JP3733613B2 - Diamond sintered body and manufacturing method thereof - Google Patents
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Description
【０００１】
【発明の属する技術分野】
本発明はダイヤモンド焼結体およびその製造方法に関するものである。本発明のダイヤモンド焼結体は非鉄金属やセラミックス等の切削、研削工具用素材および石油堀削用途等のドリルビットの刃先素材として有効に使用できるものである。
【０００２】
【従来の技術】
従来のダイヤモンド焼結体としては、焼結助剤あるいは結合剤としてＣｏ、Ｎｉ、Ｆｅなどの鉄族金属を用いたものや、ＳｉＣなどのセラミックスを用いたものが知られており、非鉄金属の切削工具や、堀削ビットなどに工業的に利用されている。
また、焼結助剤として炭酸塩を用いたものが知られている（特開平４−７４７６６号公報、特開平４−１１４９６６号公報）。
その他、天然のダイヤモンド焼結体（カーボナード）があるが、材質のバラツキが大きく、また産出量も極少量であるため、ほとんど工業的には使用されていない。
【０００３】
【発明が解決しようとする課題】
Ｃｏなどの鉄族金属を焼結助剤としたダイヤモンド焼結体は、Ｃｏなどの鉄族金属がダイヤモンドの黒鉛化を促す触媒として作用するため耐熱性に劣る。すなわち、不活性ガス雰囲気中で、７００℃程度で黒鉛化してしまう。また、ダイヤモンド粒の粒界にＣｏなどの金属が連続相として存在するため焼結体の強度はあまり高くなく、欠損しやしい。そして、この金属とダイヤモンドの熱膨張差のため熱劣化が起こり易くなるという問題もある。
耐熱性を上げるために上記の粒界の金属を酸処理により除去されたものも知られている。これにより耐熱温度は約１２００℃と向上するが、焼結体が多孔質となるため強度がさらに大幅（３０％程度）に低下する。
ＳｉＣを結合剤としたダイヤモンド焼結体は耐熱性には優れているが、ダイヤモンド粒同士は結合がないため、強度は低い。
一方、焼結助剤として炭酸塩を用いたダイヤモンド焼結体は、Ｃｏ結合剤による焼結体に比べると耐熱性に優れるが、１０００℃程度よりで炭酸塩の分解がはじまり焼結体の強度が低下する。また、炭酸塩は酸に溶けるため、堀削ビットなどの用途で使用できない。
本発明は以上の問題点を解決して、耐欠損性、耐熱性、耐酸性を有するダイヤモンド焼結体とその製造方法を提供することを意図したものである。
【０００４】
【課題を解決するための手段】
上記の課題を解決するための手段として、本発明は、鉄、コバルト、ニッケルおよびマンガンから選ばれる一種以上の金属のチタン酸塩を０．１〜３０体積％含み、残部がダイヤモンドであることを特徴とするダイヤモンド焼結体を提供する。また、鉄、コバルト、ニッケルおよびマンガンから選ばれる一種以上の金属の酸化物と、酸化チタンと、からなる複合酸化物または固溶体を０．１〜３０体積％含み、残部がダイヤモンドであることを特徴とするダイヤモンド焼結体を提供する。
【０００５】
また、このダイヤモンド焼結体の製造方法として、鉄、コバルト、ニッケルおよびマンガンから選ばれる一種以上の金属のチタン酸塩を焼結助剤として用い、該焼結助剤の粉末と、ダイヤモンド粉末もしくは非ダイヤモンド炭素粉末またはダイヤモンドと非ダイヤモンド炭素との混合粉末と、を混合し、これをダイヤモンドの熱力学的安定領域の圧力、温度条件で保持し、焼結する方法を提供する。
