JPS6140722B2 - - Google Patents
Info
- Publication number
- JPS6140722B2 JPS6140722B2 JP22729884A JP22729884A JPS6140722B2 JP S6140722 B2 JPS6140722 B2 JP S6140722B2 JP 22729884 A JP22729884 A JP 22729884A JP 22729884 A JP22729884 A JP 22729884A JP S6140722 B2 JPS6140722 B2 JP S6140722B2
- Authority
- JP
- Japan
- Prior art keywords
- diamond
- sintered body
- tool
- sintered
- temperature
- 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.)
- Expired
Links
- 229910003460 diamond Inorganic materials 0.000 claims description 79
- 239000010432 diamond Substances 0.000 claims description 79
- 239000002184 metal Substances 0.000 claims description 36
- 229910052751 metal Inorganic materials 0.000 claims description 36
- 239000000463 material Substances 0.000 claims description 24
- 238000005219 brazing Methods 0.000 claims description 22
- 239000011148 porous material Substances 0.000 claims description 16
- 239000000843 powder Substances 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 14
- 239000002904 solvent Substances 0.000 claims description 12
- 229910000831 Steel Inorganic materials 0.000 claims description 10
- 239000010959 steel Substances 0.000 claims description 10
- 229910052802 copper Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 238000005245 sintering Methods 0.000 claims description 8
- 150000002739 metals Chemical class 0.000 claims description 7
- 229910052709 silver Inorganic materials 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 6
- 230000008018 melting Effects 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 239000013078 crystal Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 238000005304 joining Methods 0.000 claims description 3
- 230000015572 biosynthetic process Effects 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 238000003786 synthesis reaction Methods 0.000 claims description 2
- 229910052715 tantalum Inorganic materials 0.000 claims 1
- 238000005520 cutting process Methods 0.000 description 19
- 239000011230 binding agent Substances 0.000 description 16
- 239000002245 particle Substances 0.000 description 10
- 239000010949 copper Substances 0.000 description 9
- 230000006866 deterioration Effects 0.000 description 7
- 229910000881 Cu alloy Inorganic materials 0.000 description 3
- 238000010306 acid treatment Methods 0.000 description 3
- QZPSXPBJTPJTSZ-UHFFFAOYSA-N aqua regia Chemical compound Cl.O[N+]([O-])=O QZPSXPBJTPJTSZ-UHFFFAOYSA-N 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000945 filler Substances 0.000 description 3
- 238000005470 impregnation Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910000679 solder Inorganic materials 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 229910010165 TiCu Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 239000002173 cutting fluid Substances 0.000 description 2
- 239000010730 cutting oil Substances 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- -1 iron group metals Chemical class 0.000 description 2
