 torr, and the temperature was 1025 ° C. for 2 hours. This was mixed with a binder phase component having the same components as in Example 1 to obtain a sintered material for a tool by an ultra high pressure sintering method. The sintering conditions were a pressure of 55 Kb and a temperature of 1750 ° C. When this was attached to a blade and used as a tool and a high carbon bearing steel (SUJ2, Rockwell hardness 62) was subjected to a cutting test as a work material, almost the same results as in Example 1 were obtained. This is probably because TiN, which is the main component of the binder phase, and TiC applied as a coating film are both Ti compounds, and TiCN, which is a composite compound, was formed and bonded, so that the grain boundary between CBN and the binder phase was strengthened. Be done.
【００４１】（実施例３）実施例１と同様な方法で粒径
４〜８μｍのダイヤモンドにＣＶＤ法でＴｉＮの被膜を
施した。ＣＶＤ処理条件は実施例１と同一で行った。さ
らに実施例１と同じ結合相成分で超高圧焼結後切削工具
となし、切削試験を実施した。被削材は鋳鉄製丸棒（直
径６０mm）で、切削速度毎分２００ｍ，切込み0.１mm，
送り0.１mm／主軸一回転で評価した。この結果、市販さ
れている金属系の結合相を持つダイヤモンド焼結工具に
比べ、同一切削距離を切削した後の被削材の面粗さが３
０％向上（従来面粗さ3.２μｍであるのに対し、面粗さ
2.２μｍ）した。(Example 3) In the same manner as in Example 1, diamond having a grain size of 4 to 8 µm was coated with a TiN film by the CVD method. The CVD processing conditions were the same as in Example 1. Further, a cutting test was conducted using the same binder phase component as in Example 1 after the ultrahigh pressure sintering to obtain a cutting tool. The work material is a cast iron round bar (diameter 60 mm), cutting speed 200 m / min, depth of cut 0.1 mm,
The feed was evaluated at 0.1 mm / spindle one revolution. As a result, the surface roughness of the work material after cutting at the same cutting distance is 3 compared with the commercially available diamond sintered tools having a metallic binder phase.
0% improvement (compared to conventional surface roughness of 3.2 μm, surface roughness
2.2 μm).
【００４２】[0042]
【発明の効果】本発明の工具用焼結材料は、ＣＢＮ粉粒
などの硬質粉粒表面に例えばＣＶＤ法で、結合相の主成
分と同一のＴｉＮ等の被膜を施こしているので、ＣＢＮ
粉粒と結合相との密着性が向上した。この結果焼結性が
向上し、より高い耐摩耗性を示した。またＣＢＮ粉粒な
どの硬質粉粒の被膜施工は、硬質粉粒表面の清浄度を高
めることに寄与していることが考えられ、この点からも
焼結性の改善が期待される。In the sintered material for a tool of the present invention, the surface of hard powder particles such as CBN powder particles is coated with the same coating film of TiN as the main component of the binder phase by, for example, the CVD method.
The adhesion between the powder particles and the binder phase was improved. As a result, sinterability was improved and higher wear resistance was exhibited. Further, it is considered that the coating of hard powder particles such as CBN powder particles contributes to enhancing the cleanliness of the surface of the hard powder particles, and from this point also improvement of sinterability is expected.
【図１】ＣＢＮ焼結工具の結合相材料の硬度を示す説明
図である。FIG. 1 is an explanatory diagram showing hardness of a binder phase material of a CBN sintering tool.
【図２】ＣＢＮ焼結工具の結合相材料の被削材との反応
性を示す説明図である。FIG. 2 is an explanatory diagram showing the reactivity of a binder phase material of a CBN sintering tool with a work material.
【図３】本発明の工具用焼結材料の組成の模式図であ
る。FIG. 3 is a schematic diagram of the composition of the sintered material for a tool of the present invention.
【図４】アルミナへジルコニアを添加した場合の実験結
果を示す説明図である。FIG. 4 is an explanatory view showing an experimental result when zirconia is added to alumina.
【図５】ＣＢＮ焼結工具の摩耗を説明する模式図及びそ
のＡ部拡大図である。5A and 5B are a schematic diagram illustrating wear of a CBN sintering tool and an enlarged view of an A portion thereof.
１ ＣＢＮ粉粒 ２ ＴｉＮ被膜 ３ 結合相 １０ 工具刃先部 １０ａ 逃げ面 １０ｂ すくい面 １１ ＣＢＮ粒 １２ 結合相 １３ 被削材 DESCRIPTION OF SYMBOLS 1 CBN powder particles 2 TiN coating 3 Binder phase 10 Tool edge part 10a Flank surface 10b Rake surface 11 CBN particles 12 Binder phase 13 Work material
───────────────────────────────────────────────────── フロントページの続き (72)発明者 角田 英雄 長崎県長崎市飽の浦町１番１号 三菱重工 業株式会社長崎研究所内 (72)発明者 山田 福司 東京都千代田区丸の内二丁目５番１号 三 菱重工業株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Hideo Kakuda 1-1 Hideoura-cho, Nagasaki-shi, Nagasaki Nagasaki Research Laboratories, Mitsubishi Heavy Industries, Ltd. (72) Fukushi Yamada 2-5-1 Marunouchi, Chiyoda-ku, Tokyo Sanryo Heavy Industries Co., Ltd.
