JPH0645880B2 - Method for producing surface-coated cemented carbide - Google Patents
Method for producing surface-coated cemented carbideInfo
- Publication number
- JPH0645880B2 JPH0645880B2 JP61248087A JP24808786A JPH0645880B2 JP H0645880 B2 JPH0645880 B2 JP H0645880B2 JP 61248087 A JP61248087 A JP 61248087A JP 24808786 A JP24808786 A JP 24808786A JP H0645880 B2 JPH0645880 B2 JP H0645880B2
- Authority
- JP
- Japan
- Prior art keywords
- cemented carbide
- coating
- layer
- coated
- carbide
- 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 - Lifetime
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 4
- 239000010410 layer Substances 0.000 claims description 25
- 229910052751 metal Inorganic materials 0.000 claims description 14
- 239000002184 metal Substances 0.000 claims description 14
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
- 239000000758 substrate Substances 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 9
- 239000010936 titanium Substances 0.000 claims description 9
- 150000001247 metal acetylides Chemical class 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- 239000011247 coating layer Substances 0.000 claims description 7
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- -1 carbonitrides Chemical class 0.000 claims description 6
- 150000001875 compounds Chemical class 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims 1
- 238000000576 coating method Methods 0.000 description 19
- 239000011248 coating agent Substances 0.000 description 18
- 238000005520 cutting process Methods 0.000 description 16
- 239000000956 alloy Substances 0.000 description 15
- 229910045601 alloy Inorganic materials 0.000 description 15
- 238000000034 method Methods 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 230000000694 effects Effects 0.000 description 7
- 238000005229 chemical vapour deposition Methods 0.000 description 6
- 150000004767 nitrides Chemical class 0.000 description 6
- 239000000843 powder Substances 0.000 description 6
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 239000001257 hydrogen Substances 0.000 description 4
- 229910052739 hydrogen Inorganic materials 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 239000011230 binding agent Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- XJDNKRIXUMDJCW-UHFFFAOYSA-J titanium tetrachloride Chemical compound Cl[Ti](Cl)(Cl)Cl XJDNKRIXUMDJCW-UHFFFAOYSA-J 0.000 description 3
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000010408 film Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910003468 tantalcarbide Inorganic materials 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Chemical Vapour Deposition (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は切削工具ならびに耐摩耗性部品として工業上有
用な耐摩耗性を著しく向上させた表面被覆した超硬合金
に関するものである。The present invention relates to a surface-coated cemented carbide with significantly improved wear resistance which is industrially useful as a cutting tool and a wear resistant part.
超硬合金は４ａ，５ａ，６ａ属の炭化物ならびに鉄族金
属が主体の焼結材料であり、炭化物微粒子を鉄族金属中
（以下結合金属という。）に分散させ、炭化物の硬さと
結合金属の靭性を兼ね備えた性質を有する。結合金属量
が多くなると靭性は増加するが、耐摩耗性が減少するの
で、種々の組成を有する超硬合金が用途に応じて使用さ
れている。一方、超硬合金からなる基体より耐摩耗性の
高い表面層を形成させ、靭性の低下を制限しながら、耐
摩耗性を向上させる技術が進歩し、種々の表面被覆した
工具材料が実用化されている。更に表面被覆する以前に
基体より耐摩耗性の向上，耐衝撃性の向上を計るために
超硬合金の表面層を硬化及び／又は軟化した層を設けて
いる。以下に従来から製造されている表面被覆された超
硬合金の表面層を硬化及び／又は軟化した層の製造方法
と特徴を列記する。Cemented carbide is a sintered material mainly composed of carbides of the 4a, 5a, and 6a groups and iron group metals, and fine carbide particles are dispersed in an iron group metal (hereinafter referred to as "bond metal") to obtain the hardness of the carbide and the bond metal. It has the property of having toughness. Although the toughness increases as the amount of the binding metal increases, the wear resistance decreases, so that cemented carbides having various compositions are used depending on the application. On the other hand, the technology for improving wear resistance while forming a surface layer having higher wear resistance than a base made of cemented carbide and limiting deterioration of toughness has advanced, and various surface coated tool materials have been put into practical use. ing. Further, before the surface coating, a layer obtained by hardening and / or softening the surface layer of the cemented carbide is provided in order to improve the wear resistance and the impact resistance of the substrate. The following is a list of manufacturing methods and characteristics of a layer obtained by hardening and / or softening the surface layer of the surface-coated cemented carbide that has been conventionally manufactured.
