JPS6167740A - Diamond sintered body for tools and its manufacturing method - Google Patents
Diamond sintered body for tools and its manufacturing methodInfo
- Publication number
- JPS6167740A JPS6167740A JP59188492A JP18849284A JPS6167740A JP S6167740 A JPS6167740 A JP S6167740A JP 59188492 A JP59188492 A JP 59188492A JP 18849284 A JP18849284 A JP 18849284A JP S6167740 A JPS6167740 A JP S6167740A
- Authority
- JP
- Japan
- Prior art keywords
- diamond
- sintered body
- less
- volume
- particle size
- 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
- 239000010432 diamond Substances 0.000 title claims description 140
- 229910003460 diamond Inorganic materials 0.000 title claims description 137
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 239000002245 particle Substances 0.000 claims description 60
- 239000002184 metal Substances 0.000 claims description 31
- 229910052751 metal Inorganic materials 0.000 claims description 31
- 239000000843 powder Substances 0.000 claims description 31
- 239000011230 binding agent Substances 0.000 claims description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 16
- -1 iron group metals Chemical class 0.000 claims description 16
- 230000000737 periodic effect Effects 0.000 claims description 15
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 13
- 229910052796 boron Inorganic materials 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 10
- 150000001247 metal acetylides Chemical class 0.000 claims description 9
- 239000013078 crystal Substances 0.000 claims description 5
- 239000011812 mixed powder Substances 0.000 claims description 5
- 238000000034 method Methods 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 3
- 239000002253 acid Substances 0.000 claims description 2
- 238000007731 hot pressing Methods 0.000 claims 2
- 230000007423 decrease Effects 0.000 description 12
- 238000005520 cutting process Methods 0.000 description 10
- 239000011148 porous material Substances 0.000 description 7
- QZPSXPBJTPJTSZ-UHFFFAOYSA-N aqua regia Chemical compound Cl.O[N+]([O-])=O QZPSXPBJTPJTSZ-UHFFFAOYSA-N 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 239000003054 catalyst Substances 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000010828 elution Methods 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000005491 wire drawing Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910009043 WC-Co Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000000498 ball milling Methods 0.000 description 1
- 238000009412 basement excavation Methods 0.000 description 1
- 150000001639 boron compounds Chemical class 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000010438 granite Substances 0.000 description 1
- 238000005087 graphitization Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000012856 packing Methods 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 229920003023 plastic Polymers 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910021332 silicide Inorganic materials 0.000 description 1
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Landscapes
- Polishing Bodies And Polishing Tools (AREA)
- Powder Metallurgy (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
［産業上の利用分野］
この発明は、結合材を用いてダイヤモンド粒子をＨいに
接合させた工具用ダイヤモンド焼結体およびその製造方
法の改良に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to improvements in a diamond sintered body for tools, in which diamond particles are joined together using a binding material, and a method for manufacturing the same.
［従来の技術］
現在、ダイヤモンドの含有量が７０容量％以上でダイヤ
モンド粒子が互いに接合した工具用焼結体が販売されて
いる。これらの焼結体は、非鉄金−５＝
属、プラスチックあるいはセラミックの切削、ドレッサ
ー、ドリルビットまたは伸線ダイスとして用いられてい
る。特に、非鉄金属の切削や銅線などの比較的軟らかい
線材を、伸線するダイスとして、これらのダイ１７モン
ド焼結体を用いた場合、その性０しは非常に優れている
。[Prior Art] Currently, sintered bodies for tools with a diamond content of 70% by volume or more and diamond particles bonded to each other are on sale. These sintered bodies are used for cutting nonferrous metals, plastics, or ceramics, dressers, drill bits, or wire drawing dies. In particular, when these die 17 mondial sintered bodies are used as dies for cutting non-ferrous metals or drawing relatively soft wire rods such as copper wires, their properties are very excellent.
これらのダイヤモンド焼結体は、通常、ダイヤモンド粒
子をダイヤモンド合成時の触媒であるＧ。These diamond sintered bodies usually use diamond particles as a catalyst for diamond synthesis.
などの鉄族金属を結合材として用いて焼結されるもので
あるため、６００℃以上の温度に加熱した場合、ダイヤ
モンドがグラファイト化し、劣化するという欠点を有し
ている。このダイヤモンド焼結体の耐熱性を向上させる
ためには、特開昭５３−１１４．５８９号に記載されて
いるように、加熱時にダイヤモンドのグラファイト化を
促進するＣなどの鉄族金属を取除けばよい。しかしなが
ら、ダイヤモンド焼結体から、Ｃｏなどの鉄族金属を溶
出すると、ダイヤモンド焼結体の強度は約２０〜３０％
低下する。特に、ダイヤモンド焼結体をビット用途とし
て用いた場合、強度と耐摩耗性と耐熱性とが要求される
が、特開昭５３−１１７１５８９号に記載されているよ
うなダイヤモンド含有量を用いたドリルビットでは、ダ
イヤモンド焼結体の強度不足のため、刃先が欠損しか命
が短いという欠点があった。Since diamonds are sintered using iron group metals such as ferrous metals as binders, they have the disadvantage that when heated to a temperature of 600° C. or higher, diamonds turn into graphite and deteriorate. In order to improve the heat resistance of this diamond sintered body, it is necessary to remove iron group metals such as C, which promote graphitization of diamond during heating, as described in JP-A-53-114.589. Bye. However, when iron group metals such as Co are leached from the diamond sintered body, the strength of the diamond sintered body decreases by about 20 to 30%.
descend. In particular, when a diamond sintered body is used as a bit, strength, wear resistance, and heat resistance are required. Bits had the disadvantage that their lifespan was shortened due to the lack of strength of the diamond sintered body, which resulted in only chipping of the cutting edge.
本願発明者達は、先に特開昭５９−３５０６６号におい
て、強度が高（、耐摩耗性が良好であり、さらに耐熱性
に優れたダイヤモンド焼結体をＩｎ！案じている。この
焼結体は、周期什表第４ａ、５ａ。The inventors of the present invention previously proposed a diamond sintered body with high strength (high strength, good wear resistance, and excellent heat resistance) in Japanese Patent Application Laid-Open No. 59-35066. The body is periodic table 4a and 5a.
６ａ族の炭化物を結合材として用いて実質的に空孔の含
有量を減少させることにより、ＣＯ溶出による焼結体の
強度低下を抑制しようどしたものである。By using Group 6a carbide as a binder to substantially reduce the content of pores, the reduction in strength of the sintered body due to CO elution is attempted to be suppressed.
