JPH04231469A - Coated ticn-base cermet - Google Patents
Coated ticn-base cermetInfo
- Publication number
- JPH04231469A JPH04231469A JP2416055A JP41605590A JPH04231469A JP H04231469 A JPH04231469 A JP H04231469A JP 2416055 A JP2416055 A JP 2416055A JP 41605590 A JP41605590 A JP 41605590A JP H04231469 A JPH04231469 A JP H04231469A
- Authority
- JP
- Japan
- Prior art keywords
- cermet
- hard
- ticn
- carbide
- toughness
- 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
- 239000011195 cermet Substances 0.000 title claims abstract description 40
- 239000002184 metal Substances 0.000 claims abstract description 21
- 229910052751 metal Inorganic materials 0.000 claims abstract description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 7
- 150000004767 nitrides Chemical class 0.000 claims abstract description 7
- 230000000737 periodic effect Effects 0.000 claims abstract description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 18
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- 239000011230 binding agent Substances 0.000 claims description 7
- 239000002245 particle Substances 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 32
- 238000005520 cutting process Methods 0.000 abstract description 13
- -1 iron group metals Chemical class 0.000 abstract description 10
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 abstract description 8
- 239000010410 layer Substances 0.000 abstract description 6
- 150000002739 metals Chemical class 0.000 abstract description 6
- 239000002344 surface layer Substances 0.000 abstract description 6
- 239000011248 coating agent Substances 0.000 abstract description 4
- 238000000576 coating method Methods 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 abstract description 4
- 239000000843 powder Substances 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 238000005245 sintering Methods 0.000 abstract description 3
- 238000004544 sputter deposition Methods 0.000 abstract description 3
- 229910003178 Mo2C Inorganic materials 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 229910052721 tungsten Inorganic materials 0.000 abstract description 2
- 239000010953 base metal Substances 0.000 abstract 1
- 150000001875 compounds Chemical class 0.000 abstract 1
- JMANVNJQNLATNU-UHFFFAOYSA-N oxalonitrile Chemical compound N#CC#N JMANVNJQNLATNU-UHFFFAOYSA-N 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 16
- 238000000034 method Methods 0.000 description 9
- 230000009257 reactivity Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 5
- 238000007733 ion plating Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- 238000010304 firing Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000011148 porous material Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005229 chemical vapour deposition Methods 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000005240 physical vapour deposition Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 238000005470 impregnation Methods 0.000 description 1
- 238000001182 laser chemical vapour deposition Methods 0.000 description 1
- 239000004973 liquid crystal related substance Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005268 plasma chemical vapour deposition Methods 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 238000007517 polishing process Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000002230 thermal chemical vapour deposition Methods 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
- 239000004416 thermosoftening plastic Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000012808 vapor phase Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、耐摩耗性、靱性に優れ
た被覆ＴｉＣＮ基サーメットおよびその製法に関するも
ので、特に切削工具として被削材の切削加工後の仕上面
に優れた被覆ＴｉＣＮ基サーメットに関する。[Field of Industrial Application] The present invention relates to a coated TiCN-based cermet with excellent wear resistance and toughness, and a method for producing the same. Regarding cermet.
【０００２】0002
【従来技術】従来から、切削用焼結体としてはＷＣ−Ｃ
ｏを主成分とする超硬合金が主として用いられていたが
、最近ではＴｉの炭化物、窒化物、炭窒化物を主成分と
するサーメット焼結体が用いられている。[Prior Art] Conventionally, WC-C has been used as a sintered body for cutting.
Cemented carbide containing Ti as a main component has been mainly used, but recently, cermet sintered bodies containing Ti carbide, nitride, and carbonitride as a main component have been used.