このダイヤモンド焼結体の別の製造方法として、鉄、コバルト、ニッケルおよびマンガンから選ばれる一種以上の金属のチタン酸塩を焼結助剤として用い、該焼結助剤の粉末の成形体と、ダイヤモンド粉末の成形体もしくは非ダイヤモンド炭素粉末の成形体またはダイヤモンドと非ダイヤモンド炭素との混合粉末の成形体と、を積層し、これをダイヤモンドの熱力学的安定領域の圧力、温度条件で保持し、焼結する方法を提供する。
【０００６】
【発明の実施の形態】
従来、鉄、コバルト、ニッケルおよびマンガンから選ばれる金属のチタン酸塩や、鉄、コバルト、ニッケルおよびマンガンから選ばれる金属の酸化物と酸化チタンの混合物がダイヤモンド焼結体の有効な焼結助剤として用いられた例はない。今回、本発明者らにより、これらの物質を焼結助剤とすることで、従来にない高強度で、かつ耐欠損性、耐熱性、耐食性に優れたダイヤモンド焼結体が得られることが見いだされ、本発明に至った。
本発明の特徴は、ダイヤモンド焼結体の焼結助剤として鉄、コバルト、ニッケルおよびマンガンから選ばれる金属のチタン酸塩あるいは、鉄、コバルト、ニッケルおよびマンガンから選ばれる金属の酸化物と酸化チタンの混合物を用いた点にある。
鉄、コバルト、ニッケルおよびマンガンから選ばれる金属のチタン酸塩としては、例えば、ＦｅＴｉＯ3 、ＦｅＴｉ2 Ｏ5 、ＣｏＴｉＯ3 、ＭｎＴｉＯ3 、ＮｉＴｉＯ3 などが挙げられる。これらは、ダイヤモンドに対し、強い触媒作用を示し、これらを焼結助剤とするとダイヤモンド粒子が極めて強固に結合したマトリックスが形成される。また、異常粒成長が起こり難く、均質な組織の焼結体が得られる。その結果、従来にない高強度で耐欠損性や耐摩耗性に優れたダイヤモンド焼結体が得られる。このような焼結助剤は０．０１〜１０μｍの粒径範囲のものが好ましい。
【０００７】
こうして得られるダイヤモンド焼結体は、鉄やコバルトなどの金属とチタンおよび酸素を含有する化合物からなる物質を含むのが特徴で、このような物質としては、上記のような鉄やコバルトなどのチタン酸塩、あるいは酸化鉄や酸化コバルトなどの酸化物と酸化チタンの複合酸化物もしくは固溶体が挙げられる。これらの物質は１３００℃程度の高温下でも安定で、また、酸やアルカリに対しても安定である。このため、本発明のダイヤモンド焼結体は耐熱性や耐食性にも非常に優れた特性を示す。
【０００８】
本発明のダイヤモンド焼結体において、鉄、コバルト、ニッケルおよびマンガンから選ばれる金属とチタンおよび酸素を含有する化合物からなる物質の含有量は０．１〜３０体積％が好ましいが、この理由は０．１体積％未満ではダイヤモンド粒子間の結合性、すなわち焼結性が低下し、３０体積％を越えると過剰のチタン酸化物の影響で、強度、耐摩耗性が低下するからである。
原料としては合成ダイヤモンド粉末、天然ダイヤモンド粉末、多結晶ダイヤモンド粉末などを用いることができる。粉末の粒径は０．０１〜２００μｍで、用途によって微粒または粗粒に粒径を揃えたもの、もしくは微粒、粗粒の混合物を用いる。
また、これらのダイヤモンドに代えて黒鉛やグラッシーカーボン、熱分解黒鉛などの非ダイヤモンドも原料とすることができる。また、ダイヤモンドとこれら非ダイヤモンド黒鉛の混合物を用いることもできる。
【０００９】