［発明が解決しにうとづる問題点］
しかしながら、この特開昭５９−３５０６６Ｑに開示し
たダイヤモンド焼結体は、たしかに強度低下こそ少ない
が、１０００℃を越える高温の下では、炭化物とダイヤ
モンドとの熱膨張差ににす、劣化が生じることがわかっ
た。したがって、地熱井掘削のように刃先が高温にさら
される用途では、未だ十分満足し得るものではなかった
。[Problems that the invention is unable to solve] However, although the diamond sintered body disclosed in JP-A-59-35066Q does not have much strength loss, at high temperatures of over 1000°C, the carbide and diamond deteriorate. It was found that deterioration occurs due to the difference in thermal expansion. Therefore, in applications where the cutting edge is exposed to high temperatures, such as geothermal well drilling, it has not yet been fully satisfactory.
それゆえに、この発明の目的は、さらに耐熱性に優れ、
かつ強度および耐摩耗性に優れた工具用ダイヤモンド焼
結体を提供することにある。Therefore, the object of this invention is to further improve heat resistance,
Another object of the present invention is to provide a diamond sintered body for tools that has excellent strength and wear resistance.
［問題点を解決ηるための手段および作用］木願発明者
達Ｃｊ：、Ｃ＋：り一層耐熱性の高いダイヤモンド焼結
体を稗るべく、鋭意研究を重ねた結果、粒度３ｆ１ｍ以
上の粗粒ダイヤモンド粒子が容量で６０〜９０％を占め
、残部が結合材５〜３９容量９６ど空孔１％以」二５％
未満より４Ｔす、該結合材の組成は粒度１μｍ以下の超
微粒のダイヤモンド粒子を容量で６０〜９５％と、１１
１ＩＩｌ以下の周ｌｌｌイ１！表第７１ａ、５ａ、５ａ
族の炭化物０．１へ・５容部％および１０容量％以下の
鉄族金属からなるダイヤモンド焼結体は、耐熱性がより
一層改善されるとともに、耐摩耗士ノ１および靭（）＋
に優れていることを見出した。[Means and actions for solving the problem] The inventors of the project Cj:, C+: As a result of intensive research in order to find a diamond sintered body with even higher heat resistance, they found a coarse diamond with a grain size of 3f1m or more Grain diamond particles account for 60 to 90% by volume, and the remainder is binder 5 to 39% by volume and 1% or more of voids.
The composition of the binder is 60 to 95% by volume of ultrafine diamond particles with a particle size of 1 μm or less, and 11
1IIl or less laps 1! Table No. 71a, 5a, 5a
Diamond sintered bodies made of iron group metals of 0.1 to 5% by volume and 10% by volume or less have further improved heat resistance, wear resistance of No. 1 and toughness () +
found that it is excellent.
この発明の焼結体は、粗粒ダイヤモンドを、微粒ダイヤ
モンドを含有する結合（オを用いて焼結するものである
。したがって、この結合材が粗粒ダイヤモンドの粒子間
に充填されるので、焼結体中のダイヤモンド含有量が極
めて高くなる。In the sintered body of the present invention, coarse diamond is sintered using a bond containing fine diamond.Therefore, this binder is filled between the particles of coarse diamond, and the sintering process is The diamond content in the compact becomes extremely high.
特に、原料ダイヤモンド粉末を、１３００℃以上の高温
で加熱し、ダイヤモンド粉末の表面を黒鉛化すれば、ダ
イヤモンド粉末の充填密度をＪ：リ一層上昇させること
が可能となり、ダイヤモンド含有量が９５％以上の緻密
な焼結体を得ることができることを見出した。In particular, if raw diamond powder is heated to a high temperature of 1,300°C or higher to graphitize the surface of the diamond powder, it is possible to further increase the packing density of the diamond powder and increase the diamond content to 95% or more. It has been found that it is possible to obtain a dense sintered body.
このダイヤモンド焼結体の耐熱性を向コーさせるには、
結合材の一部である鉄族金属を該焼結体から溶出させ、
ダイヤモンドのグラフアイｌ−化、ならびにダイヤモン
ドと鉄族金属との熱膨張差による亀裂の発生を抑圧する
必要がある。この発明のダイヤモンド焼結体では、ダイ
ヤモンドの含有量が上記のように非常に高く、したがっ
て鉄族金属を溶出させたとしても、その結果生じる空孔
が極めて少ないため、強度低下はほとｌυど生じない。To improve the heat resistance of this diamond sintered body,
eluting the iron group metal that is part of the binding material from the sintered body,
It is necessary to suppress the graphite formation of diamond and the occurrence of cracks due to the difference in thermal expansion between diamond and iron group metal. In the diamond sintered body of the present invention, the diamond content is extremely high as described above, so even if iron group metals are eluted, there are very few pores as a result, so there is almost no decrease in strength. Does not occur.
この発明のダイヤモンド焼結体が、靭性および耐摩耗性
が良好であるのは、下記の理由によると考えられる。The reason why the diamond sintered body of the present invention has good toughness and wear resistance is considered to be due to the following reasons.
ダイヤモンド焼結体の強度は、添（＝ｌの図面に示すよ
うに、粒度の増大に伴ない低下する。微粒ダイヤモンド
焼結体は抗折力が高く、靭性に優れているため、刃先は
欠損しにくいものの、個々の粒子は小さなダイヤモンド
・スケルトン部されているので、個々の粒子間の結合力
は弱い。The strength of a diamond sintered body decreases as the grain size increases, as shown in the drawing (=l).The fine-grained diamond sintered body has a high transverse rupture strength and excellent toughness, so the cutting edge will not break. Although it is difficult to do so, since each particle is made up of a small diamond skeleton, the bonding force between individual particles is weak.
したがって、切削中に個々のダイヤモンド粒子が１１ｔ
２落しやすいため、耐摩耗Ｍが劣ると考えられる。Therefore, during cutting, each individual diamond particle has 11t
2 It is considered that the wear resistance M is inferior because it is easy to drop.
他方、１１粒ダイヤモンド焼結体は大ぎなスケルトンに
より保持されており、個々のダイヤモンド粒子間の結合
力は強いため、耐摩耗性は優れているものの、スケルト
ン部が大きいので、一度クラックが発生覆る該クラック
が伝播しやすく、したがって刃先が欠損しやすくかつ靭
性が劣化するという問題が生じる。On the other hand, the 11-grain diamond sintered body is held by a large skeleton, and the bonding force between individual diamond particles is strong, so it has excellent wear resistance, but because the skeleton part is large, cracks can occur once. The problem arises that the cracks tend to propagate, and therefore the cutting edge is easily damaged and the toughness is deteriorated.
これに対して、この発明のダイヤモンド焼結体は、結合
材として微粒ダイヤモンドを含むものを用いて、粗粒ダ
イヤモンドを焼結するものであるため、微粒ダイヤモン
ドの靭性の高゛さと粗粒ダイヤモンドの耐摩耗性の良さ
とを兼備えていると考−１〇−
えられる。On the other hand, the diamond sintered body of the present invention is produced by sintering coarse-grained diamond using a material containing fine-grained diamond as a binding material. It is considered to have good wear resistance.