- 229910052755 nonmetal Inorganic materials 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052793 cadmium Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 238000005868 electrolysis reaction Methods 0.000 description 1
- 238000010828 elution Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007790 scraping Methods 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Landscapes
- Ceramic Products (AREA)
- Powder Metallurgy (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Description
ダイヤモンド粉末を超高圧下で焼結した焼結体
は、既に切削工具や線引ダイスとして一部で実用
化されている。このようなダイヤモンド焼結体と
しては結合材を含まないもの、金属を結合材とす
るもの、非金属を結合材とするものが考えられ
る。この中で結合材を含まないものは焼結に要す
る圧力、温度が高く、これを工業的に利用するこ
とはまだ難しいと考えられる。また非金属を結合
材とするものは金属を結合材とするものに比較し
て靭性の点で劣つている。金属を結合材とするダ
イヤモンド焼結体の結合金属相としてはCoを主
成分とするものが市板されている。発明者等の実
験によるとFe、Ni、Coもしくはこれ等の合金を
結合材としてダイヤモンドの安定域にある圧力、
温度条件下に一定時間保持することによつてち密
なダイヤモンド焼結体を得ることができる。これ
等の金属はダイヤモンド合成に触媒金属として使
用されるものであり、高圧、高温のダイヤモンド
安定域でダイヤモンドがこれらの金属に溶解・再
析出することによつてダイヤモンド粒間の接合が
生じ、強固なダイヤモンド粒子のスケルトンを有
する焼結体となるものと推定される。
発明者等はこれ等の鉄族金属を結合材とするダ
イヤモンド焼結体について各種の特性を調べた結
果実用上に大きな問題があることが判明した。そ
れはFe、Ni、Coの鉄族金属を結合材とするダイ
ヤモンド焼結体は約700℃に加熱することによつ
て著しく強度を失ない、例えば切削工具として用
いた場合は耐磨耗性が大巾に劣化することであ
る。ダイヤモンド焼結体を用いて、これを切削工
具に加工する場合鋼製の支持体にロウ付すること
が必要である。切削工具に限らずドリルビツト、
ドレツサー、ダイス等の製品に応用する場合ダイ
ヤモンド焼結体を支持体に固着する方法としては
一般に天然のダイヤ粒に用いれているロウ付、焼
結、鋳込み法等が考えられるが、ロウ付の場合一
般に用いられる銀ロウ材ではロウ付温度が700゜
〜850℃であり、焼結法では900℃以上の高温に加
熱される、鋳込み法でも短時間ではあるが更に高
温に加熱される場合がある。のように常圧下での
加熱に対する安定性は焼結体の応用範囲を限定す
る重要な特性である。また使用時に温度が上る用
途でも性能の劣化が予想される。この点を確認す
る為に次の実験を行なつた。
市販のCoを成分とする金属結合相を有するダ
イヤモンド焼結体を使用してこれを鋼のシヤンク
に低融点（融点約600℃）の銀ロウ材を使用して
ロウ付けした。これを加工して切削加工用のバイ
トを作成した。このバイトを用いてAl2O3を主成
分とするセラミツクを切削加工した。切削速度30
ｍ／分、切込み0.15mm、送り0.02mm／回転の条件
では切削油剤を使用しない乾式切削では５分間で
工具逃げ面摩耗巾が0.3mmに達した。一方水溶性
切削油を用いて他は同一条件のまま湿式切削する
と工具寿命は飛躍的にのびて0.3mmの逃げ面摩耗
巾となるまでに40分間切削できた。この寿命の相
違はダイヤモンド焼結体からなる工具刃先の被削
材との接触面における温度上昇の程度が異なり、
湿式切削では切削油の冷却効果により接触面温度
が低下し、ダイヤモンド焼結体の劣化が抑制され
た為工具寿命が改良されたものと考えられる。こ
のようなことは切削工具に限らず、例えば掘削用
のビツト、コアビツト等のボーリング工具又は
Mo、Ｗや鋼線など強度の高い線材の線引き加工
用ダイス、砥石成型用のドレツサーなどダイヤモ
ンド焼結体の応用が考えられる工具用途に共通し
て云えることである。
発明者等はこのダイヤモンド焼結体の加熱劣化
の原因を知る為に市販のCoを結合材とする焼結
体を500℃〜1000℃の範囲で真空炉中で30分間加
熱保持して調べたところ800℃以上に加熱された
ものはＸ線回折によりダイヤモンド以外に黒鉛が
検出された。一方ダイヤモンドの粉末のみを同じ
条件で加熱しても全く黒鉛は検出されなかつた。
このことからのダイヤモンド焼結体の加熱劣化現
象は焼結体中の結合金属であるCoがダイヤモン
ドの逆変態に際してこれを促進する作用を有して
いるものと考えられる。
ダイヤモンド粉末の焼結においてはダイヤモン
ドに対し高温、高圧下において溶媒の役割を果す
金属が結合材として存在するとダイヤモンドの溶
解折出現象によりダイヤモンド粒子相互の強固な
接合が生じ易い。一般にダイヤモンド焼結体の強
度、耐摩耗性といつた特性はこのダイヤモンド粒
子相互により形成されたスケルトンの状態に大き
く影響される。しかし前述の如く焼結体の再加熱
による劣化もこのような溶媒金属の存在によつて
いる。発明者等はこの相矛盾した点を解決する方
法を本発明で提供しようとするものである。
先ずダイヤモンド焼結体の製造に当つては例え
ば特公昭39−20483号に開示されているようにダ
イヤモンド粉末とこの溶媒金属粉末とを混合して
この混合物を超高圧、高温装置を用いてダイヤモ
ンドが安定な圧力、温度条件下で且つ溶媒金属と
ダイヤモンドの共晶融液が生じる温度以上で焼結
する（第１図参照）。しかる後にこのダイヤモン
ド焼結体中に結合相として残留する溶媒金属を酸
溶解又は電解等の方法によりその全部又は大部分
を除去する、ダイヤモンド焼結体中の結合金属相
の含有量はダイヤモンドに対する溶媒金属粉末の
混入量、ダイヤモンド粉末の粒度、焼結条件等に
よつて変化するが本発明の場合はダイヤモンドが
焼結体中で70〜95体積％を占めるようにする。ダ
イヤモンド含有量がそれ以下では焼結体中のダイ