（１）積層合金を形成する方法 表面が耐摩耗性に優れた超硬合金からなり、内部が靭性
に優れた超硬合金からなる。２種類の合金粉末から製造
される。積層合金は製造上に困難さがあるだけでなく、
耐摩耗性の向上が少ないので、今日ではほとんど製造さ
れていない。(1) Method of forming laminated alloy The surface is made of cemented carbide having excellent wear resistance, and the inside is made of cemented carbide having excellent toughness. Manufactured from two alloy powders. Not only are laminated alloys difficult to manufacture,
It is rarely manufactured today because of its little improvement in wear resistance.
（２）窒化物添加による方法 ４ａ族の窒化物を微量添加することにより表面に脱β層
を生成し、（表面から数十ミクロンにわたりβ相を含ま
ない層）被覆後の皮膜からのクラック伝播性を向上させ
る。(2) Method by addition of nitride A small amount of Group 4a nitride is added to form a de-β layer on the surface, and crack propagation from the film after coating (layer not containing β phase over several tens of microns from the surface) Improve sex.
（３）結合金属を富化させる方法 最も靭性に富む結合金属を富化し、表面被覆合金として
の耐衝撃性を向上させる方法。(3) Method for Enriching Bond Metal A method for enriching the bond metal having the highest toughness to improve the impact resistance as a surface coating alloy.
これら目的に応じて処理した超硬合金の表面に化学蒸着
法により炭化物，窒化物の被覆処理をＴｉ金属の塩化物
蒸気を水素雰囲気中でメタンガス又は窒素と反応させ、
９００℃〜１１００℃に加熱された超硬合金上にＴｉ炭
化物あるいは窒化物の薄膜を形成させる方法で製造され
る。The surface of the cemented carbide treated according to these purposes is coated with carbides and nitrides by chemical vapor deposition to react chloride vapor of Ti metal with methane gas or nitrogen in a hydrogen atmosphere,
It is manufactured by a method of forming a Ti carbide or nitride thin film on a cemented carbide that is heated to 900 ° C to 1100 ° C.
現在市販されている被覆合金には炭窒化チタン被覆合金
および窒化チタン被覆合金，Ａｌ2Ｏ3被覆合金，及びそ
れらの複層被覆合金等があり、いずれも耐摩耗性が高
く、２〜２０ミクロンの皮膜により超硬合金の耐摩耗製
は３〜１０倍増大する。The coating alloys currently on the market include titanium carbonitride coating alloys, titanium nitride coating alloys, Al 2 O 3 coating alloys, and their multilayer coating alloys, all of which have high wear resistance and have a thickness of 2 to 20 μm. The wear resistance of cemented carbide is increased by 3 to 10 times by the coating of.
現在市販されている表面処理した被覆合金の大部分は炭
化タングステン，コバルト，炭化チタン，炭化タンタル
を主成分とする切削用超硬合金の表面に炭化物，窒化物
を被覆したものであり、鋳鉄，鋼の切削に広く使用され
ているが、鋼の切削時にしばしば欠損を示し、被覆層の
優れた耐摩耗性が発揮できないことがある。その原因を
鋼切削の磨耗進行から観察すると、欠損あるいは微小カ
ケによって被覆層の１部が消失した後、消失部分から摩
耗が急速に進行するために、刃先が均一に摩耗しないで
局部的に摩耗する現象が見られる。又、工具刃先に高熱
高圧がかかると、超硬合金基体が軟化し、靭性変化する
ために被覆層の大摩耗性が十分に発揮できない場合があ
る。Most of the surface-treated coated alloys currently on the market are carbides and nitrides coated on the surface of a cemented carbide for cutting, which is mainly composed of tungsten carbide, cobalt, titanium carbide, and tantalum carbide. It is widely used for cutting steel, but it often shows defects when cutting steel, and it may not be possible to exhibit the excellent wear resistance of the coating layer. When observing the cause from the progress of wear of steel cutting, after a part of the coating layer disappears due to chipping or minute chipping, the wear progresses rapidly from the disappearing part, so the cutting edge does not wear uniformly and wears locally. You can see the phenomenon. Further, when the tool cutting edge is subjected to high heat and pressure, the cemented carbide base material is softened and the toughness is changed, so that the large wear resistance of the coating layer may not be sufficiently exhibited.