【０００３】このようなサーメット系焼結体としてはＴ
ｉＣを主成分とし、鉄族金属を結合相とし、さらに周期
律表第４ａ、５ａ、６ａ族金属の炭化物、窒化物、炭窒
化物を硬質相成分として加えたＴｉＣ基サーメットが主
流であった。しかし乍らこのようなＴｉＣ基サーメット
焼結体では耐熱性、強靱性に劣ることから、上記組成に
さらにＴｉＮ等の窒化物、炭窒化物を含有させることが
提案された。これは、ＴｉＮ自体が靱性に富むことによ
り、焼結体に靱性を付与するとともに、熱伝導率が高い
ことにより、耐熱衝撃性、耐熱塑性変形性を向上させよ
うとするものである。As such a cermet-based sintered body, T
TiC-based cermets, which have iC as the main component, iron group metals as the binder phase, and carbides, nitrides, and carbonitrides of metals from groups 4a, 5a, and 6a of the periodic table as hard phase components, were the mainstream. . However, since such TiC-based cermet sintered bodies are inferior in heat resistance and toughness, it has been proposed to further include nitrides such as TiN and carbonitrides in the above composition. This is intended to impart toughness to the sintered body due to TiN itself being rich in toughness, and to improve thermal shock resistance and thermoplastic deformation resistance due to its high thermal conductivity.
【０００４】そこで、従来よりＴｉＮを含有するＴｉＣ
基サーメットに対し、さらに各種の改良がなされている
。例えば特公昭５９−１４５３４号では、液晶出現温度
以下で窒素を炉内に導入し、焼結体表面に靱性に富む軟
化層を形成させることが、また、特公昭５９−１７１７
６号ではＣＯ還元雰囲気で焼成することにより、特定の
硬度を有する硬質層を形成させることが、さらに、特公
昭６０−３４６１８号によれば焼成後の降温時にＣＯ雰
囲気と成すことにより表面内部とも均一な機械特性を有
するサーメットを得ることが提案されている。[0004] Therefore, TiC containing TiN has conventionally been used.
Various further improvements have been made to the base cermet. For example, Japanese Patent Publication No. 59-14534 discloses that nitrogen is introduced into the furnace below the liquid crystal appearance temperature to form a softened layer with high toughness on the surface of the sintered body.
In No. 6, a hard layer having a specific hardness is formed by firing in a CO reducing atmosphere, and according to Japanese Patent Publication No. 60-34618, by forming a CO atmosphere when the temperature is lowered after firing, it is possible to form a hard layer on the surface and inside. It has been proposed to obtain cermets with uniform mechanical properties.
【０００５】しかし乍ら、前記先行技術によれば、硬度
あるいは靱性のいずれかについてのみ検討されるにとど
まり、高硬度および高靱性の双方を必要とする工具用材
料としては切削性能の上で未だ不十分である。However, according to the above-mentioned prior art, only either hardness or toughness is studied, and as a tool material that requires both high hardness and high toughness, it is still insufficient in terms of cutting performance. Not enough.
【０００６】かかる問題に対して、本出願人は、液相出
現温度以上にて窒素を導入後、焼結最高温度到達後に窒
素ガス圧力を低減することにより、焼結体の表面に内部
よりも高硬度、高靱性の改質部を形成したＴｉＣＮ基サ
ーメットを提案した。[0006] In order to solve this problem, the present applicant introduced nitrogen at a temperature higher than the liquid phase appearance temperature and then reduced the nitrogen gas pressure after the maximum sintering temperature was reached, so that the surface of the sintered body was heated more than the inside. We proposed a TiCN-based cermet with a modified portion of high hardness and high toughness.
【０００７】[0007]
【発明が解決しようとする問題点】しかしながら、上記
ＴｉＣＮ基サーメットによれば、焼結体中の表面部のＴ
ｉ含有比率が内部に比較して低いことに起因して、特に
鉄系材料を被削材として切削加工した場合、焼結体表面
部に多量に存在するＷや結合金属等と被削材とが反応し
、被削材の表面に荒れが生じるという問題があることが
わかった。[Problems to be Solved by the Invention] However, according to the TiCN-based cermet, the T of the surface portion of the sintered body is
Due to the low i content ratio compared to the inside, especially when machining a ferrous material as a work material, the large amount of W and bonding metals present on the surface of the sintered body may interact with the work material. It was found that there was a problem in that the surface of the workpiece was roughened by the reaction.