本発明のダイヤモンド焼結体の製造方法としては、ダイヤモンド粉末や非ダイヤモンド粉末と、鉄やコバルトのチタン酸塩あるいは酸化鉄や酸化コバルトと酸化チタンの混合物とを、ダイヤモンドが熱力学的に安定な圧力、温度条件下で保持する方法と、ダイヤモンド粉末や非ダイヤモンド黒鉛の成形体と、鉄やコバルトのチタン酸塩あるいは酸化鉄や酸化コバルトと酸化チタンの混合物の成形体を積層したものを原料として、上記の圧力、温度条件下で保持する方法がある。 原料と焼結助剤を混合する方法においては、原料と焼結助剤を、機械的に乾式または湿式混合した粉末を圧縮成形したもの、もしくはＭｏ等のカプセルに充填したものを高圧高温焼結する。原料粉末が微粒でも焼結助剤を均一に分散でき、また、厚い形状のダイヤモンド焼結体の製造が可能である。例えば、良好な仕上げ面が必要な切削工具（微粒焼結体）の製造や、ダイスなどの厚い形状を必要とする焼結体の製造に適する。ただし、粗粒の原料を用いた場合、均一に焼結助剤を混合するのに困難を要す。
一方、原料と焼結助剤を積層配置する方法は、原料と焼結助剤の板状の成形体をそれぞれ作製し、これらを積層して接触させ、高圧高温処理する。このとき、焼結助剤が原料層に拡散含浸し、ダイヤモンド粒子が焼結する。この方法は、粗粒の原料を用いても焼結助剤を均一に添加できるため、より高強度で耐摩耗性のあるダイヤモンド焼結体を安定して得ることができ、耐摩耗工具やドリルビットなどの焼結体の製造に適する。
【００１０】
【実施例】
以下本発明を実施例により更に詳細に説明するが、本発明をこれによって限定するものではない。
（実施例１）
焼結助剤としてＦｅＴｉＯ3 を用いた。平均粒径３．５μｍの合成ダイヤモンド粉末と、粒径１〜２μｍのＦｅＴｉＯ3 の粉末をそれぞれ９５体積％、５体積％の割合で十分に混合し、この混合物をＭｏカプセルに入れ、ベルト型の超高圧高温発生装置を用いて、７．５ＧＰａ２０００℃の圧力温度条件で１５分間保持し、焼結させた。得られたダイヤモンド焼結体について、Ｘ線回折により組成を固定したところ、ダイヤモンドの他、約５体積％のＦｅＴｉＯ3 が検出された。この焼結体の硬度をヌープ圧子により評価したところ７８００ｋｇ／ｍｍ2 と高硬度であった。また、破壊靱性をインデンテーション法により従来の市販のＣｏ結合剤焼結体に対し相対比較したところ、従来焼結体の約１．４倍の相対靱性であった。また、得られた焼結体を真空中で１２００℃に加熱処理した後、硬度、靱性を測定したが、処理前とほとんど変化がなかった。また、酸処理による焼結体の劣化は認められなかった。
【００１１】
（実施例２）
焼結助剤として、５体積％のＣｏＴｉＯ3 を用いた他は、実施例１と同様にしてダイヤモンド焼結体を作製した。得られた焼結体にはＣｏＴｉＯ3 が含まれており、硬度、靱性、耐熱性とも実施例１と同様であった。
【００１２】
（実施例３）
焼結助剤として、５体積％のＮｉＴｉＯ3 を用いた他は、実施例１と同様にしてダイヤモンド焼結体を作製した。得られた焼結体にはＮｉＴｉＯ3 が含まれており、硬度、靱性、耐熱性とも実施例１と同様であった。
【００１３】
（実施例４）
焼結助剤として、５体積％のＭｎＴｉＯ3 を用いた他は、実施例１と同様にしてダイヤモンド焼結体を作製した。得られた焼結体にはＭｎＴｉＯ3 が含まれており、硬度、靱性、耐熱性とも実施例１と同様であった。
【００１４】
（実施例５）
焼結助剤として、ＦｅＯとＴｉＯ2 の１：１（体積比）の混合物を用い、実施例１と同様にしてダイヤモンド焼結体を作製した。得られた焼結体にはＦｅＴｉＯ3 が含まれており、硬度、靱性、耐熱性とも実施例１と同様であった。
【００１５】
（実施例６）
焼結助剤として、ＣｏＯとＴｉＯ2 の１：１（体積比）の混合物を用い、実施例１と同様にしてダイヤモンド焼結体を作製した。得られた焼結体にはＣｏＴｉＯ3 が含まれており、硬度、靱性、耐熱性とも実施例１と同様であった。
【００１６】
（実施例７）