ヤモンド結晶相互が接合した状態になり難く目的
とする強度、耐摩耗性を有する焼結体が得られな
い。このようにしてダイヤモンドの溶媒金属から
なる結合金属相を除去したのみでは当然のことな
がら焼結体内部に５〜30体積％の空孔が残る。し
かし空孔が存在することは特に焼結体を工具とし
て使用する場合には強度、耐摩耗性の面で極めて
不利である。焼結体の強度に対しては空孔は応力
集中源として作用し強度は大巾に低下する。また
耐摩耗性に対しても切削屑や摩耗粉が工具表面の
空孔中に押し込まれて摩耗を促進する要因とな
る。本発明の特徴は以上のような欠点を克服する
ために一旦ダイヤモンド焼結体から溶媒金属から
なる結合相を除去した後、この空孔中にダイヤモ
ンドと反応しない非溶媒金属を含浸せしめること
にある。これにより上記したような空孔が残留す
ることによる欠点は解消される。
一旦溶媒金属を除去したダイヤモンド焼結体は
再加熱に対して安定しており、非酸化性雰囲気も
しくは真空中では1200〜1300℃の加熱に耐え得
る。従つてこの温度以下の融点を有する非溶媒金
属を主成分とする金属を選び焼結体中の空孔に含
浸せしめれば良い。これに適した金属としては
Ag又はCuを主成分とするロウ材が挙げられる。
例えばAg系のロウ材としてはJIS−Ｚ−3261にあ
るようなAgとCu、Zn、Cd、Ni、Sn等の合金か
らなるロウ材がある。Cuを主成分とするロウ材
としては純銅又はMn、Ｐ、Ag、Cu、Sn、Ni、
Zn、Si等を合金成分として含むものがある。こ
の他にダイヤモンドとの濡れ性を改善するために
Ti、Zr、Cr等を添加すれば含浸が容易になる。
この他にCuとTi、Zrの低融点の金属間化合物を
用いても良い。この中にはTi2Cu、TiCu、
Ti2Cu3、TiCu3等の成分のものがある。
尚Ag、Cuを主成分とするロウ材中で合金成分
としてNi、Mnを含むものはロウ材中の重量で
Ni、Mnが５％未満のものを使用した方が良い。
さてこのようなロウ材をダイヤモンド焼結体の
空孔中に含浸せしめる方法としては真空下で溶媒
金属結合相を除去したダイヤモンド焼結体とロウ
材を接しておき加熱してロウ材を溶解せしめて行
なう真空含浸の方法が適している。ロウ材のダイ
ヤモンドに対する濡れ性が良ければこの方法が適
しているが、濡れ性が悪い場合はロウ材が溶融し
た状態で外部から圧力をかけて強制的に高圧含浸
せしめても良い。
本発明の方法の別の特徴の一つは空孔を有する
ダイヤモンド焼結体を鋼や超硬合金等からなる工
具支持体に接合する場合、この接合ロウ材を焼結
体の空孔中に含浸せめることにより、空孔の封入
と支持体への接合を同時に行なうものである。こ
れにより工具製造の工程を簡略化することができ
る。
本発明による焼結ダイヤモンド工具材はダイヤ
モンドの劣化開始温度が700以上で、使用するロ
ウ材の種類にもよるが最高約1200℃まで加熱して
も劣化しない優れた特性を有するものである。こ
れにより工具として使用した場合工具加工面の温
度上昇に対しても耐えることができ、強度耐摩耗
性共に優れた特性を有している。このため切削工
具や、ドレツサー、ダイスドリルビツト等工具の
製造工程でロウ付け等の高温加熱工程を必要とす
るもの及び工具として使用する場合に温度上昇が
生じるものに適用して優れた性能を発揮するもの
である。
以下実施例に基いて更に具体的に説明する。
実施例 １
平均粒度５μのダイヤモンド粉末と金属Coの
微粉末を体積％でダイヤモンドが90％、Coが10
％となるように混合した。この混合粉末をMo製
の容器に詰めこれを超高圧、高温装置を用いて圧
力55Kb、温度1400℃で20分間保持して焼結し
た。この焼結体の比重を測定したところ4.0であ
つた。王水中に焼結体を浸漬し約70℃に加熱して
20時間処理した後重量を測定したところ酸処理前
に比し約20％の重量減が見られた。ダイヤモンド
とCo粉末の重量比は78.4％と21.6％の割合で混合
しており、焼結体中のCoの大部分が酸処理によ
つて除去されている。この焼結体中のダイヤモン
ドの含有量は体積％で90％であり、空孔が約9.3
体積％残存するものと推定される。
この酸処理后の微細な空孔を有する焼結体を
Cu−５％Tiの組成の銅合金に接して置き、これ
を真空炉中で1200℃に加熱した。取り出した焼結
体から余分の銅合金を削り取り焼結体をダイヤモ
ンド砥石で研削して、更にダイヤモンドパウダー
で研摩した后、組織観察したところ、ダイヤモン
ド粒子相互が接合し、スケルトン構造をなしてお
り、粒子間の微細な空隙には銅合金が均一に含浸
されていた。このものを切断加工して辺長４mm厚
さ２mmの切削加工用チツプを作成した（本発明焼
結体Ａ）。鋼製のバイトシヤンクにクランプして
切削試験を行なつた。Al2O3を主成分とするセラ
ミツクを切削加工して性能を評価した。比較の為
に同一条件で製作したCoを体積で10％含む焼結
体（比較材Ｂ）及びそのCoを王水中で加熱溶解
したもの（比較材Ｃ）で同一形状のチツプを作成
しテストした。
Sintered bodies made by sintering diamond powder under ultra-high pressure have already been put into practical use in some cutting tools and wire drawing dies. Such diamond sintered bodies may include those that do not contain a binder, those that use a metal as a binder, and those that use a non-metal as a binder. Among these, those that do not contain a binder require high pressure and temperature for sintering, and it is considered that it is still difficult to use them industrially. Also, those using non-metal as a binder are inferior in toughness compared to those using metal as a binder. The bonding metal phase of diamond sintered bodies using metal as a bonding material has been proposed to be mainly composed of Co. According to experiments conducted by the inventors, the pressure in the stable range of diamond using Fe, Ni, Co, or their alloys as a binder,