この発明のダイヤモンド焼結体における粗粒ダイヤモン
ドの粒度は、３ｆ１ｍ以上が好ましい。粗粒ダイヤモン
ドの粒度が３μｍ未満であると、耐摩耗性が低下するｆ
）ｓ ＋うである。なお、５μｍから２００μｍのダイ
ヤモンド粒子を用いた場合、靭性および耐摩耗性の双方
において最も優れている。The grain size of the coarse diamond in the diamond sintered body of the present invention is preferably 3f1m or more. If the particle size of coarse diamond is less than 3 μm, wear resistance decreases.
)s + arm. Note that when diamond particles of 5 μm to 200 μm are used, both toughness and wear resistance are the best.
０７ ｆｌシ＜は、粗粒ダイヤモンド粉末は、平均最大
粒径ａのものを４０〜６０容量％、粒径ａ／２のものを
４０〜３０容量％、残部が粒径ａ／３〜ａ／２０の割合
で混合したものを用いれば、高いクイヤモンド含有量を
ｉｔすることができる。For coarse diamond powder, 40 to 60% by volume of diamond powder with average maximum particle size a, 40 to 30% by volume of diamond powder with particle size a/2, and the remainder being particle size a/3 to a/a/2. If a mixture of 20% and 20% is used, a high diamond content can be obtained.
粗粒ダイヤモンドの含有量は、６０〜９０％が好ましい
。この含有量が、６０％未満であると耐摩耗性が低下し
、９０％を越えると焼結体中のダイヤモンド含有量が低
下するとともに靭性も低下するか１うである。The content of coarse diamond is preferably 60 to 90%. If this content is less than 60%, the wear resistance will decrease, and if it exceeds 90%, the diamond content in the sintered body will decrease and the toughness will also decrease.
空孔は、焼結体の容量％で１％以上５％未満が良い。空
孔の含有量が５％以上であると、ダイヤモンド焼結体の
強度は著しく低下するからであり、また１％未満である
と含有される鉄族金属の昂が多くなり、耐熱性が向上し
ないからである。結合材どして用いる超微粒のダイヤモ
ンド粒子は、１μｍ以下、好ましくは０．５μ以下が良
い。粒度が１１１ｍを越えると、焼結体の靭性が低下す
るからである。また、超微粒のダイヤモンド粒子の含有
量は、結合材中の容量で６０〜９５％が好ましい。含有
量が６０％未満であると結合材の耐摩耗性が低下するか
らであり、他方９５％を越えると結合材の靭性が低下す
るからである。The number of pores is preferably 1% or more and less than 5% by volume of the sintered body. If the pore content is 5% or more, the strength of the diamond sintered body will decrease significantly, and if it is less than 1%, the concentration of iron group metals will increase, improving heat resistance. Because they don't. The ultrafine diamond particles used as a binder have a diameter of 1 μm or less, preferably 0.5 μm or less. This is because if the particle size exceeds 111 m, the toughness of the sintered body decreases. Further, the content of ultrafine diamond particles is preferably 60 to 95% by volume in the binder. This is because if the content is less than 60%, the wear resistance of the binder will decrease, while if it exceeds 95%, the toughness of the binder will decrease.
周期律表第４ａ、５ａ、５ａ族の炭化物の含有量は、結
合材中の容量で０．１〜５％が好ましい。The content of carbides belonging to groups 4a, 5a, and 5a of the periodic table is preferably 0.1 to 5% by volume in the binder.
この含有量が、０．１％未満であるど、結合材中に鉄族
金属の異常集積部が発生し、強度および靭１１が低下す
るからであり、５％を越えると、これらの炭化物とダイ
ヤモンドとの熱膨張差により１０００℃を越える高温で
亀裂の発生が生じるからである。より好ましくは、０．
３〜３％とすれば、弾痕および耐熱性がより一層向−ヒ
される。If this content is less than 0.1%, abnormal accumulation of iron group metals will occur in the binder, resulting in a decrease in strength and toughness.If it exceeds 5%, these carbides and This is because cracks occur at high temperatures exceeding 1000° C. due to the difference in thermal expansion with diamond. More preferably 0.
When the content is 3 to 3%, bullet holes and heat resistance are further improved.
鉄族金属の含有量は、結合材中の容量で１０％１メ下が
好ましい。鉄族金属の含有量が１０％を越えると耐熱性
の向上が望めないからである。The content of the iron group metal is preferably 10% by volume in the binder. This is because if the content of iron group metal exceeds 10%, no improvement in heat resistance can be expected.
この発明のダイヤモンド焼結体では、特に、炭化物がＷ
Ｃあるいはこれと同一の結晶構造を有する（Ｍｏ 、Ｗ
）Ｃである場合に、靭性、耐摩耗性おにび耐熱性に優れ
ることがわかっている。In the diamond sintered body of this invention, in particular, the carbide is W
C or has the same crystal structure (Mo, W
) C is known to have excellent toughness, wear resistance, and heat resistance.
また、この発明の焼結体に、焼結体の重量で０゜００５
〜０．１５％の硼素または硼化物あるいはこれらの双方
を含有さけた場合、その特性は一段と向上する。通常、
ダイヤモンド粒子は、超高圧高温下で、鉄族金属などの
触媒によるダイヤモンドの溶解あるいは析出現象により
焼結される。硼素または硼素化合物の少なくとも一方を
添加した場合、鉄族金属の硼化物を生じ融点が低下する
のと、：Ｆ１解析出速度が増すためダイヤモンド粒子同
士の結合部（ダイヤモンド・スケルトン部）が成長し、
ダイヤモンド粒子の保持力が向上したものとＩＨ測でき
る。硼素あるいは硼化物の含有量が０゜００５％未満で
あると、ダイヤモンド・スケルトン部の形成は遅い。一
方、硼素あるいはけ化物の含有量が０．１５％を越える
と、ダイヤモンド・スケルトン部に多用のｌＩＩ素が侵
入し、ダイヤモンド・スケルトン部の強度が低下する。Further, the sintered body of the present invention has a weight of 0°005.
If the inclusion of ~0.15% boron and/or boride is avoided, the properties are further improved. usually,
Diamond particles are sintered under ultra-high pressure and high temperature by the phenomenon of diamond dissolution or precipitation using a catalyst such as an iron group metal. When at least one of boron or a boron compound is added, borides of iron group metals are produced, which lowers the melting point, and the :F1 analysis speed increases, causing the growth of bonds between diamond particles (diamond skeleton parts). ,
It can be determined by IH that the holding power of diamond particles has been improved. When the boron or boride content is less than 0.005%, the formation of the diamond skeleton is slow. On the other hand, if the content of boron or silicide exceeds 0.15%, a large amount of III elements will invade the diamond skeleton, reducing the strength of the diamond skeleton.
