JP3591858B2 - Carbide insert for aluminum cutting - Google Patents
Carbide insert for aluminum cutting Download PDFInfo
- Publication number
- JP3591858B2 JP3591858B2 JP34666093A JP34666093A JP3591858B2 JP 3591858 B2 JP3591858 B2 JP 3591858B2 JP 34666093 A JP34666093 A JP 34666093A JP 34666093 A JP34666093 A JP 34666093A JP 3591858 B2 JP3591858 B2 JP 3591858B2
- Authority
- JP
- Japan
- Prior art keywords
- aluminum
- cemented carbide
- amount
- cutting
- binder phase
- 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 - Fee Related
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- Cutting Tools, Boring Holders, And Turrets (AREA)
Description
【0001】
【産業上の利用分野】
本願発明は、アルミ切削加工用として優れた特性を発揮する超硬チップに関するものである。
【0002】
【従来の技術】
アルミの切削加工は、特にアルミとチップの溶着が激しいため刃先角度を鋭利にする、チップの表面を鏡面ラップ仕上げをする、摩擦係数の低い表面被覆(TiN、TiCN、ダイヤ、CBNなど)をするなどの対処をしている。しかし、刃先角度を鋭利にすると欠けやすくなり、鏡面ラップは製造コストがかかるとともに曲面のラップが困難である、表面被覆は膜の剥離が頻繁で安定した切削加工が困難であるなどの問題がある。
【0003】
【発明が解決しようとする課題】
このようにアルミの切削加工用超硬チップは近年広範に用いられてきてはいるが、中高温でアルミとの反応が極めて少なく、切削時の刃先にかかる応力集中に充分耐え得る靭性と強度を持った切削加工用超硬チップはなかった。
【0004】
【本発の目的】
本発明は充分な靭性と強度を保ちつつ、中高温でアルミとの反応が極めて少ない超硬材質を創生しアルミ切削加工用超硬チップに供することを目的とする。
【0005】
【課題を解決するための手段】
本発明者らは、中高温におけるアルミと超硬との反応機構を鋭意調査した結果、超硬表面の損傷はアルミと超硬材質の構成要素である金属結合相とが反応していること、金属結合相はCoが一般的であるが、Crを従来になく多量に含んだCo−Cr系を金属結合相とすることでその反応が極端に減少すること、さらにNi、V、TaC、NbCなどを適宜添加することで反応はさらに減少し得ることを見いだした。本願発明は、WCと金属結合相とを含むWC基超硬合金において、該金属結合相はCoとCrを含み、該金属結合相量が合金の4〜25重量%を占め、Crが該金属結合相量の16.7〜36.7%であり、該WCは平均粒径0.2〜7μmで構成されることを特徴とするアルミ切削加工用超硬チップである。
【0006】
【作用】
以下、特許請求の範囲に従ってさらに詳細に説明する。先ず、Crは金属結合相に対して16.7〜36.7重量%含有されることが必要である。16.7%未満では耐アルミ反応性が不十分であり、36.7%を越えるとCo3CrやCo2Crなどの金属間化合物や複炭化物が製造過程で形成され、靭性が低下する。Crの一部をVで置換するとこれも目下理由は不明だがアルミの溶着が減少する。この場合10%未満ではVの効果が明瞭でなく30%を越えるとやや靭性が低下するため10〜30%とした。
【0007】
結合相量は合金の3〜25重量%を占めることが望ましい。3%未満では靭性が低下し応力集中に耐えれなくて破損する確率が高くなる。25%を越えると剛性が低下し、実用に供し得ない。Coの一部をNiに置換すると耐食性と耐酸化性が向上し実用上好ましい。この場合10%未満ではNiの効果が明瞭でなく40%を越えるとやや靭性が低下するため10〜40%とした。
【0008】
WCの平均粒径は0.2〜7μmであることが本発明の主旨に合致する。0.2μm未満では靭性(破壊靭性値K1C)が低下し欠けの確率が高くなる。7μmを越えるとWC炭化物自体が破壊の起点となるためやはり靭性が低下し実用上望ましくない。超硬は一般に1400℃近辺の高温で焼結して製造されるためWCや他の炭化物が金属結合相に溶解するため金属結合相にはW、Ta、Nbなどが必然的に小量含有される。WCの一部を耐火炭化物で置換するとそれぞれの炭化物に応じた効果が得られる。TaCで置換すると中高温での強度が向上し、実用上好ましい。この場合3%未満ではTaCの効果が明瞭でなく10%を越えるとやや靭性が低下するため3〜10%とした。NbCも同じ効果が得られる。この場合3%未満ではNbCの効果が明瞭でなく10%を越えるとやや靭性が低下するため3〜10%とした。
【0009】
【実施例】
WC、Co、Crなどの原料粉末を所定の比に秤量後ボールミルでアルコールを分散剤として用い72時間湿式混合した。混合終了後スプレードライを用いて乾燥造粒を行った。できた造粒粉をプレス成形し適宜処理温度を選定しながら真空焼結を行った。焼結完了後所定の形状に加工し靭性(破壊靭性値K1C)、アルミとの反応性および切削性能をを調査した。組成等を表1〜表3に示す。
尚、表1〜表3には、「Cr比」として、(Cr+V)/(Co+Ni+Cr+V)を示す。
【0010】
【表1】
【0011】
【表2】
【0012】
【表3】
【0013】
アルミとの反応性は鏡面ラップした各超硬試料の上にアルミの円筒状の塊を置き真空中800℃で2時間放置後超硬ラップ面に生じた反応相の厚みで評価した。評価は下記のように4段階とした。
1:反応相の厚みが30μm未満(大いに効果あり)
2:30〜70μm(効果あり)
3:71〜100μm(従来より効果あり)
4:100μmを越えた場合(従来と同じ)
【0014】
切削性能はチップ形状TNGG331(内接円9.525mm、厚み4.76mm、ノーズ0.4mm)を用いて切削速度300mm切り込み2mm送り0.2mm/REV、アルミの旋削加工を行い、加工物の表面状態、切り粉の形状、刃先の溶着状況等から判定した工具寿命で良否を判定した。その結果を表1〜表3に併記する。
【0015】
【発明の効果】
このように本発明の材種はアルミに対する反応性が低くアルミ加工用の切削工具として優れた特性をもつ。[0001]
[Industrial applications]