A dense diamond sintered body can be obtained by holding it under temperature conditions for a certain period of time. These metals are used as catalyst metals in diamond synthesis, and diamond dissolves and re-precipitates in these metals in the diamond stability region of high pressure and high temperature, creating bonds between diamond grains and making it strong. It is estimated that the sintered body has a skeleton of diamond particles. The inventors investigated various characteristics of these diamond sintered bodies using iron group metals as a binder, and as a result, it was found that there were major problems in practical use. Diamond sintered bodies made of iron group metals such as Fe, Ni, and Co do not significantly lose their strength when heated to approximately 700℃, and have great wear resistance when used as cutting tools, for example. It is a serious deterioration. When processing a diamond sintered body into a cutting tool, it is necessary to braze it to a steel support. Not only cutting tools but also drill bits,
When applied to products such as dressers and dies, brazing, sintering, and casting methods, which are generally used for natural diamond particles, can be considered as methods for fixing the diamond sintered body to the support. Generally used silver solder metal has a brazing temperature of 700° to 850°C, and in the sintering method, it is heated to a high temperature of 900°C or more, and even in the casting method, it may be heated to an even higher temperature, albeit for a short time. . Stability against heating under normal pressure is an important characteristic that limits the range of applications of sintered bodies. Deterioration in performance is also expected in applications where the temperature rises during use. In order to confirm this point, we conducted the following experiment. A commercially available diamond sintered body having a metal bonding phase containing Co as a component was used and brazed to a steel shank using a silver solder with a low melting point (melting point of approximately 600°C). I processed this to create a cutting tool. Ceramic whose main component is Al 2 O 3 was cut using this cutting tool. cutting speed 30
m/min, depth of cut 0.15 mm, and feed rate 0.02 mm/rotation, the tool flank wear width reached 0.3 mm in 5 minutes in dry cutting without using cutting fluid. On the other hand, when performing wet cutting using water-soluble cutting oil and keeping the other conditions the same, the tool life was dramatically extended, and it was possible to cut for 40 minutes until the flank wear width was 0.3 mm. This difference in life is due to the difference in the degree of temperature rise at the contact surface of the cutting edge of the tool made of diamond sintered body with the workpiece.