この発明のダイヤモンド焼結体に用いるダイヤモンド原
料粉末は、３μｍ以上のダイヤモンド粒子と、１μｍ以
下、好ましくは０．５７１１１１以下のミクロンパウダ
ーである。合成ダイヤモンド、天然ダイヤモンドのいず
れを用いることも可能である。The diamond raw material powder used in the diamond sintered body of the present invention includes diamond particles of 3 μm or more and micron powder of 1 μm or less, preferably 0.571111 or less. It is possible to use either synthetic diamond or natural diamond.
このダイヤモンド粉末と周期９１１表第４ａ 、 ５ａ
。This diamond powder and Periodic Table 911 Tables 4a and 5a
.
６ａ族の炭化物およびＦｅ、ｃｏ、Ｎｉなどの鉄族金属
粉末あるいはこれに硼素または硼化物を加えた粉末を、
ボールミルなどの手段を用いて均一に混合する。この鉄
族金属は、予め混合せずに焼結時に溶浸せしめてもよい
。Group 6a carbides and iron group metal powders such as Fe, co, and Ni, or powders containing boron or boride,
Mix uniformly using a ball mill or other means. This iron group metal may be infiltrated during sintering without being mixed in advance.
また、本願発明者達の先願（特願昭５２−５１８８１￥
Ｓ）のように、ボールミル時のポットとボールとを、混
入する周期律表第４ａ、５ａ、５ａ族の炭化物と鉄族金
属との焼結体で作成しておき、ダイヤモンド粉末をボー
ルミル粉砕すると同時に、ボッ１〜とボールとから周期
１１表第４ａ、５ａ、６ａ族の炭化物と鉄族金属との焼
結体の微細粉末を混入させる方法もとり得る。In addition, the inventors' earlier application (Japanese Patent Application No. 52-51881￥
As shown in S), the pot and ball for ball milling are made of a sintered body of carbides of groups 4a, 5a, and 5a of the periodic table and iron group metal, and diamond powder is ground by ball mill. At the same time, a method may be adopted in which fine powder of a sintered body of a carbide of Groups 4a, 5a, and 6a of the Periodic Table of Eleven and an iron group metal is mixed in from the balls.
）捏合された粉末を、超高圧装置に入れ、ダイヤモンド
が安定な条件の下で焼結を行なう。このどきに用いた鉄
族金属と炭化物等の化合物間に生じる共晶液相の出現温
度以上で焼結する必要がある。) The kneaded powder is placed in an ultra-high pressure device and sintered under conditions where the diamond is stable. It is necessary to sinter at a temperature higher than the temperature at which a eutectic liquid phase appears between the iron group metal and the compound such as carbide used at this time.
このようにしてＨ３Ｗされたダイヤモンド焼結体を、た
とえば王水のように鉄族金属を腐蝕し１ｑることの可能
な酸中に入れ、鉄族金属を溶出して空孔を形成する。The diamond sintered body subjected to H3W in this manner is placed in an acid such as aqua regia that can corrode iron group metals to 1q, and the iron group metals are eluted to form pores.
この発明のダイヤモンド焼結体の用途としては、ビット
のほかに、伸線ダイス、セラミック切削加工用バイト、
ドレッサーなどが挙げられる。In addition to bits, the diamond sintered body of this invention can be used as wire drawing dies, ceramic cutting tools, etc.
Examples include dressers.
［実施例１
実施例１
粒度１μｍの合成ダイヤモンド粉末を、ＷＣ−Ｃｏ超硬
合金製のポットとボールとを用いて粉砕した。ｊｑられ
た粉末の組成は、平均粒度０．５μｍの微粒ダイヤモン
ド９１容量％、ＷＣ７容量％、Ｃｏ ２容量％であった
。この粉末と、第１表に示す粗粒のダイヤモンド粉末と
を混合した。これらの完成粉末を、１０−’Ｔｏｒｒの
真空中で、１５００℃の温度で３０分間加熱処理を行な
った。しかる後、ＭＯ製の容器に詰め、ＣＯ板を完成粉
末上に１面き、超高圧装置を用いてまず圧力を５５Ｋｂ
加え、引続き１４５０℃の温ｍに加熱し１５分間保持し
た。このようにして１！７られた焼結体を容器Ｊ：り取
出ＩＪ 、加熱王水中に浸漬しＣＯを溶出させた。この
焼結体を分析したところ、第１表に示す組成を有するこ
とがわかった。次に、これらのダイヤモンド焼結体を、
真空中で１２００℃の温度にて３０分間加熱し、抗折力
試験によりその強度を測定した。[Example 1 Example 1 Synthetic diamond powder with a particle size of 1 μm was pulverized using a pot and ball made of WC-Co cemented carbide. The composition of the jqed powder was 91% by volume of fine diamond with an average particle size of 0.5 μm, 7% by volume of WC, and 2% by volume of Co. This powder was mixed with coarse diamond powder shown in Table 1. These finished powders were heat treated at a temperature of 1500°C for 30 minutes in a vacuum of 10-'Torr. After that, it is packed in an MO container, a CO plate is placed on top of the finished powder, and the pressure is first increased to 55Kb using an ultra-high pressure device.
The mixture was then heated to a temperature of 1450° C. and held for 15 minutes. The sintered body thus prepared was taken out from a container J and immersed in heated aqua regia to elute the CO. When this sintered body was analyzed, it was found that it had the composition shown in Table 1. Next, these diamond sintered bodies are
It was heated in vacuum at a temperature of 1200° C. for 30 minutes, and its strength was measured by a transverse rupture strength test.
なお、比較のために第１表に示すダイヤモンド焼結体の
強度も同時に測定した。For comparison, the strength of the diamond sintered bodies shown in Table 1 was also measured at the same time.
実施例２
第１表の試利番月３．７．９および１２のダイヤモンド
焼結体を加工し、切削工具用チップを作成した。比較の
ために、市販のＣＯを溶出した焼結ダイヤモンド（空孔
的１０％）のチップを作成した。十記試判７１３．’
７．９．１２のダイヤモンド焼結体にＪ：るチツプイｒ
らびに市販ダイヤモンド焼結体によるチップを用いて、
花崗岩を、１００ｍ／分の速度で乾式で１０分間切削を
行なった。Example 2 Diamond sintered bodies with trial numbers 3.7.9 and 12 in Table 1 were processed to produce tips for cutting tools. For comparison, a commercially available sintered diamond (10% porosity) chip from which CO was eluted was prepared. Juki trial 713. '
7.9.12 Diamond sintered body J:Ru chip r
and a chip made of a commercially available diamond sintered body.
Granite was dry-cut for 10 minutes at a speed of 100 m/min.
この結果を第２表に示す。The results are shown in Table 2.
