JPH0394062A - Diamond-coated sintered hard alloy - Google Patents
Diamond-coated sintered hard alloyInfo
- Publication number
- JPH0394062A JPH0394062A JP1232218A JP23221889A JPH0394062A JP H0394062 A JPH0394062 A JP H0394062A JP 1232218 A JP1232218 A JP 1232218A JP 23221889 A JP23221889 A JP 23221889A JP H0394062 A JPH0394062 A JP H0394062A
- Authority
- JP
- Japan
- Prior art keywords
- diamond
- alloy
- amount
- binding phase
- sintered
- 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.)
- Granted
Links
- 229910003460 diamond Inorganic materials 0.000 title claims abstract description 35
- 239000010432 diamond Substances 0.000 title claims abstract description 35
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 26
- 239000000956 alloy Substances 0.000 title claims abstract description 26
- 239000011230 binding agent Substances 0.000 claims description 13
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- -1 iron group metals Chemical class 0.000 claims 1
- 230000015572 biosynthetic process Effects 0.000 abstract description 6
- 238000003786 synthesis reaction Methods 0.000 abstract description 6
- 230000003247 decreasing effect Effects 0.000 abstract description 2
- 238000005245 sintering Methods 0.000 abstract description 2
- 239000000853 adhesive Substances 0.000 abstract 2
- 230000001070 adhesive effect Effects 0.000 abstract 2
- 238000010521 absorption reaction Methods 0.000 abstract 1
- 238000005229 chemical vapour deposition Methods 0.000 abstract 1
- 230000006866 deterioration Effects 0.000 abstract 1
- 230000002542 deteriorative effect Effects 0.000 abstract 1
- 230000005764 inhibitory process Effects 0.000 abstract 1
- 239000002994 raw material Substances 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 11
- 238000005520 cutting process Methods 0.000 description 7
- 239000010408 film Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000000034 method Methods 0.000 description 6
- 238000000576 coating method Methods 0.000 description 5
- 239000011248 coating agent Substances 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910000531 Co alloy Inorganic materials 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000002230 thermal chemical vapour deposition Methods 0.000 description 3
- 239000012808 vapor phase Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 229930195733 hydrocarbon Natural products 0.000 description 1
- 150000002430 hydrocarbons Chemical class 0.000 description 1
- 229910010272 inorganic material Inorganic materials 0.000 description 1
- 239000011147 inorganic material Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000005268 plasma chemical vapour deposition Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000001308 synthesis method Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】
く産業上の利用分野〉
この発明は、例えば切削工具や耐摩部品等に好適な耐摩
耗性の極めて優れたダイヤモンド被覆超硬合金部品に関
するものである。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to a diamond-coated cemented carbide component having extremely excellent wear resistance and suitable for use in, for example, cutting tools and wear-resistant parts.
〈従来の技術〉
ダイヤモンドの合成において超高圧・高温を用いずに、
炭化水素を分解して気相から母材表面にダイヤモンドを
合成させ被覆する、ダイヤモンドの気相合成技術が１９
８１年に無機材質研究所によって開発されて以来、種々
の分野でダイヤモンド気相合成技術の応用が考えられて
いる。<Conventional technology> Diamond synthesis without using ultra-high pressure and high temperature.
Diamond vapor phase synthesis technology that decomposes hydrocarbons and synthesizes and coats diamond onto the surface of the base material from the gas phase is 19
Since it was developed by the Inorganic Materials Research Institute in 1981, applications of diamond vapor phase synthesis technology have been considered in various fields.
ダイヤモンドは特に硬い物質であり、又、化学的にも極
めて安定で、酸素及び鉄を除き他の物質と殆ど反応しな
いという際立った特徴を有するため、切削工具材料とし
て極めて好ましいことは言うまでもない。そのため、超
硬合金等の従来工具の表面にダイヤモンドの薄膜を厚さ
５〜ｌＯμｍ程度に被覆したダイヤモンド被覆超硬合金
が盛んに研究されている。It goes without saying that diamond is a particularly hard material, and has the distinguishing feature of being extremely chemically stable and hardly reacting with other substances except oxygen and iron, making it extremely desirable as a cutting tool material. Therefore, diamond-coated cemented carbide, in which the surface of a conventional tool such as cemented carbide is coated with a thin film of diamond to a thickness of about 5 to 10 μm, is being actively researched.
く発明が解決しようとする課題〉
気相合成法で超硬合金表面にダイヤモンド被覆を形成し
た場合、母材との接着性が十分でなく、工具性能として
は実用の域に達していないというのが現状である。Problems to be Solved by the Invention When a diamond coating is formed on the surface of a cemented carbide using a vapor phase synthesis method, the adhesion to the base material is insufficient and the tool performance has not reached the level of practical use. is the current situation.