【０００８】よって、本発明は、ポア、ボイドがなく、
ＴｉＮの持つ特性を充分に発揮し、耐熱性、耐摩耗性、
靱性に優れるとともに被削材の切削加工後の表面が良好
な工具用の材料を提供することを目的とするものである
。[0008] Therefore, the present invention has no pores or voids,
Fully exhibiting the properties of TiN, it has heat resistance, abrasion resistance,
The object of the present invention is to provide a material for tools that has excellent toughness and has a good surface after cutting the work material.
【０００９】[0009]
【問題点を解決するための手段】本発明者は上記欠点に
対し研究を重ねた結果、本出願人が提案したその表面に
内部よりも高硬度、高靱性の改質部を有するＴｉＣＮ基
サーメットを母材とし、その表面にＴｉに富むとともに
、平均粒径が０．４μｍ 以下、且つ鉄族金属の含有量
が１００ｐｐｍ以下のＴｉを含有する硬質膜を被覆する
ことにより、サーメット母材の有する優れた特性を生か
しつつ、被削材とサーメットとの反応性が極力低減され
、切削後の被削材表面が良好なサーメットが得られるこ
とを知見し本発明に至った。[Means for Solving the Problems] As a result of repeated research into the above-mentioned drawbacks, the present inventor proposed a TiCN-based cermet having a modified portion on its surface that is harder and tougher than the inside. By coating the surface with a Ti-rich hard film containing Ti with an average particle size of 0.4 μm or less and a content of iron group metals of 100 ppm or less, the cermet base material has The present invention was achieved based on the finding that, while taking advantage of the excellent properties, the reactivity between the work material and the cermet is reduced as much as possible, and a cermet with a good surface of the work material after cutting can be obtained.
【００１０】本発明において母材となるＴｉＣＮ基サー
メットは、硬質相成分として、Ｔｉを炭化物、窒化物あ
るいは炭窒化物換算で５０乃至８０重量％、特に５５乃
至６５重量％とＷ、Ｍｏ等の周期律表６ａ族元素を炭化
物換算で１０乃至４０重量％、特に１５乃至３０重量％
とを含有する。The TiCN-based cermet which is the base material in the present invention contains Ti as a hard phase component in an amount of 50 to 80% by weight, particularly 55 to 65% by weight in terms of carbide, nitride or carbonitride, and W, Mo, etc. 10 to 40% by weight, especially 15 to 30% by weight of Group 6a elements of the periodic table in terms of carbide
Contains.
【００１１】このような硬質相成分において、Ｔｉの量
が５０重量％を下回ると耐摩耗性が低下し、９０重量％
を越えると焼結性が低下し好ましくない。また、第６ａ
族元素は粒成長抑制、結合相との濡れ性を向上させる効
果を有するが、１０重量％を下回ると上記効果が得られ
ず、硬質相が粗大化し、硬度、強度が低下する。また４
０重量％を越えるとη相等の不健全相が生じると共に焼
結が困難となる。In such a hard phase component, if the amount of Ti is less than 50% by weight, the wear resistance decreases;
If it exceeds this, the sinterability will deteriorate, which is not preferable. Also, Section 6a
Group elements have the effect of suppressing grain growth and improving wettability with the binder phase, but if the amount is less than 10% by weight, the above effects cannot be obtained, the hard phase becomes coarse, and hardness and strength decrease. Also 4
If it exceeds 0% by weight, unhealthy phases such as η phase will occur and sintering will become difficult.