Ｘ幕例３
第３表に示す結合材粉末を作成した。微粒ダイヤモンド
としては、平均粒径０．５１１ｍのものを用いた。この
結合材と、粒径８Ｑ７１ｍ、４０μｍおよび５〜２０μ
ｍの各ダイヤモンド粉末を６；３：１で混合した粗粒ダ
イヤモンド粒子を第４表に示す割合で混合し、完成粉末
を作成した。Curtain X Example 3 A binder powder shown in Table 3 was prepared. The fine diamond particles used had an average particle size of 0.511 m. This binder and particle size 8Q71m, 40μm and 5~20μ
Coarse diamond particles prepared by mixing 6:3:1 of each diamond powder were mixed at the ratio shown in Table 4 to prepare a finished powder.
第３表
含有量（容量％）
上記の完成粉末を、１／１５０℃の湿度で１時間真空中
で処理した後、ＭＯ製の容器に詰め、実施例１と同様に
て超高圧焼結した後、ダイヤモンド焼結体を取出し加熱
王水中で１００時間処理した。Table 3 Content (% by volume) The above finished powder was treated in vacuum at a humidity of 1/150°C for 1 hour, then packed into an MO container and sintered at ultra-high pressure in the same manner as in Example 1. Thereafter, the diamond sintered body was taken out and treated in heated aqua regia for 100 hours.
鉄族金属溶出後の焼結体の空孔の含有量もイク１せて第
４表に示す。次に、これらの焼結体を用いて、切削加工
用のバイトを作成し、ビッカース硬度２０００のアルミ
ナを８．０ｍ／分の速度で乾式で１５分間切削し、耐熱
性および強度をみた。その結果を、合せて第４表に示す
。The content of pores in the sintered body after iron group metal elution is also shown in Table 4. Next, a cutting tool was prepared using these sintered bodies, and alumina having a Vickers hardness of 2000 was dry cut at a speed of 8.0 m/min for 15 minutes to examine heat resistance and strength. The results are also shown in Table 4.
なお、第４表の試料ＮＱ、２１は、特開昭ら９−３５０
６６号に開示された組成による比較例である。試料Ｎｏ
、２１の結果と、この発明の範囲に入る試料Ｎｏ、１４
−、Ｎｏ、１９の結果の比較により、この発明の焼結体
が耐熱性および強度において優れることがわかる。In addition, sample NQ, 21 in Table 4 is published by JP-A-Kokai et al. 9-350.
This is a comparative example using the composition disclosed in No. 66. Sample No.
, 21 and sample No. 14, which falls within the scope of this invention.
Comparison of the results of No. -, No. 19 shows that the sintered body of the present invention is excellent in heat resistance and strength.
実施例４
平均粒度０．５μｍのダイヤモンド粒子と、硼素粉末を
ｗｃ−ｃｏ超硬合金製のポットとボールとを用いて粉砕
混合した。得られた混合粉末の組成は、平均粒度０．３
μｍの微粒ダイヤモンド８７容量％、ＷＣ／Ｉ容量％容
量Ｏ８容慴％、硼素１゜０容量％であった。この混合粉
末と、１００−１５０μｍ、５０−８０μｍ、１０−３
０μｍの粒径のダイヤモンド粒子を、５５：３０：１５
の比率で混合した粗粒ダイヤモンドを１５：８５の割合
で配合し、１４． Ｏ０℃の温度で１時間、真空中で処
■甲しｌこ。Example 4 Diamond particles having an average particle size of 0.5 μm and boron powder were pulverized and mixed using a pot and ball made of WC-CO cemented carbide. The composition of the obtained mixed powder has an average particle size of 0.3
The content was 87% by volume of micron diamond particles, 8% by volume of WC/I, 8% by volume of boron, and 1°0% by volume of boron. This mixed powder, 100-150 μm, 50-80 μm, 10-3
Diamond particles with a particle size of 0 μm were mixed in a ratio of 55:30:15.
Coarse diamonds mixed in the ratio of 15:85 are mixed, 14. Treat in vacuo at a temperature of 0°C for 1 hour.
このようにして１ｑられた完成粉末を、ＭＯ製の容器に
入れ、この上にＣｏ板を冒ぎ、実施例１と同様にして焼
結を行なった。ダイヤモンド焼結体中の硼素の含有量を
ｍｌｌ定したところ、Ｃ−Ｔ Ｖ’ −ｂ 。1 q of the finished powder thus obtained was placed in an MO container, a Co plate was placed on top of the container, and sintering was performed in the same manner as in Example 1. When the boron content in the diamond sintered body was determined in milliliter, it was C-TV'-b.
１％であった。It was 1%.
次に、このダイヤモンド焼結体を直ｉ￥１．５ｍｍ。Next, the diameter of this diamond sintered body was 1.5 mm.
良さ３ｍｍの円柱に加工した後、加熱王水中で１５０時
間処理した。処理後の空孔は、焼結体中に２゜５％含有
されていた。また、焼結体中のダイヤモンドの含有量は
９７．３％であった。この焼結体を、調性のシャンクに
Ｗ、ＷＣ，Ｆｅ、Ｇｏ、Ｎ＋、ＯＬ＋の混合粉末よりな
る高融点高硬度のマトリックスを１１００℃で焼結して
固定し、ザー７丁スセットのコアビットを作成した。After processing into a cylinder with a thickness of 3 mm, it was treated in heated aqua regia for 150 hours. After the treatment, the sintered body contained 2.5% of pores. Further, the diamond content in the sintered body was 97.3%. This sintered body was sintered at 1100°C with a matrix of high melting point and high hardness made of mixed powders of W, WC, Fe, Go, N+, and OL+, and fixed to the shank of a tonal shank. It was created.
比較のために、市販の４０〜６０μｍの粒径のダイヤモ
ンド粒子よりなるダイヤモンド焼結体で結合材であるＧ
ｏを溶出したもののコアピットも同様に作成した。For comparison, G, which is a commercially available diamond sintered body made of diamond particles with a particle size of 40 to 60 μm and is a binder, was used.
A core pit from which o was eluted was also created in the same manner.
これらのビットを用いて、−軸圧縮強度１８００Ｋｇ／
ｍｍ２の安山岩を回転速度９００回転／分で掘削した。Using these bits, -axial compressive strength of 1800Kg/
Andesite of mm2 was excavated at a rotational speed of 900 revolutions/min.
その結果、この発明のダイヤモンド焼結体を用いたビッ
トは、掘進速度１５ｃｍ／分で５０ｍ掘削してもまだ掘
削可能であったのに対し、市販のダイヤモンド焼結体を
用いたピッ１へは、掘進速庶８ｃｍ／分で１５ｍ掘削し
た時点で寿命となった。As a result, the bit using the diamond sintered body of the present invention was still able to dig even after digging 50m at a digging speed of 15 cm/min, whereas the bit using the commercially available diamond sintered body The life span was reached when 15 m had been excavated at an excavation speed of 8 cm/min.