焼結助剤としてＦｅＴｉＯ3 を用いた。平均粒径１５μｍの合成ダイヤモンド粉末と粒径１〜２μｍのＦｅＴｉＯ3 粉末をそれぞれ厚み２ｍｍ、１ｍｍに成形したものを交互に積層してＭｏカプセルに入れ、ベルト型の超高圧高温発生装置を用いて、７．５ＧＰａ、２０００℃の圧力温度条件で１５分間保持し焼結した。得られたダイヤモンド焼結体について、Ｘ線回折により組成を固定したところ、ダイヤモンドの他、約２体積％のＦｅＴｉＯ3 が検出された。この焼結体の硬度をヌープ圧子により評価したところ約８０００ｋｇ／ｍｍ2 と高硬度であった。また、破壊靱性をインデンテーション法により従来の市販のＣｏ結合剤焼結体に対し相対比較したところ、従来焼結体の約１．４倍の相対靱性であった。また、得られた焼結体を真空中で１２００℃に加熱処理した後、硬度、靱性を測定したが、処理前とほとんど変化がなかった。また、酸処理による焼結体の劣化は認められなかった。
【００１７】
（実施例８）
焼結助剤としてＦｅＴｉＯ3 を用いた。平均粒径３μｍの高純度等方性黒鉛の厚み２ｍｍの状焼結体と、粒径１〜２μｍのＦｅＴｉＯ3 の粉末を厚み１ｍｍに型押し成形したものを交互に積層してＭｏカプセルに入れ、ガードル型の超高圧高温発生装置を用いて、７．５ＧＰａ、２０００℃の圧力温度条件で１５分間保持し、焼結させた。得られたダイヤモンド焼結体について、Ｘ線回折により組成を同定したところ、ダイヤモンドの他、約３体積％のＦｅＴｉＯ3 が検出された。この焼結体の硬度をヌープ圧子により評価したところ約７８００ｋｇ／ｍｍ2 と高硬度であった。また、破壊靱性をインデンテーション法により従来の市販のＣｏ結合剤焼結体に対し相対比較したところ、従来焼結体の約１．３倍の相対靱性であった。また、得られた焼結体を真空中で１２００℃に加熱処理した後、硬度、靱性を測定したが、処理前とほとんど変化がなかった。また、酸処理による焼結体の劣化は認められなかった。
【００１８】
（比較例１）
焼結助剤としてＦｅＴｉＯ3 を用いた。平均粒径３．５μｍの合成ダイヤモンド粉末に微量の粒径１〜２μｍのＦｅＴｉＯ3 の粉末（約０．０５体積％）添加し、十分に混合したものを原料にした他は、実施例１と同様にダイヤモンド焼結体の製造を試みた。しかし、得られた焼結体には、未焼結部が多く残留していた。
【００１９】
（比較例２）
焼結助剤としてＦｅＴｉＯ3 を用いた。平均粒径３．５μｍの合成ダイヤモンド粉末６０体積％と、粒径１〜２μｍのＦｅＴｉＯ3 の粉末４０体積％を添加し、十分に混合したものを原料にした他は、実施例１と同様にダイヤモンド焼結体の製造を試みた。しかし、得られた焼結体は、粒子同士の結合が十分でなく、硬度は３５００ｋｇ／ｍｍ2 程度と低かった。
【００２０】
【発明の効果】
以上説明したように、本発明のダイヤモンド焼結体は、従来にない高強度で、耐熱性、耐欠損性、耐食性を有するので、非鉄金属やセラミックス等の切削、研削工具用素材の他、石油堀削用途等のドリルビットの刃先素材として有効に使用できる。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a diamond sintered body and a method for producing the same. The diamond sintered body of the present invention can be effectively used as a cutting edge material for drill bits for cutting non-ferrous metals, ceramics, etc., grinding tool materials, and petroleum drilling applications.