In wet cutting, the contact surface temperature was lowered due to the cooling effect of the cutting oil, and deterioration of the diamond sintered body was suppressed, resulting in improved tool life. This kind of thing is not limited to cutting tools, for example, boring tools such as drilling bits and core bits,
This is common to all tool applications where diamond sintered bodies can be applied, such as dies for drawing high-strength wires such as Mo, W, and steel wires, and dressers for forming grindstones. In order to find out the cause of this thermal deterioration of diamond sintered bodies, the inventors investigated commercially available sintered bodies using Co as a binder by heating and holding them in a vacuum furnace for 30 minutes at a temperature ranging from 500°C to 1000°C. However, in those heated to over 800°C, graphite was detected in addition to diamond by X-ray diffraction. On the other hand, when only diamond powder was heated under the same conditions, no graphite was detected.
From this, it is thought that the thermal deterioration phenomenon of the diamond sintered body is due to Co, which is a binding metal in the sintered body, having the effect of promoting reverse transformation of diamond. In the sintering of diamond powder, if a metal that acts as a solvent for diamond under high temperature and high pressure is present as a binder, strong bonding between diamond particles tends to occur due to the phenomenon of diamond dissolution and precipitation. Generally, properties such as strength and wear resistance of a diamond sintered body are greatly influenced by the state of the skeleton formed by the diamond particles. However, as mentioned above, the deterioration of the sintered body due to reheating is also due to the presence of such solvent metals. The inventors have attempted to provide a method for solving this contradictory point with the present invention. First, in manufacturing a diamond sintered body, as disclosed in Japanese Patent Publication No. 39-20483, diamond powder and this solvent metal powder are mixed, and this mixture is heated to form a diamond using an ultra-high pressure and high temperature device. Sintering is carried out under stable pressure and temperature conditions and above the temperature at which a eutectic melt of solvent metal and diamond is formed (see Figure 1). Thereafter, all or most of the solvent metal remaining as a binder phase in this diamond sintered body is removed by a method such as acid dissolution or electrolysis.The content of the binder metal phase in the diamond sintered body is determined by the solvent for the diamond. Although it varies depending on the amount of metal powder mixed in, the particle size of diamond powder, sintering conditions, etc., in the case of the present invention, diamond occupies 70 to 95% by volume in the sintered body. If the diamond content is less than that, the diamond crystals in the sintered body are difficult to bond to each other, and a sintered body having the desired strength and wear resistance cannot be obtained. If only the binder metal phase consisting of the diamond solvent metal is removed in this way, 5 to 30% by volume of pores will naturally remain inside the sintered body. However, the presence of pores is extremely disadvantageous in terms of strength and wear resistance, especially when the sintered body is used as a tool. The pores act as a stress concentration source for the strength of the sintered body, and the strength is significantly reduced. Also, with regard to wear resistance, cutting chips and wear particles are pushed into the pores on the tool surface and become a factor that accelerates wear. The feature of the present invention is to overcome the above-mentioned drawbacks by first removing the binder phase made of solvent metal from the diamond sintered body, and then impregnating the voids with a non-solvent metal that does not react with diamond. . This eliminates the drawbacks caused by the remaining pores as described above. Once the solvent metal has been removed, the diamond sintered body is stable against reheating and can withstand heating of 1200 to 1300°C in a non-oxidizing atmosphere or in a vacuum. Therefore, a metal whose main component is a non-solvent metal having a melting point below this temperature may be selected and impregnated into the pores in the sintered body. The metal suitable for this is
Examples include brazing filler metals containing Ag or Cu as a main component.