特に、ダイヤモンド焼結体工具の代替用として需要の高
いＡｌｌ − ＳＬ合金に対しては、極めて低い寿命し
か示さない。In particular, the All-SL alloy, which is in high demand as a substitute for diamond sintered tools, shows an extremely short service life.
これは、ダイヤモンド被覆中に合金表面のＣＯが合金中
より炭素を吸収してダイヤモンド合成を抑制したり、あ
るいは生成したダイヤモンドをグラファイトに変態させ
る等してダイヤモンドの密着性を低下させているものと
考えられる。This is because CO on the alloy surface absorbs carbon from the alloy during diamond coating, suppressing diamond synthesis, or transforming the formed diamond into graphite, reducing the adhesion of the diamond. Conceivable.
このため、従来は靭性を若干犠牲にして合金中のＧｏ量
を少なくさせて対応している。Conventionally, this has been dealt with by reducing the amount of Go in the alloy at the expense of some toughness.
しかしながら、上記のＡＩ−Ｓｉ合金切削にはかなりの
靭性が要求され、Ｇｏ量を低下させて密着性を向上させ
たダイヤモンド被覆超硬合金では欠損しやすく、本来の
目的が達成されないのである。However, considerable toughness is required for cutting the above-mentioned AI-Si alloy, and diamond-coated cemented carbide, which has improved adhesion by reducing the amount of Go, is prone to chipping and cannot achieve its original purpose.
〈課題を解決するための手段〉
この発明は上記の問題点を解決すべく検討の結果、得ら
れたものであって、気相合成技術によりダイヤモンドの
薄膜な超硬合金母材に被覆してなる超硬合金において、
該超硬合金の表面から１００μｍまでの間の結合相を該
超硬合金内部の結合相に比較して減少させ、超硬合金表
面から５〜１００μｍの間に存在する結合相富化層の結
合相量が合金内部の結合相量に対して１．２〜５倍に富
化されてなり、かかる合金表面にダイヤモンド膜を被覆
させたダイヤモンド被覆超硬合金を提供するものである
。<Means for Solving the Problems> The present invention was obtained as a result of studies to solve the above-mentioned problems. In the cemented carbide,
Reduce the binder phase within 100 μm from the surface of the cemented carbide compared to the binder phase inside the cemented carbide, and bond the binder phase enriched layer existing between 5 and 100 μm from the surface of the cemented carbide. The present invention provides a diamond-coated cemented carbide in which the phase amount is enriched 1.2 to 5 times as much as the binder phase amount inside the alloy, and the surface of the alloy is coated with a diamond film.
〈作用〉
この発明においては、■ 超硬合金表面から１００ｌｌ
ｍの間のＧｏ等の結合相量が減少しているため、ダイヤ
モンドとの密着性が大幅に向上する。<Function> In this invention, ■ 100 liters from the cemented carbide surface
Since the amount of the binder phase such as Go between m is reduced, the adhesion with diamond is significantly improved.
このＧｏ等の結合相の減少が超硬合金表面から１００ｌ
ｌｍ以上におよぶと合金強度の大幅な低下が生じてくる
ので好ましくない。This reduction of the binder phase such as Go is 100L from the cemented carbide surface.
If it exceeds lm, the alloy strength will be significantly reduced, which is not preferable.
■ 超硬合金表面部のＣｏ結合相量の減少による強度の
低下は、表面から５〜１００ １ｍの間に存在する結合
相富化層で補うことができる。(2) The decrease in strength due to a decrease in the amount of Co binder phase on the surface of the cemented carbide can be compensated for by a binder phase enriched layer existing between 5 and 100 m from the surface.
５ ｇｍ以内であると、ダイヤモンド生成時にダイヤモ
ンドの合成を抑制したり、グラファイトに変態させるこ
とがあり、好ましくない。If it is less than 5 gm, it may inhibit the synthesis of diamond during diamond production or transform it into graphite, which is not preferable.
また１００μｍ以上であると合金強度の低下抑制に効果
がない。Ｃｏの富化量は１．２倍以下では抑制効果がな
く、５倍を越えると耐摩耗性を低下させ好ましくない。Moreover, if it is 100 μm or more, it is not effective in suppressing a decrease in alloy strength. If the enrichment amount of Co is 1.2 times or less, there is no suppressing effect, and if it exceeds 5 times, the wear resistance is decreased, which is not preferable.
この発明の超硬合金を得る手段としては、１つは結合相
量の異なる圧１接体をラミネート構造としてプレス、成
形、焼結することによって達成できる。または同一組成
の完粉を液相または固相下で脱炭処理や浸炭処置を繰返
して達成させることができる。One method for obtaining the cemented carbide of the present invention can be achieved by pressing, molding, and sintering a laminated structure of pressed bodies having different binder phase amounts. Alternatively, finished powder having the same composition can be repeatedly subjected to decarburization treatment or carburization treatment in a liquid phase or solid phase.