[0002]
[Prior art]
As conventional diamond sintered bodies, those using iron group metals such as Co, Ni, and Fe as sintering aids or binders and those using ceramics such as SiC are known. It is used industrially for cutting tools and excavation bits.
In addition, those using carbonate as a sintering aid are known (Japanese Patent Laid-Open Nos. 4-74766 and 4-114966).
In addition, there is a natural diamond sintered body (carbonado), but due to the large variation in materials and the extremely small amount of production, it is hardly used industrially.
[0003]
[Problems to be solved by the invention]
A diamond sintered body using an iron group metal such as Co as a sintering aid is inferior in heat resistance because the iron group metal such as Co acts as a catalyst for promoting graphitization of diamond. That is, it graphitizes at about 700 ° C. in an inert gas atmosphere. In addition, since a metal such as Co is present as a continuous phase at the grain boundaries of the diamond grains, the strength of the sintered body is not so high and is easily damaged. And there also exists a problem that thermal deterioration becomes easy to occur because of the thermal expansion difference between this metal and diamond.
In order to increase the heat resistance, those obtained by removing the metal at the grain boundary by acid treatment are also known. As a result, the heat resistance temperature is improved to about 1200 ° C., but since the sintered body becomes porous, the strength is further greatly reduced (about 30%).
A diamond sintered body using SiC as a binder is excellent in heat resistance, but the diamond grains are not bonded to each other, so that the strength is low.
On the other hand, a diamond sintered body using carbonate as a sintering aid is superior in heat resistance compared to a sintered body using a Co binder, but the decomposition of the carbonate starts at about 1000 ° C and the strength of the sintered body. Decreases. Further, since carbonate is soluble in acid, it cannot be used for applications such as excavation bits.
The present invention intends to solve the above problems and provide a diamond sintered body having fracture resistance, heat resistance and acid resistance and a method for producing the same.
[0004]
[Means for Solving the Problems]
As a means for solving the above-mentioned problems, the present invention includes 0.1 to 30% by volume of a titanate of one or more metals selected from iron, cobalt, nickel and manganese , with the balance being diamond. A diamond sintered body is provided . Further, it contains 0.1 to 30% by volume of a composite oxide or solid solution composed of one or more metal oxides selected from iron, cobalt, nickel and manganese and titanium oxide, and the balance is diamond. A diamond sintered body is provided .
[0005]
Further, as a method for producing this diamond sintered body, a titanate of one or more metals selected from iron, cobalt, nickel and manganese is used as a sintering aid, and the powder of the sintering aid and diamond powder or Provided is a method of mixing non-diamond carbon powder or a mixed powder of diamond and non-diamond carbon, and holding and sintering this under pressure and temperature conditions in a thermodynamically stable region of diamond.
As another method for producing this diamond sintered body, a titanate of one or more metals selected from iron, cobalt, nickel and manganese is used as a sintering aid, and a powder compact of the sintering aid, A diamond powder molded body or a non-diamond carbon powder molded body or a diamond and non-diamond carbon mixed powder molded body is laminated, and this is held at the pressure and temperature conditions of the thermodynamic stability region of diamond, A method of sintering is provided .