Claims (2)
質粉粒と、金属元素の窒化物、硼化物、炭化物、及びこ
れらの複化物から選ばれた結合相とからなる工具用焼結
材料において、上記硬質粉粒に結合相成分と同一、ある
いは各結合相成分の金属元素の他の化合物の被膜を施し
たことを特徴とする工具用焼結材料。1. A sintered material for tools comprising hard powder particles such as cubic boron nitride and diamond, and a binder phase selected from nitrides of metal elements, borides, carbides, and complex compounds thereof. A sintered material for a tool, characterized in that the hard powder particles are coated with the same compound as the binder phase component or with another compound of a metal element of each binder phase component.
と、結合相の主成分となる窒化チタン１５〜４５体積％
と、結合相の副成分となる酸化アルミニウム、酸化ジル
コニウム、窒化アルミニウム及び炭化硅素の針状結晶の
混合粉粒１５〜３５体積％とからなる組成を有し、且つ
上記結合相の副成分の組成が酸化アルミニウム５０〜６
５体積％、酸化ジルコニウム１〜５体積％，窒化アルミ
ニウム２０〜４０体積％及び炭化硅素の針状結晶５〜１
５体積％の比率となる工具用焼結材料であって、立方晶
窒化硼素の粉粒に結合相成分と同一、あるいは各結合相
成分の金属元素の他の化合物の被膜を施したことを特徴
とする工具用焼結材料。2. Cubic boron nitride powder particles 40 to 70% by volume
And 15 to 45% by volume of titanium nitride, which is the main component of the binder phase
And 15 to 35% by volume of mixed powder particles of acicular crystals of aluminum oxide, zirconium oxide, aluminum nitride, and silicon carbide, which are subcomponents of the binder phase, and the composition of the subcomponent of the binder phase. Is aluminum oxide 50-6
5% by volume, zirconium oxide 1-5% by volume, aluminum nitride 20-40% by volume, and silicon carbide needle crystals 5-1
A sintered material for tools with a ratio of 5% by volume, characterized in that powders of cubic boron nitride are coated with the same compound as the binder phase component or another compound of the metal element of each binder phase component. And sintered materials for tools.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3209635A JP2858600B2 (en) | 1991-08-21 | 1991-08-21 | Sintered materials for tools |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3209635A JP2858600B2 (en) | 1991-08-21 | 1991-08-21 | Sintered materials for tools |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0551267A true JPH0551267A (en) | 1993-03-02 |
| JP2858600B2 JP2858600B2 (en) | 1999-02-17 |
Family
ID=16576059
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3209635A Expired - Lifetime JP2858600B2 (en) | 1991-08-21 | 1991-08-21 | Sintered materials for tools |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2858600B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6008153A (en) * | 1996-12-03 | 1999-12-28 | Sumitomo Electric Industries, Ltd. | High-pressure phase boron nitride base sinter |
| WO2013039093A1 (en) * | 2011-09-12 | 2013-03-21 | 三菱マテリアル株式会社 | Cutting tool made of cubic boron nitride-based sintered material |
| WO2013172095A1 (en) * | 2012-05-16 | 2013-11-21 | 三菱マテリアル株式会社 | Cutting tool made from cubic boron nitride-based sintered material |
| JP2014147988A (en) * | 2013-01-31 | 2014-08-21 | Mitsubishi Materials Corp | Cutting tool made of cubic boron nitride-based sintered material |
| GB2591316A (en) * | 2019-09-13 | 2021-07-28 | Element Six Uk Ltd | Sintered polycrystalline cubic boron nitride material |
-
1991
- 1991-08-21 JP JP3209635A patent/JP2858600B2/en not_active Expired - Lifetime
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6008153A (en) * | 1996-12-03 | 1999-12-28 | Sumitomo Electric Industries, Ltd. | High-pressure phase boron nitride base sinter |
| WO2013039093A1 (en) * | 2011-09-12 | 2013-03-21 | 三菱マテリアル株式会社 | Cutting tool made of cubic boron nitride-based sintered material |
| JP2013075357A (en) * | 2011-09-12 | 2013-04-25 | Mitsubishi Materials Corp | Cutting tool formed of cubic boron nitride-based sintered material |
| CN103796778A (en) * | 2011-09-12 | 2014-05-14 | 三菱综合材料株式会社 | Cutting tool made of cubic boron nitride-based sintered material |
| US9499441B2 (en) | 2011-09-12 | 2016-11-22 | Mitsubishi Materials Corporation | Cutting tool made of cubic boron nitride-based sintered material |
| WO2013172095A1 (en) * | 2012-05-16 | 2013-11-21 | 三菱マテリアル株式会社 | Cutting tool made from cubic boron nitride-based sintered material |
| US9662711B2 (en) | 2012-05-16 | 2017-05-30 | Mitsubishi Materials Corporation | Cutting tool made of cubic boron nitride-based sintered material |
| JP2014147988A (en) * | 2013-01-31 | 2014-08-21 | Mitsubishi Materials Corp | Cutting tool made of cubic boron nitride-based sintered material |
| GB2591316A (en) * | 2019-09-13 | 2021-07-28 | Element Six Uk Ltd | Sintered polycrystalline cubic boron nitride material |
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| Publication number | Publication date |
|---|---|
| JP2858600B2 (en) | 1999-02-17 |
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