The present gun invention relates to hard tip which exhibits excellent characteristics as for aluminum machining.
[0002]
[Prior art]
In aluminum cutting, the edge of the chip is sharpened due to severe welding of the aluminum and the chip, and the surface of the chip is mirror-finished, and the surface is coated with a low coefficient of friction (TiN, TiCN, diamond, CBN, etc.). And so on. However, when the edge angle is sharpened, chipping tends to occur, and mirror-surface wraps have problems such as high manufacturing cost and difficulty in wrapping curved surfaces, and surface coating, in which film peeling is frequent and stable cutting is difficult. .
[0003]
[Problems to be solved by the invention]
As described above, carbide tips for cutting aluminum have been widely used in recent years.However, there is very little reaction with aluminum at medium and high temperatures, and toughness and strength sufficient to withstand stress concentration applied to the cutting edge during cutting. There was no carbide insert for cutting.
[0004]
[Purpose of the invention]
It is an object of the present invention to create a cemented carbide material which has very little reaction with aluminum at medium to high temperatures while maintaining sufficient toughness and strength, and to provide the cemented carbide chip for aluminum cutting.
[0005]
[Means for Solving the Problems]
The present inventors have conducted intensive studies on the reaction mechanism between aluminum and cemented carbide at medium and high temperatures, and found that damage to the cemented carbide surface is a reaction between aluminum and the metal bonding phase that is a component of the cemented carbide material. The metal binding phase is generally Co, but the reaction is extremely reduced by using a Co—Cr system containing a large amount of Cr, which is unprecedented, as well as Ni, V, TaC, NbC. It has been found that the reaction can be further reduced by adding such as appropriate. The present invention relates to a WC-based cemented carbide containing WC and a metal binder phase , wherein the metal binder phase contains Co and Cr , the amount of the metal binder phase accounts for 4 to 25% by weight of the alloy, and The amount of the binder phase is 16.7 to 36.7% , and the WC is a cemented carbide chip for aluminum cutting characterized by having an average particle size of 0.2 to 7 μm.
[0006]
[Action]
Hereinafter, the present invention will be described in more detail according to the claims. First, it is necessary that Cr be contained in an amount of 16.7 to 36.7 % by weight based on the metal binder phase. If it is less than 16.7%, the reactivity to aluminum is insufficient, and if it exceeds 36.7% , intermetallic compounds such as Co 3 Cr and Co 2 Cr and double carbides are formed in the production process, and the toughness is reduced. If a part of Cr is replaced by V, the reason for this is still unknown, but the welding of aluminum is reduced. In this case, if it is less than 10%, the effect of V is not clear, and if it exceeds 30%, the toughness is slightly lowered.