[0006]
DETAILED DESCRIPTION OF THE INVENTION
Conventionally, a titanate of a metal selected from iron, cobalt, nickel, and manganese, and a mixture of a metal oxide selected from iron, cobalt, nickel, and manganese and titanium oxide are effective sintering aids for a diamond sintered body. There is no example used as. This time, the present inventors have found that by using these substances as sintering aids, a diamond sintered body having high strength and excellent fracture resistance, heat resistance, and corrosion resistance can be obtained. This led to the present invention.
A feature of the present invention is that a titanium titanate of a metal selected from iron, cobalt, nickel and manganese or a metal oxide selected from iron, cobalt, nickel and manganese and titanium oxide as a sintering aid for a diamond sintered body It is in the point using the mixture of.
Iron, cobalt, as the titanates of metal selected from nickel and manganese, for example, FeTiO 3, FeTi 2 O 5 , CoTiO 3, MnTiO 3, etc. NiTiO 3 and the like. These have a strong catalytic action on diamond, and when these are used as sintering aids, a matrix is formed in which diamond particles are extremely firmly bonded. Moreover, abnormal grain growth hardly occurs, and a sintered body having a homogeneous structure can be obtained. As a result, it is possible to obtain a diamond sintered body having a high strength and excellent fracture resistance and wear resistance, which has not been conventionally obtained. Such a sintering aid preferably has a particle size range of 0.01 to 10 μm.
[0007]
The diamond sintered body obtained in this way is characterized by containing a substance composed of a compound containing metal such as iron or cobalt and titanium and oxygen. Examples of such a substance include titanium such as iron and cobalt as described above. Examples thereof include acid salts, and composite oxides or solid solutions of oxides such as iron oxide and cobalt oxide and titanium oxide. These substances are stable even at a high temperature of about 1300 ° C., and are stable against acids and alkalis. For this reason, the diamond sintered body of the present invention exhibits very excellent characteristics in heat resistance and corrosion resistance.
[0008]
In the diamond sintered body of the present invention, the content of the substance composed of a metal selected from iron, cobalt, nickel and manganese and a compound containing titanium and oxygen is preferably 0.1 to 30% by volume. When the amount is less than 1% by volume, the bondability between diamond particles, that is, the sinterability is lowered, and when it exceeds 30% by volume, the strength and wear resistance are lowered due to the influence of excess titanium oxide.
As a raw material, synthetic diamond powder, natural diamond powder, polycrystalline diamond powder, or the like can be used. The powder has a particle size of 0.01 to 200 μm, and a fine or coarse particle having a uniform particle size or a mixture of fine and coarse particles is used depending on the application.
Further, in place of these diamonds, non-diamonds such as graphite, glassy carbon, and pyrolytic graphite can be used as a raw material. A mixture of diamond and these non-diamond graphites can also be used.
[0009]
The diamond sintered body of the present invention can be produced by using diamond powder or non-diamond powder and iron or cobalt titanate or a mixture of iron oxide or cobalt oxide and titanium oxide in which the diamond is thermodynamically stable. The raw material is a method of holding under pressure and temperature conditions, diamond powder and non-diamond graphite compacts, and iron or cobalt titanate or iron oxide or a mixture of cobalt oxide and titanium oxide. There is a method of holding under the above pressure and temperature conditions. In the method of mixing the raw material and the sintering aid, high-pressure and high-temperature sintering is performed by compressing and molding the raw material and the sintering aid into a mechanically dry or wet-mixed powder or filling a capsule such as Mo. To do. Even if the raw material powder is fine, the sintering aid can be uniformly dispersed, and a thick diamond sintered body can be produced. For example, it is suitable for manufacturing a cutting tool (fine sintered body) that requires a good finished surface and a sintered body that requires a thick shape such as a die. However, when using coarse raw materials, it is difficult to mix the sintering aid uniformly.