【００１２】また、硬質相成分としては上記の他、耐ク
レータ摩耗性向上を目的としてＴａ、Ｎｂ、さらに耐塑
性変形性を向上させることを目的としてＺｒ、Ｖ、Ｈｆ
等を窒化物、炭化物、炭窒化物換算で５乃至４０重量％
の割合で含むことも可能であるが、４０重量％を越える
と耐摩耗性劣化、ポア、ボイドの発生著しく増加する傾
向にあり好ましくない。In addition to the above, the hard phase components include Ta and Nb for the purpose of improving crater wear resistance, and Zr, V, and Hf for the purpose of improving plastic deformation resistance.
5 to 40% by weight of nitrides, carbides, carbonitrides etc.
However, if it exceeds 40% by weight, it tends to deteriorate wear resistance and significantly increase the occurrence of pores and voids, which is not preferable.
【００１３】一方、結合相はＦｅ、Ｃｏ、Ｎｉ等の鉄族
金属を主体として成るもので、一部、硬質相形成成分が
含まれる場合がある。On the other hand, the binder phase is mainly composed of iron group metals such as Fe, Co, and Ni, and may partially contain hard phase forming components.
【００１４】焼結体全体として硬質相成分は６０乃至９
５重量％、結合相成分は５乃至４０重量％の割合から成
る。[0014] The hard phase component of the sintered body as a whole is 60 to 9.
5% by weight, and the binder phase component comprises a proportion of 5 to 40% by weight.
【００１５】本発明における組成上の特徴は、硬質相成
分中において（窒素／炭素＋窒素）で表される原子比が
０．４乃至０．６、特に０．４乃至０．５の範囲に設定
される点にある。即ち、この原子比が０．４を下回ると
靱性、耐摩耗性の向上が望めず、本発明の目的が達成さ
れず、０．６を越えると焼結体中にポア、ボイドが発生
し、工具としての信頼性が低下する。The compositional feature of the present invention is that the atomic ratio expressed by (nitrogen/carbon+nitrogen) in the hard phase component is in the range of 0.4 to 0.6, particularly 0.4 to 0.5. It is at the point where it is set. That is, if this atomic ratio is less than 0.4, no improvement in toughness or wear resistance can be expected, and the object of the present invention will not be achieved, and if it exceeds 0.6, pores and voids will occur in the sintered body. Reliability as a tool decreases.
【００１６】本発明におけるＴｉＣＮ基サーメットはこ
のような構成により、窒素を多量に含むことによる靱性
、耐摩耗性、耐熱性の向上効果を長期に旦り維持するこ
とができ、工具としての長寿命化、高信頼性を図ること
が可能性となる。しかも焼結後の焼結体に対し研磨工程
等を行うことなく、製品化することも可能となる。さら
に、サーメットの表面からおよそ１０００μｍまでの表
層部に内部より高硬度、高靱性の改質部が存在するとい
う特徴を有する。この改質層の存在によって、被覆工具
の母材として従来のサーメットと比較して切削工具とし
ての耐摩耗性、耐欠損性を大きく向上させることが可能
となった。[0016] Due to this structure, the TiCN-based cermet of the present invention can maintain the improvement effects of toughness, wear resistance, and heat resistance due to containing a large amount of nitrogen over a long period of time, and has a long life as a tool. This makes it possible to achieve high reliability. Moreover, it is possible to commercialize the sintered body without performing a polishing process or the like on the sintered body. Furthermore, the cermet is characterized in that a modified part with higher hardness and higher toughness exists in the surface layer up to approximately 1000 μm from the surface of the cermet. Due to the presence of this modified layer, it has become possible to greatly improve the wear resistance and chipping resistance of the coated tool as a base material compared to conventional cermets as a cutting tool.