For example, as an Ag-based brazing material, there is a brazing material made of an alloy of Ag and Cu, Zn, Cd, Ni, Sn, etc. as specified in JIS-Z-3261. Pure copper, Mn, P, Ag, Cu, Sn, Ni,
Some contain Zn, Si, etc. as alloy components. In addition, to improve wettability with diamond
Addition of Ti, Zr, Cr, etc. makes impregnation easier.
In addition, low melting point intermetallic compounds of Cu, Ti, and Zr may be used. This includes Ti 2 Cu, TiCu,
There are those with components such as Ti 2 Cu 3 and TiCu 3 . In addition, in brazing filler metals whose main components are Ag and Cu, those containing Ni and Mn as alloying ingredients are calculated by weight in the brazing filler metal.
It is better to use a material containing less than 5% Ni and Mn. Now, as a method of impregnating such a brazing material into the pores of a diamond sintered body, the diamond sintered compact from which the solvent-metal binder phase has been removed is brought into contact with the brazing material under vacuum, and then heated to melt the brazing material. A method of vacuum impregnation is suitable. This method is suitable if the brazing material has good wettability with diamond, but if the wettability is poor, pressure may be applied from the outside while the brazing material is molten to force high-pressure impregnation. Another feature of the method of the present invention is that when a diamond sintered body having pores is joined to a tool support made of steel, cemented carbide, etc., this joining brazing material is inserted into the pores of the sintered body. By impregnating it, pores are filled and bonded to the support at the same time. This allows the tool manufacturing process to be simplified. The sintered diamond tool material according to the present invention has a diamond deterioration starting temperature of 700° C. or higher, and has excellent properties such that it does not deteriorate even when heated up to about 1200° C., depending on the type of brazing material used. As a result, when used as a tool, it can withstand temperature rises on the machined surface of the tool, and has excellent properties in terms of strength and wear resistance. For this reason, it exhibits excellent performance when applied to cutting tools, dressers, die drill bits, and other tools that require high-temperature heating processes such as brazing in the tool manufacturing process, and those that cause a temperature rise when used as tools. It is something to do. A more specific explanation will be given below based on Examples. Example 1 Diamond powder with an average particle size of 5μ and fine powder of metal Co were mixed in volume% of 90% diamond and 10% Co.
%. This mixed powder was packed in a Mo container and sintered using an ultra-high pressure, high temperature device at a pressure of 55 Kb and a temperature of 1400°C for 20 minutes. The specific gravity of this sintered body was measured and found to be 4.0. The sintered body is immersed in aqua regia and heated to approximately 70℃.
When the weight was measured after 20 hours of treatment, it was found that the weight had decreased by about 20% compared to before the acid treatment. The weight ratio of diamond and Co powder was 78.4% and 21.6%, and most of the Co in the sintered body was removed by acid treatment. The diamond content in this sintered body is 90% by volume, and the pores are approximately 9.3%.
It is estimated that % by volume remains. After this acid treatment, the sintered body with fine pores is
It was placed in contact with a copper alloy having a composition of Cu-5% Ti and heated to 1200°C in a vacuum furnace. After scraping off the excess copper alloy from the sintered body and grinding the sintered body with a diamond grindstone and further polishing with diamond powder, we observed the structure and found that the diamond particles were bonded to each other and formed a skeleton structure. The fine voids between the particles were uniformly impregnated with copper alloy. This material was cut into chips for cutting with a side length of 4 mm and a thickness of 2 mm (sintered body A of the present invention). A cutting test was conducted by clamping it to a steel bit shank. Ceramic whose main component is Al 2 O 3 was cut and its performance was evaluated. For comparison, chips with the same shape were made and tested using a sintered body containing 10% Co by volume (comparative material B) manufactured under the same conditions and a sintered body containing 10% Co by volume (comparative material C) made by heating and melting the Co in aqua regia (comparative material C). .