ダイヤモンド被覆の方法としては、例えば熱ＣＶＤ法、
プラズマＣｖＤ法、ＥＡＣＶＤ法、アークプラズマＣＶ
Ｄ法等が知られている。例えば熱ＣＶＤ法によれば、Ｈ
２とＣＩ．の混合ガス（ＣＨ４濃度が０．１〜５容積％
程度）を２０００℃以上で加熱したタングステン等の金
属フィラメントにて予熱した後、７００〜１０００℃に
加熱した基材表面上で混合ガスを分解してダイヤモンド
を析出させることができる。Examples of diamond coating methods include thermal CVD method,
Plasma CvD method, EACVD method, arc plasma CV
D method etc. are known. For example, according to the thermal CVD method, H
2 and CI. mixed gas (CH4 concentration is 0.1 to 5% by volume)
After preheating a metal filament of tungsten or the like heated to 2000°C or higher, the mixed gas can be decomposed on the surface of the base material heated to 700 to 1000°C to precipitate diamond.
ダイヤモンド被覆の厚さは０．１μｍ以上２０ｐｍ以下
が好ましい。２０μｍを越えると膜中の熱応力により膜
が剥離するので好ましくなく、０．１ｇｍ未満では被覆
の効果が認められない。The thickness of the diamond coating is preferably 0.1 μm or more and 20 pm or less. If it exceeds 20 μm, the film will peel off due to thermal stress in the film, which is undesirable, and if it is less than 0.1 gm, no coating effect will be observed.
〈実施例〉 以下、この発明を実施例により詳細に説明する。<Example> Hereinafter, this invention will be explained in detail with reference to Examples.
実施例１
ｗｃ−ｉｏ％Ｃｏ合金完粉を用いてＩＳＯ ＳＰＧＮ
１２０３０８の形状にプレスした後、１３５０℃で０．
Ｉ Ｔｏｒｒの真空雰囲気中で３０分間保持した。Example 1 ISO SPGN using wc-io%Co alloy complete powder
After pressing into the shape of 120308, it was heated to 1350°C and 0.
It was held in a vacuum atmosphere of I Torr for 30 minutes.
次いで ５℃／ｍｉｎ．（４）， ２℃／ｍｉｎ．＠，
０．５℃／ ｍ ｉ ｎ ． （Ｑの３種の冷却速度で
１２５０℃まで５ＴｏｒｒのＣＨ４とＨ２の混合ガス雰
囲気中で冷却した。Then 5°C/min. (4), 2°C/min. @,
0.5℃/min. (It was cooled to 1250° C. at three cooling rates (Q) in a mixed gas atmosphere of CH4 and H2 at 5 Torr.
次に、上記で得た３種の合金を１４００℃、０． ｌＴ
ｏｒｒのＣＨ４の微浸炭性雰囲気中で２時間保持した。Next, the three types of alloys obtained above were heated at 1400°C and 0.5°C. lT
It was held for 2 hours in a slightly carburizing atmosphere of CH4 of orr.
かくして得た合金のＧｏ分布をＸＭＡで分析したところ
、第１図に示す結果が得られた。When the Go distribution of the thus obtained alloy was analyzed by XMA, the results shown in FIG. 1 were obtained.
又、比較として通常のｗｃ−ｉｏ％Ｃｏ合金を用いて表
面に一般的な熱ＣＶＤ法でダイヤモンドを５μｍ被覆し
た。この表面にロックウエル圧子を６０ｋｇｆで１０秒
間圧入し、密着性を評価したところ、通常の合金は圧子
周辺で膜剥離が生じていたが、この発明の合金は膜剥離
は殆ど生じていなかった。For comparison, a normal wc-io%Co alloy was used and its surface was coated with 5 μm of diamond by a general thermal CVD method. A Rockwell indenter was injected into this surface at 60 kgf for 10 seconds and the adhesion was evaluated. In the case of ordinary alloys, film peeling occurred around the indenter, but in the case of the alloy of the present invention, almost no film peeling occurred.
実施例２
実施例１で作製した（４）、（ロ）、０の３種の合金及
び通常の合金（５％ＣｏとｌＯ％Ｃｏ）にダイヤモンド
膜を被覆したものを用いて下記の条件で切削テストを行
なった。Example 2 Three types of alloys (4), (b), and 0 prepared in Example 1 and ordinary alloys (5%Co and 1O%Co) coated with a diamond film were used under the following conditions. A cutting test was conducted.