［発明の効果１
以上のように、この発明にＪ：れば耐熱性、強度Ｊ５
Ｊ：び耐摩耗性に優れた工具用ダイヤモンド焼結体を１
ｑることが可能どなる。[Effect of the invention 1 As described above, this invention has J: heat resistance, strength J5
J: Diamond sintered body for tools with excellent wear resistance
Is it possible to do this?
図面は、ダイヤモンド焼結体にお【プる強度（抗折力）
と、ダイヤモンド粒度との関係を表わす図である。
炉用〜）ｇＪ、Ｉｊ−■
手続補正書The drawing shows the strength (transverse rupture strength) of the diamond sintered body.
FIG. 3 is a diagram showing the relationship between the diamond particle size and For furnace~) gJ, Ij-■ Procedural amendment
Claims (12)
６０〜９０％を占め、残部が結合材５〜３９容量％と、
空孔１％以上５％未満とよりなり、前記結合材の組成は
粒度１μｍ以下の超微粒のダイヤモンド粒子を容量で６
０〜９５％、１μｍ以下の周期律表第４ａ、５ａ、６ａ
族の炭化物０．１〜５容量％と鉄族金属１０容量％以下
とよりなるものである、工具用ダイヤモンド焼結体。(1) Coarse diamond particles with a particle size of 3 μm or more account for 60 to 90% by volume, and the remainder is a binder of 5 to 39% by volume,
The composition of the binder is 6% by volume of ultrafine diamond particles with a particle size of 1 μm or less.
0-95%, 1 μm or less Periodic Table 4a, 5a, 6a
1. A diamond sintered body for tools, which comprises 0.1 to 5% by volume of a group carbide and 10% by volume or less of an iron group metal.
μｍ以下である、特許請求の範囲第１項記載の工具用ダ
イヤモンド焼結体。(2) The particle size of coarse diamond particles is 5 μm or more 200
The diamond sintered body for tools according to claim 1, which has a diameter of μm or less.
たはＷＣと同一結晶構造を有する（Ｍｏ、Ｗ）Ｃである
、特許請求の範囲第１項または第２項記載の工具用ダイ
ヤモンド焼結体。(3) The diamond for tools according to claim 1 or 2, wherein the carbide of groups 4a, 5a, and 6a of the periodic table is WC or (Mo, W)C having the same crystal structure as WC. Sintered body.
で６０〜９０％を占め、残部が結合材５〜３９容量％と
空孔１％以上５％未満よりなり、前記結合材が粒度１μ
ｍ以下の超微粒のダイヤモンド粒子を容量で６０〜９５
％と、１μｍ以下の周期律表第４ａ、５ａ、６ａ族の炭
化物０．１〜５容量、鉄族金属１０容量％以下ならびに
硼素および／または硼化物とよりなり、硼素および／ま
たは硼化物の含有量は焼結体の重量で０．００５〜０．
１５％である、工具用ダイヤモンド焼結体。(4) Coarse diamond particles with a particle size of 3 μm or more account for 60 to 90% by volume, and the remainder consists of a binder of 5 to 39% by volume and 1% to less than 5% of voids, and the binder has a particle size of 1 μm.
Ultra-fine diamond particles with a capacity of 60 to 95 m or less
%, 0.1 to 5 volumes of carbides of Groups 4a, 5a, and 6a of the periodic table of 1 μm or less, 10 volume% or less of iron group metals, and boron and/or borides. The content is 0.005 to 0.00 by weight of the sintered body.
15%, a diamond sintered body for tools.
μｍ以下である、特許請求の範囲第４項記載の工具用ダ
イヤモンド焼結体。(5) Particle size of coarse diamond particles is 5 μm or more 200
The diamond sintered body for tools according to claim 4, which has a diameter of μm or less.
ＣまたはＷＣと同一結晶構造を有する（Ｍｏ、Ｗ）Ｃで
ある、特許請求の範囲第４項または第５項記載の工具用
ダイヤモンド焼結体。(6) The carbide of groups 4a, 5a, and 6a of the periodic table is W
The diamond sintered body for tools according to claim 4 or 5, which is (Mo, W)C having the same crystal structure as C or WC.
微粒ダイヤモンド粉末、１μｍ以下の周期律表第４ａ、
５ａ、６ａ族の炭化物ならびに鉄族金属の混合粉末とを
作成し、１３００℃以上の温度で原料粉末の一部を黒鉛
化した後、超高圧高温装置を用いて、ダイヤモンドが安
定な高温高圧下においてホットプレスし、焼結体を作成
し、該焼結体を酸処理することにより、鉄族金属の一部
を溶出することを特徴とする、３μｍ以上の粗粒のダイ
ヤモンド粒子が容量で６０〜９０％を占め、残部が結合
材５〜３９容量％と空孔１％以上５％未満よりなり、該
結合材の組成が粒度１μｍ以下の超微粒のダイヤモンド
粒子を容量で６０〜９５％と１μｍ以下の周期律表第４
ａ、５ａ、６ａ族の炭化物０．１〜５容量％および鉄族
金属１０容量％以下である、工具用ダイヤモンド焼結体
の製造方法。(7) Diamond powder of 3 μm or more, ultrafine diamond powder of 1 μm or less, periodic table 4a of 1 μm or less,
After creating a mixed powder of carbides of groups 5a and 6a and iron group metals and graphitizing a part of the raw material powder at a temperature of 1300°C or higher, using an ultra-high pressure and high temperature equipment, the diamond is heated under high temperature and high pressure where it is stable. By hot pressing to create a sintered body, and acid-treating the sintered body, coarse diamond particles of 3 μm or more are dissolved in a volume of 60 ~90% by volume, and the remainder is 5 to 39% by volume of binder and 1% to less than 5% of voids, and the composition of the binder is 60 to 95% by volume of ultrafine diamond particles with a particle size of 1 μm or less. 4th periodic table of 1 μm or less
A method for producing a diamond sintered body for tools, comprising 0.1 to 5% by volume of carbides of groups A, 5a, and 6a and 10% by volume or less of iron group metals.
００μｍ以下である、特許請求の範囲第７項記載の工具
用ダイヤモンド焼結体の製造方法。(8) The particle size of the coarse diamond particles is 5 μm or more2
8. The method for producing a diamond sintered body for tools according to claim 7, wherein the diamond sintered body has a diameter of 00 μm or less.
て、ＷＣまたはこれと同一結晶構造を有する（Ｍｏ、Ｗ
）Ｃを用いる、特許請求の範囲第７項または第８項記載
の工具用ダイヤモンド焼結体の製造方法。(9) As the carbide of groups 4a, 5a, and 6a of the periodic table, WC or having the same crystal structure (Mo, W
) A method for manufacturing a diamond sintered body for tools according to claim 7 or 8, using C.