本発明は、新しい現象の発見に基ずいた表面処理に超硬
合金に関するもので、従来の被覆超硬合金の性能上の問
題点を一挙に解決し、より耐摩耗性と汎用性を備えた工
具材料を提供するものである。The present invention relates to a cemented carbide for surface treatment based on the discovery of a new phenomenon. It solves all the performance problems of the conventional coated cemented carbide, and has more wear resistance and versatility. It provides a tool material.
本発明は４ａ，５ａ，６ａ族の炭化物，炭窒化物及び鉄
族金属からなる超硬合金の表面が、基体より軟質の厚さ
２〜４０ミクロンの中間層よりなる超硬合金において、
被覆層が四塩化チタ−水素有機ＣＮ化合物及び／又は窒
素混合ガス中で加熱し、７００℃〜９００℃で超硬合金
に炭窒化チタン及び／又は窒化チタンを被覆したことを
特徴とする表面被覆超硬合金に関するものである。The present invention is directed to a cemented carbide in which the surface of the cemented carbide of 4a, 5a, 6a group carbides, carbonitrides, and iron group metals is an intermediate layer having a thickness of 2 to 40 microns, which is softer than the base,
A surface coating characterized in that the coating layer is heated in a titanium tetrachloride-hydrogen organic CN compound and / or a nitrogen mixed gas to coat the cemented carbide with titanium carbonitride and / or titanium nitride at 700 ° C to 900 ° C. It relates to cemented carbide.
基体より軟質な超硬合金は高い靭性を有するが、硬さが
不足しているために切削工具として使用することはきわ
めて稀れであるが、それが２〜４０ミクロンの薄層とし
て靭性の比較的少ない超硬合金上に設けられるならば、
耐欠損性の向上にきわめて有利である。２ミクロン未満
ではその効果が少なく、４０ミクロンを越えると工具と
しての耐塑性変形性を低下させる。Cemented carbide, which is softer than the base material, has high toughness, but it is extremely rare to use it as a cutting tool due to lack of hardness, but it has a toughness comparison as a thin layer of 2 to 40 microns. If it is installed on the cemented carbide that is less
It is extremely advantageous for improving fracture resistance. If it is less than 2 microns, its effect is small, and if it exceeds 40 microns, the plastic deformation resistance as a tool is deteriorated.
本発明は４ａ，５ａ，６ａ族の炭化物，炭窒化物及び鉄
族金属からなる超硬合金の表面が、基体より軟質の厚さ
２〜４０ミクロの中間層を焼結時のガス雰囲気を調整す
ることにより生成し、次に四塩化チタン−水素−有機Ｃ
Ｎ化合物及び／又は窒素混合ガス中で加熱し、７００℃
〜９００℃で超硬合金に炭窒化チタン及び／又は窒化チ
タンを被覆したものである。The present invention adjusts the gas atmosphere at the time of sintering an intermediate layer of a cemented carbide having 4a, 5a, 6a group carbides, carbonitrides and iron group metals that is softer than the substrate and has a thickness of 2 to 40 micron. And then titanium tetrachloride-hydrogen-organic C
700 ° C by heating in N compound and / or nitrogen mixed gas
Cemented carbide is coated with titanium carbonitride and / or titanium nitride at ˜900 ° C.
化学蒸着法による炭窒化チタン，窒化チタン被覆処理は
四塩化チタン，水素，有機ＣＮ化合物，及び／又は窒素
からなる混合ガス中で行なう。有機ＣＮ化合物の分圧は
四塩化チタンの分圧より低くし、かつ水素分圧の１／１
０以下が適している。The titanium carbonitride and titanium nitride coating treatment by the chemical vapor deposition method is performed in a mixed gas of titanium tetrachloride, hydrogen, an organic CN compound, and / or nitrogen. The partial pressure of the organic CN compound should be lower than that of titanium tetrachloride, and should be 1/1 of the hydrogen partial pressure.