切削条件
被削材 ｕ − ｉｇ％Ｓｉ
切削速度 ２００ｍ／ｍｉｎ
切込み ０．５ｍｍ
送り量 ０．１ｍｍ／ｒｅｖ
切削時間 １０分
この結果、囚，＠，０のｖ８摩耗量は０． ２６ｍｍ，
０． ４９ｍｍ、０．２４ｍｍであり、一方、通常の合
金では５％および１０％Ｃｏ合金は１分切削後、摩耗量
が０． ３０ｍｍを越して寿命と認められた。Cutting conditions Work material u - ig%Si Cutting speed 200m/min Depth of cut 0.5mm Feed rate 0.1mm/rev Cutting time 10 minutes As a result, the v8 wear amount of @, 0 is 0. 26mm,
0. 49 mm and 0.24 mm, while the normal alloys, 5% and 10% Co alloys, have a wear amount of 0.0.5 mm after 1 minute of cutting. When the length exceeded 30 mm, it was recognized that the service life had expired.
図面はこの発明で作威した超硬合金の表面からの距離と
ＣＯ分布の関係を示す線図である。The drawing is a diagram showing the relationship between the distance from the surface of the cemented carbide used in this invention and the CO distribution.
Claims (2)
相とした超硬合金において、該超硬合金の表面から１０
０μｍまでの間の結合相量を該超硬合金内部の結合相量
に比較して減少させるとともに該超硬合金表面にダイヤ
モンド膜を被覆させたことを特徴とするダイヤモンド被
覆超硬合金。(1) In a cemented carbide with a binder phase of WC and one or more iron group metals, the surface of the cemented carbide is
1. A diamond-coated cemented carbide, characterized in that the amount of the bonding phase between 0 μm and 0 μm is reduced compared to the amount of the bonding phase inside the cemented carbide, and the surface of the cemented carbide is coated with a diamond film.
する結合相富化層の結合相量が合金内部の結合相量に対
して１．２〜５倍に富化されていることを特徴とする請
求項（１）記載のダイヤモンド被覆超硬合金。(2) The amount of binder phase in the binder phase enriched layer existing between 5 and 100 μm from the surface of the cemented carbide is 1.2 to 5 times the amount of binder phase inside the alloy. A diamond-coated cemented carbide according to claim (1).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1232218A JP2539922B2 (en) | 1989-09-06 | 1989-09-06 | Diamond coated cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1232218A JP2539922B2 (en) | 1989-09-06 | 1989-09-06 | Diamond coated cemented carbide |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0394062A true JPH0394062A (en) | 1991-04-18 |
| JP2539922B2 JP2539922B2 (en) | 1996-10-02 |
Family
ID=16935835
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1232218A Expired - Lifetime JP2539922B2 (en) | 1989-09-06 | 1989-09-06 | Diamond coated cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2539922B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1995012009A1 (en) * | 1993-10-29 | 1995-05-04 | Balzers Aktiengesellschaft | Coated body, its method of production and its use |
| JPH07238483A (en) * | 1994-02-23 | 1995-09-12 | Osaka Diamond Ind Co Ltd | Guide for strand |
| US6998173B2 (en) * | 2000-03-24 | 2006-02-14 | Kennametal Inc. | Cemented carbide tool and method of making |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6195068B2 (en) * | 2013-02-25 | 2017-09-13 | 三菱マテリアル株式会社 | Diamond coated cemented carbide cutting tool with improved cutting edge strength |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6267174A (en) * | 1985-09-19 | 1987-03-26 | Sumitomo Electric Ind Ltd | Production of hard carbon film coated sintered hard alloy |
| JPS63100182A (en) * | 1986-04-24 | 1988-05-02 | Mitsubishi Metal Corp | Cutting tool tip made of diamond-coated tungsten carbide-based sintered hard alloy |
-
1989
- 1989-09-06 JP JP1232218A patent/JP2539922B2/en not_active Expired - Lifetime
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6267174A (en) * | 1985-09-19 | 1987-03-26 | Sumitomo Electric Ind Ltd | Production of hard carbon film coated sintered hard alloy |
| JPS63100182A (en) * | 1986-04-24 | 1988-05-02 | Mitsubishi Metal Corp | Cutting tool tip made of diamond-coated tungsten carbide-based sintered hard alloy |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1995012009A1 (en) * | 1993-10-29 | 1995-05-04 | Balzers Aktiengesellschaft | Coated body, its method of production and its use |
| JPH07238483A (en) * | 1994-02-23 | 1995-09-12 | Osaka Diamond Ind Co Ltd | Guide for strand |
| US6998173B2 (en) * | 2000-03-24 | 2006-02-14 | Kennametal Inc. | Cemented carbide tool and method of making |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2539922B2 (en) | 1996-10-02 |
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