On the other hand, the raw material and the sintering aid are laminated and prepared by preparing plate-like molded bodies of the raw material and the sintering aid, laminating them and bringing them into contact with each other, followed by high-pressure and high-temperature treatment. At this time, the sintering aid diffuses and impregnates the raw material layer, and the diamond particles are sintered. In this method, since a sintering aid can be uniformly added even when coarse raw materials are used, a diamond sintered body with higher strength and wear resistance can be stably obtained, and wear resistant tools and drills can be obtained. Suitable for manufacturing sintered bodies such as bits.
[0010]
【Example】
The present invention will be described in more detail below by way of examples, but the present invention is not limited thereby.
Example 1
FeTiO 3 was used as a sintering aid. Synthetic diamond powder having an average particle size of 3.5 μm and FeTiO 3 powder having a particle size of 1 to 2 μm are sufficiently mixed at a ratio of 95% by volume and 5% by volume, respectively, and this mixture is put into a Mo capsule. Using an ultra-high pressure and high temperature generator, it was held for 15 minutes under a pressure temperature condition of 7.5 GPa 2000 ° C. and sintered. When the composition of the obtained diamond sintered body was fixed by X-ray diffraction, about 5% by volume of FeTiO 3 was detected in addition to diamond. When the hardness of this sintered body was evaluated using a Knoop indenter, it was a high hardness of 7800 kg / mm 2 . Further, when the fracture toughness was compared relative to a conventional commercially available Co binder sintered body by an indentation method, the relative toughness was about 1.4 times that of the conventional sintered body. Moreover, after heat-processing the obtained sintered compact at 1200 degreeC in the vacuum, the hardness and toughness were measured, but there was almost no change with the process front. Moreover, deterioration of the sintered compact by acid treatment was not recognized.
[0011]
(Example 2)
A diamond sintered body was produced in the same manner as in Example 1 except that 5% by volume of CoTiO 3 was used as a sintering aid. The obtained sintered body contained CoTiO 3 , and the hardness, toughness, and heat resistance were the same as in Example 1.
[0012]
Example 3
A diamond sintered body was produced in the same manner as in Example 1 except that 5% by volume of NiTiO 3 was used as a sintering aid. The obtained sintered body contained NiTiO 3 and had the same hardness, toughness and heat resistance as in Example 1.
[0013]
(Example 4)
A diamond sintered body was produced in the same manner as in Example 1 except that 5% by volume of MnTiO 3 was used as a sintering aid. The obtained sintered body contained MnTiO 3 , and the hardness, toughness and heat resistance were the same as in Example 1.
[0014]
(Example 5)
A diamond sintered body was produced in the same manner as in Example 1 using a 1: 1 (volume ratio) mixture of FeO and TiO 2 as a sintering aid. The obtained sintered body contained FeTiO 3 , and the hardness, toughness and heat resistance were the same as in Example 1.
[0015]
(Example 6)
A diamond sintered body was produced in the same manner as in Example 1 using a 1: 1 (volume ratio) mixture of CoO and TiO 2 as a sintering aid. The obtained sintered body contained CoTiO 3 , and the hardness, toughness, and heat resistance were the same as in Example 1.
[0016]
(Example 7)
FeTiO 3 was used as a sintering aid. Synthetic diamond powder with an average particle size of 15 μm and FeTiO 3 powder with a particle size of 1 to 2 μm, each formed to a thickness of 2 mm and 1 mm, are alternately stacked and placed in a Mo capsule, using a belt-type ultra-high pressure and high temperature generator , 7.5 GPa, 2000 ° C. under pressure and temperature conditions for 15 minutes, and sintered. When the composition of the obtained sintered diamond was fixed by X-ray diffraction, about 2% by volume of FeTiO 3 was detected in addition to diamond. When the hardness of this sintered body was evaluated using a Knoop indenter, it was high as about 8000 kg / mm 2 . Further, when the fracture toughness was compared relative to a conventional commercially available Co binder sintered body by an indentation method, the relative toughness was about 1.4 times that of the conventional sintered body. Moreover, after heat-processing the obtained sintered compact at 1200 degreeC in the vacuum, the hardness and toughness were measured, but there was almost no change with the process front. Moreover, deterioration of the sintered compact by acid treatment was not recognized.