0 or less is suitable.
反応温度は７００〜９００℃が適している。上記条件で
表面の結合金属を富化した超硬合金に炭窒化チタン被覆
を施すと、結合相が富化しているため母材−皮膜の境界
に脱炭層が生成しやすく工具としての耐欠損性を劣化さ
せる。本発明はその為４塩化チタンと有機ＣＮ化合物を
併用することにより蒸着時の低温化を計り脱炭層の生成
を減少した。従来の化学蒸着法では基体と皮膜の境界に
生じる脱炭層（η−炭化物，Ｍ6Ｃ）のため、被覆合金
としては強度の低下が６０〜７０％と激しかったが、本
方法では８０〜９０％と小さくなる。The reaction temperature is preferably 700 to 900 ° C. When a titanium carbide / nitride coating is applied to a cemented carbide that is enriched with a binder metal on the surface under the above conditions, a decarburized layer is likely to be formed at the boundary between the base material and the coating because the binder phase is enriched, and the fracture resistance as a tool Deteriorate. Therefore, in the present invention, by using titanium tetrachloride and an organic CN compound in combination, the temperature at the time of vapor deposition can be lowered and the formation of a decarburized layer can be reduced. In the conventional chemical vapor deposition method, since the decarburized layer (η-carbide, M 6 C) formed at the boundary between the substrate and the coating, the strength of the coating alloy was severely reduced to 60 to 70%, but in the present method, it is 80 to 90%. It becomes as small as%.
第１図は従来の炭化チタン被覆超硬合金と本発明合金の
表面から微小ビッカース硬さを測定した結果を示したも
のであり、従来品は硬さが皮膜から超硬合金の硬さまで
低下しているのに対し、本発明品は基体より軟質の中間
層のため、表面より基体内部に向かって硬さが徐々に硬
くなっている。FIG. 1 shows the results of measuring the minute Vickers hardness from the surface of the conventional titanium carbide-coated cemented carbide and the alloy of the present invention. In the conventional product, the hardness decreases from the film to the hardness of the cemented carbide. On the other hand, since the product of the present invention is an intermediate layer softer than the substrate, the hardness gradually increases from the surface toward the inside of the substrate.
本発明の表面被覆超硬合金は鋼及び鋳物の断続切削に適
している。すなわち従来の被覆合金は、軟質な中間層を
設けた効果と脱炭層による逆効果が重なっても、強度は
向上する。更に、軟質な層一皮膜間の強度を高めたた
め、欠損性を向上する効果があるためである。The surface-coated cemented carbide of the present invention is suitable for intermittent cutting of steel and castings. That is, in the conventional coating alloy, the strength is improved even if the effect of providing the soft intermediate layer and the adverse effect of the decarburized layer overlap. Furthermore, since the strength between the soft layer-layer coatings is increased, there is an effect of improving the chipping property.
以下実施例について詳細に説明する。Examples will be described in detail below.
実施例１ 市販のＷＣ粉末（平均粒度４μｍ）ＴｉＣＮ粉末（平均
粒度１μｍ）ＴａＣ粉末（同１．２μｍ），Ｃｏ粉末
（同１μｍ）Ｎｉ粉末（同１μｍ）を用意し、これらを
切削用超硬合金Ｐ３０相当の組成に配合し、ボールミル
中で湿式粉砕、混合を９６時間行ない、乾燥処理後１To
n／cm2の圧力でプレス成形した。次に真空中１４００℃
で焼結し、焼結終了後ＣＨ4ガスを導入し、徐冷し、窒
化物，炭化物を主とした軟質の中間層を形成させて，そ
の後低温化学蒸着法によりＴｉＣＮを６μｍ被覆して本
発明のチップを製造した。Example 1 Commercially available WC powder (average particle size 4 μm) TiCN powder (average particle size 1 μm) TaC powder (same 1.2 μm), Co powder (same 1 μm) Ni powder (same 1 μm) were prepared. Blended to a composition equivalent to alloy P30, wet pulverized and mixed in a ball mill for 96 hours, and dried to 1 To
Press molding was performed at a pressure of n / cm 2 . Then in vacuum at 1400 ° C
After the sintering is completed, CH 4 gas is introduced and gradually cooled to form a soft intermediate layer mainly composed of nitride and carbide, and then TiCN is coated to a thickness of 6 μm by a low temperature chemical vapor deposition method. The chips of the invention were manufactured.