[0007]
Desirably, the binder phase accounts for 3 to 25% by weight of the alloy. If it is less than 3%, the toughness is reduced and the probability of breakage due to inability to withstand stress concentration increases. If it exceeds 25%, the rigidity is reduced, and it cannot be put to practical use. Substituting a part of Co for Ni improves corrosion resistance and oxidation resistance, which is practically preferable. In this case, if it is less than 10%, the effect of Ni is not clear, and if it exceeds 40%, the toughness is slightly lowered.
[0008]
The average particle size of WC is 0.2 to 7 μm, which is consistent with the gist of the present invention. If it is less than 0.2 μm, the toughness (fracture toughness value K 1C ) decreases and the probability of chipping increases. If it exceeds 7 μm, the WC carbide itself becomes a starting point of fracture, so that the toughness is also lowered, which is not desirable for practical use. Carbide is generally manufactured by sintering at a high temperature of around 1400 ° C., so that WC and other carbides dissolve in the metal binder phase, so that the metal binder phase necessarily contains small amounts of W, Ta, Nb, and the like. You. When a part of the WC is replaced with a refractory carbide, an effect corresponding to each carbide can be obtained. Substitution with TaC improves the strength at medium and high temperatures and is practically preferable. In this case, if the content is less than 3%, the effect of TaC is not clear, and if it exceeds 10%, the toughness is slightly lowered. NbC has the same effect. In this case, if it is less than 3%, the effect of NbC is not clear, and if it exceeds 10%, the toughness is slightly lowered.
[0009]
【Example】
Raw material powders such as WC, Co, and Cr were weighed at a predetermined ratio, and were wet-mixed for 72 hours in a ball mill using alcohol as a dispersant. After the completion of mixing, dry granulation was performed using spray drying. The resulting granulated powder was press-formed and vacuum-sintered while appropriately selecting a processing temperature. After sintering was completed, it was processed into a predetermined shape, and its toughness (fracture toughness value K 1C ), reactivity with aluminum, and cutting performance were investigated. Tables 1 to 3 show the composition and the like.
Tables 1 to 3 show (Cr + V) / (Co + Ni + Cr + V) as the “Cr ratio”.
[0010]
[Table 1]
[0011]
[Table 2]
[0012]
[Table 3]
[0013]
The reactivity with aluminum was evaluated by placing a cylindrical lump of aluminum on each mirror-wrapped cemented carbide sample, leaving it at 800 ° C. in a vacuum for 2 hours, and then evaluating the thickness of the reaction phase formed on the cemented carbide wrap surface. The evaluation was made in four stages as follows.
1: The thickness of the reaction phase is less than 30 μm (very effective)
2: 30 to 70 µm (with effect)
3: 71 to 100 μm (more effective than before)
4: When exceeding 100 μm (same as before)
[0014]
The cutting performance is as follows: Using a tip shape TNGG331 (inscribed circle 9.525 mm, thickness 4.76 mm, nose 0.4 mm), cutting speed 300 mm, cutting depth 2 mm, feed 0.2 mm / REV, aluminum turning, and the surface of the workpiece Pass / fail was determined based on the tool life determined from the state, the shape of the cutting powder, the welding state of the cutting edge, and the like. The results are also shown in Tables 1 to 3 .
[0015]
【The invention's effect】
As described above, the grade of the present invention has low reactivity to aluminum and has excellent characteristics as a cutting tool for aluminum processing.
Claims (5)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP34666093A JP3591858B2 (en) | 1993-12-22 | 1993-12-22 | Carbide insert for aluminum cutting |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP34666093A JP3591858B2 (en) | 1993-12-22 | 1993-12-22 | Carbide insert for aluminum cutting |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH07178605A JPH07178605A (en) | 1995-07-18 |
JP3591858B2 true JP3591858B2 (en) | 2004-11-24 |
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Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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JP34666093A Expired - Fee Related JP3591858B2 (en) | 1993-12-22 | 1993-12-22 | Carbide insert for aluminum cutting |
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JP (1) | JP3591858B2 (en) |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2003073766A (en) * | 2001-08-28 | 2003-03-12 | Kyocera Corp | High-hardness sintered alloy and aluminum wrought member using it |
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1993
- 1993-12-22 JP JP34666093A patent/JP3591858B2/en not_active Expired - Fee Related
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JPH07178605A (en) | 1995-07-18 |
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