超微粒ダイヤモンド粉末、１μｍ以下の周期律表第４ａ
、５ａ、６ａ族の炭化物、鉄族金属、ならびに硼素およ
び／または硼化物の混合粉末を作成し、１３００℃以上
の温度で原料粉末の一部を黒鉛化した後、超高圧高温装
置を用いてダイヤモンドが安定な高温・高圧下において
ホットプレスし、焼結体を作成し、該焼結体を酸処理す
ることにより鉄族金属の一部を溶出することを特徴とす
る、３μｍ以上の粗粒のダイヤモンド粒子が容量で６０
〜９０％を占め、残部が結合材５〜３９容量％と空孔１
％以上５％未満よりなり、該結合材が粒度１μｍ以下の
超微粒のダイヤモンド粒子を容量で６０〜９５％と、１
μｍ以下の周期律表第４ａ、５ａ、６ａ族の炭化物０．
１〜５容量％、鉄族金属１０容量％以下および硼素およ
び／または硼化物よりなり、該硼素および／または硼化
物の含有量が焼結体の重量で０．００５〜０．１５％で
ある、工業用ダイヤモンド焼結体の製造方法。(10) Diamond powder of 3 μm or more, ultrafine diamond powder of 1 μm or less, periodic table 4a of 1 μm or less
, 5a, 6a group carbides, iron group metals, and boron and/or boride mixed powder is created, and after graphitizing a part of the raw material powder at a temperature of 1300°C or higher, using an ultra-high pressure and high temperature equipment. Coarse grains of 3 μm or more, characterized by hot pressing under high temperature and high pressure where diamond is stable, creating a sintered body, and treating the sintered body with acid to elute a part of the iron group metal. Diamond particles have a capacity of 60
~90%, and the remainder is binder 5~39% by volume and 1 vacancy.
% or more and less than 5%, and the binder contains 60 to 95% by volume of ultrafine diamond particles with a particle size of 1 μm or less, and 1
Carbides of groups 4a, 5a, and 6a of the periodic table with a size of 0.0 μm or less.
1 to 5% by volume, 10% by volume or less of an iron group metal, and boron and/or boride, and the content of the boron and/or boride is 0.005 to 0.15% by weight of the sintered body. , a method for producing industrial diamond sintered bodies.
０μｍ以下である、特許請求の範囲第１０項記載の工具
用ダイヤモンド焼結体の製造方法。(11) The particle size of coarse diamond particles is 5 μm or more20
The method for producing a diamond sintered body for tools according to claim 10, wherein the diamond sintered body has a diameter of 0 μm or less.
して、ＷＣまたはこれと同一結晶構造を有する（Ｍｏ、
Ｗ）Ｃを用いる、特許請求の範囲第１０項または第１１
項記載の工具用ダイヤモンド焼結体の製造方法。(12) As the carbide of groups 4a, 5a, and 6a of the periodic table, WC or having the same crystal structure as this (Mo,
W) Claim 10 or 11 using C
A method for producing a diamond sintered body for tools as described in .
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59188492A JPS6167740A (en) | 1984-09-08 | 1984-09-08 | Diamond sintered body for tools and its manufacturing method |
| AU46632/85A AU571419B2 (en) | 1984-09-08 | 1985-08-26 | Diamond sintered for tools and method of manufacture |
| DE8585110715T DE3583567D1 (en) | 1984-09-08 | 1985-08-26 | SINTERED DIAMOND TOOL BODY AND METHOD FOR PRODUCING IT. |
| US06/769,609 US4636253A (en) | 1984-09-08 | 1985-08-26 | Diamond sintered body for tools and method of manufacturing same |
| EP85110715A EP0174546B1 (en) | 1984-09-08 | 1985-08-26 | Diamond sintered body for tools and method of manufacturing the same |
| ZA856653A ZA856653B (en) | 1984-09-08 | 1985-08-30 | Diamond sintered body for tools and method of manufacturing the same |
| KR1019850006553A KR900002701B1 (en) | 1984-09-08 | 1985-09-07 | Diamond sintered body for tools and method of manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59188492A JPS6167740A (en) | 1984-09-08 | 1984-09-08 | Diamond sintered body for tools and its manufacturing method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6167740A true JPS6167740A (en) | 1986-04-07 |
Family
ID=16224674
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59188492A Pending JPS6167740A (en) | 1984-09-08 | 1984-09-08 | Diamond sintered body for tools and its manufacturing method |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JPS6167740A (en) |
| ZA (1) | ZA856653B (en) |
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6324003A (en) * | 1986-07-16 | 1988-02-01 | Mitsubishi Metal Corp | Composite cutting tip |
| JP2004509054A (en) * | 2000-09-20 | 2004-03-25 | キャムコ、インターナショナル、（ユーケイ）、リミテッド | High volume density polycrystalline diamond with catalytic surface depleted working surface |
| JP2010508164A (en) * | 2006-10-31 | 2010-03-18 | エレメント シックス （プロダクション）（プロプライエタリィ） リミテッド | Polycrystalline diamond abrasive compact |
| JP2013500920A (en) * | 2009-07-31 | 2013-01-10 | エレメント シックス リミテッド | Polycrystalline diamond composite compact |
| CN105506355A (en) * | 2015-12-25 | 2016-04-20 | 北京有色金属研究总院 | Diamond/copper gradient composite material and preparation method thereof |
| US9783425B1 (en) | 2013-06-18 | 2017-10-10 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US9789587B1 (en) | 2013-12-16 | 2017-10-17 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US9908215B1 (en) | 2014-08-12 | 2018-03-06 | Us Synthetic Corporation | Systems, methods and assemblies for processing superabrasive materials |
| US10011000B1 (en) | 2014-10-10 | 2018-07-03 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US10105820B1 (en) | 2009-04-27 | 2018-10-23 | Us Synthetic Corporation | Superabrasive elements including coatings and methods for removing interstitial materials from superabrasive elements |
| US10265673B1 (en) | 2011-08-15 | 2019-04-23 | Us Synthetic Corporation | Protective leaching cups, leaching trays, and methods for processing superabrasive elements using protective leaching cups and leaching trays |
| US10723626B1 (en) | 2015-05-31 | 2020-07-28 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US10807913B1 (en) | 2014-02-11 | 2020-10-20 | Us Synthetic Corporation | Leached superabrasive elements and leaching systems methods and assemblies for processing superabrasive elements |
| US10900291B2 (en) | 2017-09-18 | 2021-01-26 | Us Synthetic Corporation | Polycrystalline diamond elements and systems and methods for fabricating the same |
| JP2022085687A (en) * | 2020-11-27 | 2022-06-08 | トーメイダイヤ株式会社 | Carbide-bonded polycrystalline diamond electrode material |
| US11420304B2 (en) | 2009-09-08 | 2022-08-23 | Us Synthetic Corporation | Superabrasive elements and methods for processing and manufacturing the same using protective layers |
| US11766761B1 (en) | 2014-10-10 | 2023-09-26 | Us Synthetic Corporation | Group II metal salts in electrolytic leaching of superabrasive materials |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5935066A (en) * | 1982-08-18 | 1984-02-25 | 住友電気工業株式会社 | Diamond sintered body for tools |
-
1984
- 1984-09-08 JP JP59188492A patent/JPS6167740A/en active Pending
-
1985