【００１７】しかし、上記のサーメットは、表層部に高
硬度、高靱性の改質層が形成されるメカニズム上、サー
メットの表層部にはＴｉ等の鉄族金属との反応性が小さ
い金属の含有比率が小さく、Ｗ等の第６ａ族金属および
結合金属量が大きいことに起因して、例えば構造用合金
鋼ＳＣＭ４３５を被削材として切削を行うと、サーメッ
ト中のＷや鉄族金属が反応し、切削後の仕上げ面が荒れ
ることがある。そこで本発明によれば、かかるＴｉＣＮ
基サーメットの表面にＴｉを含有する硬質膜を被覆する
ことを特徴とする。However, because of the mechanism by which a modified layer with high hardness and high toughness is formed in the surface layer of the above cermet, the surface layer of the cermet contains metals such as Ti that have low reactivity with iron group metals. Due to the small ratio and large amount of group 6a metals such as W and combined metals, when cutting, for example, structural alloy steel SCM435 as a work material, W and iron group metals in the cermet react. , the finished surface may become rough after cutting. Therefore, according to the present invention, such TiCN
It is characterized in that the surface of the base cermet is coated with a hard film containing Ti.
【００１８】この被覆膜は、サーメット母材と被削材と
の反応性を抑制させるために、硬質膜中のＴｉ量を母材
のＴｉ量よりも富んだ膜にすることにより前述したサー
メットの被削材との反応性を抑制することができる。ま
た、サーメット表面に前述の硬質膜を形成する際にサー
メット表面に富む鉄族金属が硬質膜中に拡散し、これが
硬質膜の硬度、被削材との低反応性等硬質膜本来の特性
を劣化させてしまう。よってこの硬質膜は、その膜中の
鉄族金属量が１００ｐｐｍ以下、特に７０ｐｐｍ以下に
制御することが必要である。[0018] In order to suppress the reactivity between the cermet base material and the workpiece material, this coating film is produced by making the hard film have a Ti content richer than that of the base material. Reactivity with the work material can be suppressed. In addition, when forming the above-mentioned hard film on the cermet surface, the iron group metals that are abundant on the cermet surface diffuse into the hard film, which affects the hard film's original properties such as its hardness and low reactivity with the workpiece material. It will cause it to deteriorate. Therefore, it is necessary to control the amount of iron group metal in the hard film to 100 ppm or less, particularly 70 ppm or less.
【００１９】さらに、硬質膜を構成する結晶の粒径は、
膜の硬度、強度を左右する要因となり、その結晶粒径が
小さいほど硬質且つ高強度、高靱性な被膜となる。よっ
て本発明によれば、この硬質膜の結晶粒径が０．４μｍ
以下、特に０．３μｍ 以下に制御することにより硬
質膜としての本来の機能を発揮するとともに、膜中破壊
に起因する粒脱落、しいては膜剥離を防止することがで
きる。Furthermore, the grain size of the crystals constituting the hard film is
It is a factor that influences the hardness and strength of the film, and the smaller the crystal grain size, the harder, higher strength, and higher toughness the film becomes. Therefore, according to the present invention, the crystal grain size of this hard film is 0.4 μm.
In particular, by controlling the thickness to 0.3 μm or less, it is possible to exhibit its original function as a hard film, and to prevent particle drop-off due to breakage in the film, and thus film peeling.
【００２０】なお、Ｔｉ量がサーメット中のＴｉ量より
も富むＴｉ含有硬質膜としては、ＴｉＣ、ＴｉＮ、Ｔｉ
ＣＮ等が好適であり、これらの膜中には酸素が含まれる
場合もある。[0020] The Ti-containing hard film in which the Ti content is higher than that in the cermet includes TiC, TiN, Ti
CN or the like is preferred, and these films may contain oxygen.
【００２１】この硬質膜は、サーメット表面に１−１０
μｍ の厚みで被覆することが望ましく、膜厚が１μｍ
より小さいと被削材との反応性抑制効果がなく、被削
材の表面に荒れが生じ、１０μｍ より厚いと母材と被
覆層との熱膨張差に起因して使用時に膜剥離を生じやす
い。[0021] This hard film coats the cermet surface with a 1-10
It is desirable to coat with a thickness of 1 μm.