次に鏡面にラップし、中間層の硬さをマイクロビッカー
ス（５００ｇ荷重）で測定した。本発明冷と通常の真空
焼結の例を第１図に示す。Next, it was wrapped in a mirror surface and the hardness of the intermediate layer was measured with a micro Vickers (load of 500 g). FIG. 1 shows an example of the present invention cold and ordinary vacuum sintering.
第１図では２０μｍ程度の軟化層を形成した例を示して
いるがＣＨ4ガス分圧，冷却速度をコントロールするこ
とにより軟質の中間層の厚さ，結合相量を変化させるこ
とができ、更に基体中にＣとＮの比率の異なる場合には
ＣＨ4ガス分圧を調整することが必要である。Although FIG. 1 shows an example in which a softened layer of about 20 μm is formed, the thickness of the soft intermediate layer and the amount of binder phase can be changed by controlling the CH 4 gas partial pressure and cooling rate. When the ratio of C and N in the substrate is different, it is necessary to adjust the CH 4 gas partial pressure.
実施例２ 実施例１の合金を用いて下記の条件で切削試験を行な
い、その性能を評価した。尚比較のため通常の焼結体に
ＣＶＤ法でＴｉＣＮを６μｍ被覆した資料も試験した。Example 2 Using the alloy of Example 1, a cutting test was conducted under the following conditions to evaluate its performance. For comparison, a material obtained by coating an ordinary sintered body with TiCN to a thickness of 6 μm by the CVD method was also tested.
寿命試験 被削材 ＳＣＭ４４０ （Ｈｓ４０） チップ ＳＮＭＮ４３２（ホーニング0.03mm） 切削速度 ２００ｍ／min 送り ０．２mm／rev 切り込み ２mm 切削時間 １０min 評価 逃げ面摩耗 耐欠損性試験 被削材 ＳＣＭ４４０ （Ｈｓ４０）（４ツ溝入） チップ ＳＮＭＮ４３２（ホーニング0.03mm） 切削速度 １００ｍ／min 送り ０．３〜１．０mm／rev 切り込み ２mm 切削時間 １min 評価 ０．３mm／revより開始し、クリアーした
場合には、０．０５mm／rev送り上げ更に切削試験を続
け順次送りを増加した。Life test Work material SCM440 (Hs40) Tip SNMN432 (Honing 0.03mm) Cutting speed 200m / min Feed 0.2mm / rev Depth of cut 2mm Cutting time 10min Evaluation flank wear fracture resistance test Work material SCM440 (Hs40) (4 pieces) Grooving) Chip SNMN432 (Honing 0.03mm) Cutting speed 100m / min Feed 0.3-1.0mm / rev Depth of cut 2mm Cutting time 1min Evaluation 0.3mm / rev When started and cleared, 0.05mm / min rev feed increase The cutting test was continued and the feed was increased sequentially.
本発明チップは中間層を形成させることにより逃げ面摩
耗量ＶB＝０．１２に対し、比較チップはＶB＝０．１３
と同程度の耐摩耗性を示し中間層もある程度の厚さでは
耐摩耗性にほとんど影響していないことが分かった。次
に耐欠損性は本発明チップは中間層を形成させることに
より送り量０．８５ｍｍ／ｒｅｖに対し比較チップは送
り量０．３５ｍｍ／ｒｅｖと著しく優れていることが分
かった。The chip of the present invention has a flank wear amount VB = 0.12 by forming an intermediate layer, while the comparative chip has VB = 0.13.
It was found that the same level of wear resistance was exhibited and that the intermediate layer also had little effect on wear resistance at a certain thickness. Next, it has been found that the chip of the present invention is extremely excellent in chipping resistance as the feed rate is 0.85 mm / rev by forming the intermediate layer, while the comparative tip is the feed rate of 0.35 mm / rev.