[0017]
(Example 8)
FeTiO 3 was used as a sintering aid. A 2 mm thick sintered compact of high purity isotropic graphite with an average particle diameter of 3 μm and an FeTiO 3 powder with a particle diameter of 1 to 2 μm embossed to a thickness of 1 mm are alternately stacked and placed in a Mo capsule. Using a girdle type ultra-high pressure and high temperature generator, it was held for 15 minutes under pressure conditions of 7.5 GPa and 2000 ° C. and sintered. When the composition of the obtained sintered diamond was identified by X-ray diffraction, about 3% by volume of FeTiO 3 was detected in addition to diamond. When the hardness of this sintered body was evaluated with a Knoop indenter, it was as high as about 7800 kg / mm 2 . Further, when the fracture toughness was compared with a conventional commercially available Co binder sintered body by an indentation method, the relative toughness was about 1.3 times that of the conventional sintered body. Moreover, after heat-processing the obtained sintered compact at 1200 degreeC in the vacuum, the hardness and toughness were measured, but there was almost no change with the process front. Moreover, deterioration of the sintered compact by acid treatment was not recognized.
[0018]
(Comparative Example 1)
FeTiO 3 was used as a sintering aid. Example 1 except that a minute amount of FeTiO 3 powder (about 0.05% by volume) was added to synthetic diamond powder having an average particle size of 3.5 μm and thoroughly mixed to obtain a raw material. Similarly, production of a diamond sintered body was attempted. However, many unsintered parts remained in the obtained sintered body.
[0019]
(Comparative Example 2)
FeTiO 3 was used as a sintering aid. The same as in Example 1 except that 60% by volume of synthetic diamond powder having an average particle size of 3.5 μm and 40% by volume of FeTiO 3 powder having a particle size of 1 to 2 μm were added and mixed thoroughly. An attempt was made to produce a diamond sintered body. However, the obtained sintered body had insufficient bonding between particles, and the hardness was as low as about 3500 kg / mm 2 .
[0020]
【The invention's effect】
As described above, since the diamond sintered body of the present invention has unprecedented high strength, heat resistance, fracture resistance, and corrosion resistance, in addition to cutting materials such as non-ferrous metals and ceramics, materials for grinding tools, petroleum It can be used effectively as a cutting edge material for drill bits for excavation.
Claims (4)
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17209595A JP3733613B2 (en) | 1995-07-07 | 1995-07-07 | Diamond sintered body and manufacturing method thereof |
| ZA965744A ZA965744B (en) | 1995-07-07 | 1996-07-05 | A diamond sintered compact and a process for the production of the same |
| US08/675,932 US5769176A (en) | 1995-07-07 | 1996-07-05 | Diamond sintered compact and a process for the production of the same |
| EP96305018A EP0752267A3 (en) | 1995-07-07 | 1996-07-08 | A diamond sintered compact and a process for the production of the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17209595A JP3733613B2 (en) | 1995-07-07 | 1995-07-07 | Diamond sintered body and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0925163A JPH0925163A (en) | 1997-01-28 |
| JP3733613B2 true JP3733613B2 (en) | 2006-01-11 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17209595A Expired - Fee Related JP3733613B2 (en) | 1995-07-07 | 1995-07-07 | Diamond sintered body and manufacturing method thereof |
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| Country | Link |
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| JP (1) | JP3733613B2 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013176959A (en) * | 2012-01-31 | 2013-09-09 | Mitsuboshi Diamond Industrial Co Ltd | Scribing wheel, scribing device, and scribing method |
| EP4248824A3 (en) | 2017-09-22 | 2023-11-29 | SharkNinja Operating LLC | Hand-held surface cleaning device |
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| Publication number | Publication date |
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| JPH0925163A (en) | 1997-01-28 |
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