If it is smaller than 10 μm, it will not have the effect of suppressing the reactivity with the workpiece material and the surface of the workpiece material will become rough, and if it is thicker than 10μm, the film will likely peel off during use due to the difference in thermal expansion between the base material and the coating layer. .
【００２２】本発明の被覆ＴｉＣＮ基サーメットにおい
て、母材となる上記ＴｉＣＮ基サーメットを製造する方
法は、例えば特開平２−１５１３９号に記載された方法
に基づき容易に製造することができる。In the coated TiCN-based cermet of the present invention, the TiCN-based cermet serving as the base material can be easily manufactured based on, for example, the method described in JP-A-2-15139.
【００２３】かかるＴｉＣＮ基サーメットの表面にＴｉ
含有硬質膜を形成する方法としては具体的には、熱ＣＶ
Ｄ法、プラズマＣＶＤ法、レーザＣＶＤ法等の化学気相
成長法（ＣＶＤ法）、スパッタリング法、イオンプレー
ティング法等の物理的蒸着法（ＰＶＤ法）、あるいは気
相含浸法等が採用できるが、本発明に基づき硬質膜の粒
径を０．４μｍ 以下に制御するにはイオンプレーティ
ング法、スパッタリング法が望ましい。[0023] Ti is deposited on the surface of such TiCN-based cermet.
Specifically, the method for forming the containing hard film is thermal CVD.
Chemical vapor deposition methods (CVD methods) such as the D method, plasma CVD method, and laser CVD method, physical vapor deposition methods (PVD methods) such as sputtering methods and ion plating methods, or vapor phase impregnation methods can be used. In order to control the particle size of the hard film to 0.4 μm or less based on the present invention, ion plating method and sputtering method are preferable.
【００２４】また、鉄族金属の硬質膜中への混入量を１
００ｐｐｍ以下に制御するとともに母材との膜付着強度
を考慮した場合、イオンプレーティング法、プラズマＣ
ＶＤ法が望ましく、特にイオンプレーティング法によれ
ば成膜温度が低いことに起因して膜の結晶粒の制御が容
易で、しかも母材からの鉄族金属の拡散が抑制されるた
めに膜中への混入を防止することができる。また、成膜
にあたっては、反応炉内の設備等において鉄族金属製の
部品を極力排除するように考慮することも必要である。
以下、本発明を次の例で説明する。[0024] Also, the amount of iron group metal mixed into the hard film was reduced to 1
When controlling the amount to 00 ppm or less and considering the film adhesion strength to the base material, ion plating method, plasma C
The VD method is preferable, and in particular, the ion plating method allows easy control of crystal grains in the film due to the low film formation temperature, and also suppresses the diffusion of iron group metals from the base material, making it difficult to form a film. It is possible to prevent the mixture from entering the inside. Furthermore, during film formation, it is also necessary to consider eliminating parts made of iron group metals as much as possible in the equipment in the reactor. The invention will now be explained with the following examples.