【表】
切削油剤は用いず乾式で切削速度60ｍ／分、切
込み0.15mm、送り0.02mm／回転で切削し工具の逃
げ面摩耗巾が0.3mmに達する寿命時間を求めた。
結果は第１表の通りである。
実施例 ２
平均粒度10μのダイヤモンド粉末とカーボニル
Ni粉末とを体積％でダイヤモンドが85％、Niが
15％となるよう混合した。これを実施例１と同様
にして圧力55Kb、温度1450℃で20分間保持して
焼結した。焼結体を塩酸水溶液中で電解して結合
相のNiを溶出せしめ、更に王水中で加熱し残つ
たNiを除去した。この焼結体中のダイヤモンド
含有量は85体積％でNi溶出後の重量変化より、
焼結体中にはNiは0.5体積％以下で残部は空孔で
ある事が推定された。この焼結体を研削加工して
切削加工用のチツプの形状にした。鋼製の支持体
とこのチツプの間に72％Ag−28％Cuの組成を有
する銀ロウ材の板を置き更にこの板TiH2の微粉
末をアルコールに分散させて塗布した。このチツ
プ、ロウ材、支持体を真空炉に入れ850℃まで加
熱した。炉から取出したところダイヤモンド焼結
体部は鋼支持体に強固に接合されており、その側
面を研削加工して観察したところダイヤモンド焼
結体のNiを溶出した後の空孔中に銀ロウが浸入
していた。[Table] Dry cutting was performed without using cutting fluid at a cutting speed of 60 m/min, depth of cut of 0.15 mm, and feed rate of 0.02 mm/rotation to determine the life time until the flank wear width of the tool reached 0.3 mm.
The results are shown in Table 1. Example 2 Diamond powder and carbonyl with an average particle size of 10μ
Diamond is 85% and Ni is 85% by volume with Ni powder.
It was mixed to be 15%. This was sintered in the same manner as in Example 1 at a pressure of 55 Kb and a temperature of 1450°C for 20 minutes. The sintered body was electrolyzed in an aqueous hydrochloric acid solution to elute the Ni in the binder phase, and further heated in aqua regia to remove the remaining Ni. The diamond content in this sintered body is 85% by volume, and from the weight change after Ni elution,
It was estimated that the Ni content in the sintered body was less than 0.5% by volume, with the remainder being pores. This sintered body was ground into the shape of a chip for cutting. A plate of silver brazing material having a composition of 72%Ag-28%Cu was placed between the steel support and this chip, and this plate was further coated with fine powder of TiH 2 dispersed in alcohol. The chip, brazing material, and support were placed in a vacuum furnace and heated to 850°C. When the diamond sintered body was taken out of the furnace, it was found that it was firmly joined to the steel support, and when the side surface was ground and observed, silver solder was found in the pores after Ni had been eluted from the diamond sintered body. It was infiltrating.
第１図は本発明の焼結体の製造条件を説明する
ためのものでダイヤモンドの圧力、温度相図上に
おける熱力学的な安定領域を示す。
FIG. 1 is for explaining the manufacturing conditions of the sintered body of the present invention, and shows the thermodynamically stable region on the pressure and temperature phase diagram of diamond.
Claims (1)
をなすダイヤモンド焼結体であつて、焼結体全体
の70〜95体積％がダイヤモンド結晶よりなり、残
部がCu又はAgを主成分とする金属ロウ材からな
る焼結ダイヤモンド工具材が鋼又は超硬合金製の
工具の支持体に接合されてなることを特徴とする
焼結ダイヤモンド工具。 ２ ダイヤモンド粉末とダイヤモンド合成時に溶
媒となるFe、Ni、Co、Mn、Cr、Ta又はこれら
と他の金属の合金を接触する状態におき、ダイヤ
モンドが安定な温度、圧力範囲内で圧力45Kb以
上、温度1200℃以上でダイヤモンド粉末相互を焼
結せしめてのち、焼結体中に残留する前記金属を
溶解除去し、更に焼結体中に残留した空孔にCu
又はAgを主成分とする金属ロウ材をロウ材の溶
融温度以上で含浸せしめ、鋼または超硬合金製の
工具支持体に接合することを特徴とする焼結ダイ
ヤモンド工具の製造方法。 ３ 特許請求の範囲２項に記載の方法において、
空孔を有するダイヤモンド焼結体を鋼又は超硬合
金からなる工具の支持体に接合する工程におい
て、この接合材としてCu又はAgを主成分とする
ロウ材を用いて該ダイヤモンド焼結体と支持体を
真空炉中で加熱して接合せしめると同時にダイヤ
モンド焼結体の空孔中に該ロウ材を真空含浸せし
めることを特徴とする焼結ダイヤモンド工具の製
造方法。[Scope of Claims] 1. A diamond sintered body having a structure in which diamond crystals are interconnected, wherein 70 to 95% by volume of the entire sintered body is composed of diamond crystals, and the remainder is mainly composed of Cu or Ag. A sintered diamond tool, characterized in that a sintered diamond tool material made of a brazing metal is joined to a tool support made of steel or cemented carbide. 2. Bringing diamond powder into contact with Fe, Ni, Co, Mn, Cr, Ta, or alloys of these and other metals, which will be used as a solvent during diamond synthesis, at a temperature and pressure of 45 Kb or more within a stable temperature and pressure range, After sintering the diamond powders at a temperature of 1200°C or higher, the metal remaining in the sintered body is dissolved and removed, and Cu is added to the pores remaining in the sintered body.