- 1985-08-30 ZA ZA856653A patent/ZA856653B/en unknown
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5935066A (en) * | 1982-08-18 | 1984-02-25 | 住友電気工業株式会社 | Diamond sintered body for tools |
Cited By (28)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6324003A (en) * | 1986-07-16 | 1988-02-01 | Mitsubishi Metal Corp | Composite cutting tip |
| JP2004509054A (en) * | 2000-09-20 | 2004-03-25 | キャムコ、インターナショナル、（ユーケイ）、リミテッド | High volume density polycrystalline diamond with catalytic surface depleted working surface |
| JP2010508164A (en) * | 2006-10-31 | 2010-03-18 | エレメント シックス （プロダクション）（プロプライエタリィ） リミテッド | Polycrystalline diamond abrasive compact |
| US10105820B1 (en) | 2009-04-27 | 2018-10-23 | Us Synthetic Corporation | Superabrasive elements including coatings and methods for removing interstitial materials from superabrasive elements |
| JP2013500920A (en) * | 2009-07-31 | 2013-01-10 | エレメント シックス リミテッド | Polycrystalline diamond composite compact |
| US12502749B2 (en) | 2009-09-08 | 2025-12-23 | Us Synthetic Corporation | Superabrasive elements and related methods for processing and manufacturing using protective layers |
| US11420304B2 (en) | 2009-09-08 | 2022-08-23 | Us Synthetic Corporation | Superabrasive elements and methods for processing and manufacturing the same using protective layers |
| US10265673B1 (en) | 2011-08-15 | 2019-04-23 | Us Synthetic Corporation | Protective leaching cups, leaching trays, and methods for processing superabrasive elements using protective leaching cups and leaching trays |
| US11383217B1 (en) | 2011-08-15 | 2022-07-12 | Us Synthetic Corporation | Protective leaching cups, leaching trays, and methods for processing superabrasive elements using protective leaching cups and leaching trays |
| US12043549B2 (en) | 2013-06-18 | 2024-07-23 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US9783425B1 (en) | 2013-06-18 | 2017-10-10 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US11370664B1 (en) | 2013-06-18 | 2022-06-28 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US9789587B1 (en) | 2013-12-16 | 2017-10-17 | Us Synthetic Corporation | Leaching assemblies, systems, and methods for processing superabrasive elements |
| US12037291B2 (en) | 2014-02-11 | 2024-07-16 | Us Synthetic Corporation | Leached diamond elements and leaching systems, methods and assemblies for processing diamond elements |
| US10807913B1 (en) | 2014-02-11 | 2020-10-20 | Us Synthetic Corporation | Leached superabrasive elements and leaching systems methods and assemblies for processing superabrasive elements |
| US11618718B1 (en) | 2014-02-11 | 2023-04-04 | Us Synthetic Corporation | Leached superabrasive elements and leaching systems, methods and assemblies for processing superabrasive elements |
| US9908215B1 (en) | 2014-08-12 | 2018-03-06 | Us Synthetic Corporation | Systems, methods and assemblies for processing superabrasive materials |
| US11253971B1 (en) | 2014-10-10 | 2022-02-22 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US11766761B1 (en) | 2014-10-10 | 2023-09-26 | Us Synthetic Corporation | Group II metal salts in electrolytic leaching of superabrasive materials |
| US12023782B2 (en) | 2014-10-10 | 2024-07-02 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US10011000B1 (en) | 2014-10-10 | 2018-07-03 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US12296435B2 (en) | 2014-10-10 | 2025-05-13 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US12544878B2 (en) | 2014-10-10 | 2026-02-10 | Us Synthetic Corporation | Leached superabrasive elements, subterranian tools with leached superabrasive elements, and related systems and methods |
| US11535520B1 (en) | 2015-05-31 | 2022-12-27 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| US10723626B1 (en) | 2015-05-31 | 2020-07-28 | Us Synthetic Corporation | Leached superabrasive elements and systems, methods and assemblies for processing superabrasive materials |
| CN105506355A (en) * | 2015-12-25 | 2016-04-20 | 北京有色金属研究总院 | Diamond/copper gradient composite material and preparation method thereof |
| US10900291B2 (en) | 2017-09-18 | 2021-01-26 | Us Synthetic Corporation | Polycrystalline diamond elements and systems and methods for fabricating the same |
| JP2022085687A (en) * | 2020-11-27 | 2022-06-08 | トーメイダイヤ株式会社 | Carbide-bonded polycrystalline diamond electrode material |
Also Published As
| Publication number | Publication date |
|---|---|
| ZA856653B (en) | 1986-04-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP0174546B1 (en) | Diamond sintered body for tools and method of manufacturing the same | |
| JPS6167740A (en) | Diamond sintered body for tools and its manufacturing method | |
| JP2004505786A (en) | Manufacturing method of polishing products containing diamond | |
| JPS5935066A (en) | Diamond sintered body for tools | |
| KR20050072753A (en) | Method for producing a sintered, supported polycrystalline diamond compact | |
| JP3902404B2 (en) | Abrasive grain production method and abrasive grain produced by this method | |
| JPS6241778A (en) | Improvement of composite polycrystal diamond plunged body | |
| JPH0530897B2 (en) | ||
| JPH083131B2 (en) | Method for manufacturing diamond sintered body for tool | |
| JPS6355161A (en) | Manufacture of industrial diamond sintered body | |
| JPH0245693B2 (en) | ||
| WO2003057936A1 (en) | Metal carbide composite | |
| JPS6319585B2 (en) | ||
| JPS58199776A (en) | Diamond sintered body for tools and its manufacturing method | |
| JPS62105911A (en) | Hard diamond mass and its manufacturing method | |
| JPS5916942A (en) | Composite diamond-sintered body useful as tool and its manufacture | |
| JPS6283447A (en) | Sintered diamond and its manufacturing method | |
| JP3481702B2 (en) | Cubic boron nitride sintered body using hard alloy as binder and method for producing the same | |
| JPS58199777A (en) | Diamond sintered body for tool and manufacture | |
| JPS5891056A (en) | Diamond sintered body for tools and manufacture | |
| JPS5899169A (en) | Diamond sintered body for tool and manufacture | |
| TW388732B (en) | 087111547 | |
| JPS61205664A (en) | Method of manufacturing conductive sintered diamond | |
| JPS60162747A (en) | Composite diamond sintered body and its production | |
| JPS58213676A (en) | Diamond sintered body for tool and manufacture |