【００２５】[0025]
【実施例】原料粉末として平均粒径が１〜１．５μｍ
のＴｉ（ＣＮ）、ＴｉＮ、ＴｉＣ、ＷＣ、Ｍｏ２ Ｃ，
ＮｂＣ、ＮｂＮ、ＶＣ、ＮｉおよびＣｏを用い、表１の
組成に調合後、振動ミルで粉砕を行い、バインダーを添
加したものをＴＮＧＡ３３２チップ形状にプレス成形し
、３００℃で脱バインダー後、この成形体を焼成炉内に
配置し、約１３００℃の液相出現温度以降に７０ａｔｍ
の圧力の窒素ガスを導入し 、１５００℃の焼成最高
温度まで昇温後、圧力を徐々に減圧し最終的に真空まで
減圧した。得られたサーメットについてその表面部と内
部との硬度および靱性を測定したところ、いずれも表層
部の方が硬度、靱性ともに高くなっており、表層部に改
質部が形成されていることを確認した。また得られた焼
結体に対し、硬質相の炭素、窒素を定量分析し、（Ｎ／
Ｃ＋Ｎ）原子比を求めた。[Example] Average particle size as raw material powder is 1 to 1.5 μm
Ti(CN), TiN, TiC, WC, Mo2C,
NbC, NbN, VC, Ni, and Co were mixed into the composition shown in Table 1, then ground in a vibrating mill, and a binder was added, which was then press-molded into the shape of a TNGA332 chip. After removing the binder at 300°C, this molding was performed. The body is placed in a firing furnace and heated to 70 atm after the liquid phase appearance temperature of approximately 1300°C.
After introducing nitrogen gas at a pressure of 1,500° C. and raising the temperature to the maximum firing temperature of 1,500° C., the pressure was gradually reduced and finally reduced to vacuum. When we measured the hardness and toughness of the surface and interior of the obtained cermet, both hardness and toughness were higher in the surface layer, confirming that a modified part was formed in the surface layer. did. In addition, the obtained sintered body was quantitatively analyzed for carbon and nitrogen in the hard phase.
C+N) atomic ratio was determined.
【００２６】次に、各サーメットを母材としてイオンプ
レーティング法により母材温度を３００−７００℃に設
定し、３μｍ の厚みになるようにＴｉＮ、ＴｉＣＮ、
ＴｉＣＮＯ膜を形成した。また、被覆膜における平均結
晶粒径をＳＥＭにより、また膜中の鉄族金属量をＩＣＰ
分析により測定した。Next, using each cermet as a base material, the base material temperature was set at 300-700°C using the ion plating method, and TiN, TiCN,
A TiCNO film was formed. In addition, the average grain size in the coating film was measured by SEM, and the amount of iron group metals in the film was measured by ICP.
Determined by analysis.
【００２７】次に各試料に対し、下記条件で耐摩耗試験
、耐欠損試験を行い、耐摩耗試験ではフランク摩耗量（
ｍｍ）を測定し、耐欠損試験では、試験後欠損が生じな
かったコーナ数を調べた。Next, each sample was subjected to a wear resistance test and a chipping resistance test under the following conditions, and the flank wear amount (
mm), and in the fracture resistance test, the number of corners where no fracture occurred after the test was determined.
【００２８】摩耗試験
被削材 ＳＣＭ４３５
切削速度 ２００ｍ／ｍｉｎ
切り込み ２ｍｍ
送り ０．３ｍｍ／ｒｅｖ切削時間
１０ｍｉｎ
耐欠損試験
被削材 ＳＣＭ４３５（丸棒Ｎｓ−４０）４
ツ溝入り
切削速度 １００ｍ／ｍｉｎ
切削時間 １ｍｉｎ
切り込み ２ｍｍ
送り ０．２ｍｍ／ｒｅｖWear test work material SCM435 Cutting speed 200m/min Depth of cut 2mm Feed 0.3mm/rev Cutting time
10min Fracture resistance test work material SCM435 (round bar Ns-40) 4
Grooving cutting speed 100m/min Cutting time 1min Depth of cut 2mm Feed 0.2mm/rev
【００２９】
また、仕上げ面の評価として。表面粗さ計を用いて、被
削材仕上げ面状態をＲｍａｘにて表現する手法により、
この値が１０ｓ以上のものを×、１０ｓ未満のものを○
として評価した。[0029]
Also, as an evaluation of the finished surface. By using a surface roughness meter to express the finished surface condition of the workpiece material in terms of Rmax,
× if this value is 10s or more, ○ if this value is less than 10s
It was evaluated as
【００３０】[0030]
【表１】[Table 1]
【００３１】[0031]
【表２】[Table 2]
【００３２】表１および表２の結果から明らかなように
、（Ｎ／Ｃ＋Ｎ）比が０．４を下回る試料番号３は焼結
体表面に粗れが生じており、耐摩耗性も悪い。逆に比が
０．６を越える試料番号４では良好な焼結体を得られず
、耐摩耗テストができなかった。As is clear from the results in Tables 1 and 2, Sample No. 3, in which the (N/C+N) ratio was less than 0.4, had roughness on the surface of the sintered body and had poor wear resistance. On the other hand, in sample number 4 where the ratio exceeded 0.6, a good sintered body could not be obtained and the wear resistance test could not be performed.