Alternatively, a method for manufacturing a sintered diamond tool, which comprises impregnating the metal brazing material containing Ag as a main component at a temperature higher than the melting temperature of the brazing material, and bonding the tool to a tool support made of steel or cemented carbide. 3. In the method described in claim 2,
In the process of joining a diamond sintered body with holes to a tool support made of steel or cemented carbide, a brazing material mainly composed of Cu or Ag is used as the joining material to bond the diamond sintered body and the support. 1. A method for manufacturing a sintered diamond tool, which comprises heating and joining the diamond sintered bodies in a vacuum furnace, and at the same time vacuum-impregnating the brazing material into the pores of the diamond sintered body.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22729884A JPS60187603A (en) | 1984-10-29 | 1984-10-29 | Sintered diamond tool and its manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22729884A JPS60187603A (en) | 1984-10-29 | 1984-10-29 | Sintered diamond tool and its manufacturing method |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP54036540A Division JPS6012161B2 (en) | 1979-03-27 | 1979-03-27 | Sintered diamond tool material and its manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS60187603A JPS60187603A (en) | 1985-09-25 |
| JPS6140722B2 true JPS6140722B2 (en) | 1986-09-10 |
Family
ID=16858619
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22729884A Granted JPS60187603A (en) | 1984-10-29 | 1984-10-29 | Sintered diamond tool and its manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60187603A (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6155755A (en) * | 1998-03-02 | 2000-12-05 | Sumitomo Electric Industries, Ltd. | Hard sintered body tool |
| JP4045014B2 (en) | 1998-04-28 | 2008-02-13 | 住友電工ハードメタル株式会社 | Polycrystalline diamond tools |
| US7377341B2 (en) | 2005-05-26 | 2008-05-27 | Smith International, Inc. | Thermally stable ultra-hard material compact construction |
| CA2619547C (en) | 2007-02-06 | 2016-05-17 | Smith International, Inc. | Polycrystalline diamond constructions having improved thermal stability |
| US7942219B2 (en) | 2007-03-21 | 2011-05-17 | Smith International, Inc. | Polycrystalline diamond constructions having improved thermal stability |
| US9297211B2 (en) | 2007-12-17 | 2016-03-29 | Smith International, Inc. | Polycrystalline diamond construction with controlled gradient metal content |
| US8083012B2 (en) | 2008-10-03 | 2011-12-27 | Smith International, Inc. | Diamond bonded construction with thermally stable region |
| US8590130B2 (en) | 2009-05-06 | 2013-11-26 | Smith International, Inc. | Cutting elements with re-processed thermally stable polycrystalline diamond cutting layers, bits incorporating the same, and methods of making the same |
| US9194189B2 (en) | 2011-09-19 | 2015-11-24 | Baker Hughes Incorporated | Methods of forming a cutting element for an earth-boring tool, a related cutting element, and an earth-boring tool including such a cutting element |
| CN103395009B (en) * | 2013-07-08 | 2015-07-01 | 中原工学院 | Ceramic hollow sphere multi-layer brazed diamond block and manufacturing method thereof |
| CN117620177A (en) * | 2023-12-22 | 2024-03-01 | 河南工业大学 | Preparation method and product of polycrystalline cubic boron nitride cutting tool |
-
1984
- 1984-10-29 JP JP22729884A patent/JPS60187603A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS60187603A (en) | 1985-09-25 |
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