中間層を形成することによりチップの耐摩耗性を従来の
チップと変えずに耐欠損性を向上することが出来た。By forming the intermediate layer, the chipping resistance could be improved without changing the wear resistance of the chip to that of the conventional chip.
本願表面被覆超硬合金は、基体と被覆層の中間に結合金
属に富む軟質の中間層により基体の耐欠損性を向上し、
低温化学蒸着法を適用することによる表面被覆の効果を
発揮することにより耐摩耗性，耐欠損性，耐熱性，耐溶
着性が大巾に向上し、切削工具として好適なものであ
る。The surface-coated cemented carbide of the present application improves the fracture resistance of the substrate by a soft intermediate layer rich in binding metal between the substrate and the coating layer,
By exerting the effect of surface coating by applying the low temperature chemical vapor deposition method, wear resistance, fracture resistance, heat resistance, and welding resistance are greatly improved, and it is suitable as a cutting tool.
第１図は本発明の基体と被覆層の中間に結合金属に富む
軟質の中間層の硬さをマイクロビッカース硬さで測定し
た結果を示す図である。FIG. 1 is a diagram showing the results of measuring the hardness of a soft intermediate layer rich in binding metal between the substrate and the coating layer of the present invention by micro Vickers hardness.
Claims (1)
び鉄族金属からなる超硬合金の表面が平均２０％以上の
鉄族金属と、主として前記炭化物からなり、基体より軟
質で、その厚さが２〜４０ミクロンの中間層を設けてな
る超硬合金において、被覆層が四塩化チタン−水素−有
機ＣＮ化合物及び／又は窒素混合ガス中で加熱し、７０
０℃〜９００℃で超硬合金にＴｉＣＮ及び／又はＴｉＮ
を被覆したことを特徴とする表面被覆超硬合金の製造方
法。1. A cemented carbide comprising 4a, 5a, and 6a group carbides, carbonitrides, and iron group metals has an average surface of 20% or more of an iron group metal and mainly the above-mentioned carbides, and is softer than a substrate. In a cemented carbide having an intermediate layer having a thickness of 2 to 40 microns, the coating layer is heated in a titanium tetrachloride-hydrogen-organic CN compound and / or nitrogen mixed gas,
TiCN and / or TiN on cemented carbide at 0 ° C to 900 ° C
A method for producing a surface-coated cemented carbide, characterized by being coated with.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61248087A JPH0645880B2 (en) | 1986-10-17 | 1986-10-17 | Method for producing surface-coated cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61248087A JPH0645880B2 (en) | 1986-10-17 | 1986-10-17 | Method for producing surface-coated cemented carbide |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63103072A JPS63103072A (en) | 1988-05-07 |
| JPH0645880B2 true JPH0645880B2 (en) | 1994-06-15 |
Family
ID=17173013
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61248087A Expired - Lifetime JPH0645880B2 (en) | 1986-10-17 | 1986-10-17 | Method for producing surface-coated cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0645880B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0364469A (en) * | 1989-08-01 | 1991-03-19 | Hitachi Tool Eng Ltd | Coated sintered hard alloy tool |
| JPH0386403A (en) * | 1989-08-29 | 1991-04-11 | Hitachi Tool Eng Ltd | Surface coated throw away tip |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52110209A (en) * | 1976-03-15 | 1977-09-16 | Mitsubishi Metal Corp | Coated hard alloy tool |
| JPS5826428B2 (en) * | 1977-04-23 | 1983-06-02 | 三菱マテリアル株式会社 | Coated cemented carbide tools |
| US4548786A (en) * | 1983-04-28 | 1985-10-22 | General Electric Company | Coated carbide cutting tool insert |
| JPS6133802A (en) * | 1984-07-26 | 1986-02-17 | Hitachi Metals Ltd | Coating chip for cutting |
| JPS63103069A (en) * | 1986-10-17 | 1988-05-07 | Hitachi Tool Eng Ltd | Surface coated sintered hard alloy |
-
1986
- 1986-10-17 JP JP61248087A patent/JPH0645880B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63103072A (en) | 1988-05-07 |
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