【００３３】[0033]
【発明の効果】以上、詳述した通り、本発明の被覆Ｔｉ
ＣＮ基サーメットによれば、窒素は所定量含有するとと
もに、表面部に内部よりも高硬度、高靱性を有する改質
相が存在するサーメットの表面にＴｉ含有硬質膜を形成
することにより、優れた耐摩耗性、耐欠損性を有し、且
つ被削材との反応性が抑制されることによりサーメット
母材の特性を維持しつつ、被削材の切削加工後の表面を
良好なものとすることができる。Effects of the Invention As detailed above, the coated Ti of the present invention
According to the CN-based cermet, a Ti-containing hard film is formed on the surface of the cermet, which contains a predetermined amount of nitrogen and has a modified phase that has higher hardness and toughness than the inside. It has wear resistance and fracture resistance, and suppresses reactivity with the workpiece material, thereby maintaining the characteristics of the cermet base material and improving the surface of the workpiece material after cutting. be able to.
Claims (1)
換算で５０乃至８０重量％、周期律表第６ａ族元素を炭
化物換算で１０乃至４０重量％の割合で含有するととも
に、（窒素／炭素＋窒素）で表される原子比が０．４乃
至０．６の範囲にある硬質相成分６０乃至９５重量％と
、鉄族金属を主成分とする結合相成分５乃至４０重量％
とから構成され、表面から１０００μｍまでの表層部に
内部より高靱性、高硬度の改質部が存在するＴｉＣＮ基
サーメットの表面に、該ＴｉＣＮ基サーメット中のＴｉ
量よりも富み、平均粒径０．４μｍ以下、鉄族金属含有
量が１００ｐｐｍ以下のＴｉを含有する硬質膜を被覆し
てなることをを特徴とする被覆ＴｉＣＮ基サーメットClaim 1: Contains Ti in a proportion of 50 to 80% by weight in terms of carbide, nitride, or carbonitride, and contains 10 to 40% by weight of Group 6a elements of the periodic table in terms of carbide; 60 to 95% by weight of a hard phase component having an atomic ratio of 0.4 to 0.6 (carbon + nitrogen), and 5 to 40% by weight of a binder phase component whose main component is an iron group metal.
The surface of the TiCN-based cermet is composed of
A coated TiCN-based cermet characterized by being coated with a hard film containing Ti with an average particle size of 0.4 μm or less and an iron group metal content of 100 ppm or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2416055A JP2828512B2 (en) | 1990-12-27 | 1990-12-27 | Coated TiCN-based cermet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2416055A JP2828512B2 (en) | 1990-12-27 | 1990-12-27 | Coated TiCN-based cermet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04231469A true JPH04231469A (en) | 1992-08-20 |
| JP2828512B2 JP2828512B2 (en) | 1998-11-25 |
Family
ID=18524308
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2416055A Expired - Fee Related JP2828512B2 (en) | 1990-12-27 | 1990-12-27 | Coated TiCN-based cermet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2828512B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110373593A (en) * | 2019-07-01 | 2019-10-25 | 南京理工大学 | A kind of titanium carbonitride based composite metal ceramic material microwave sintering process |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103540824B (en) * | 2013-10-21 | 2015-11-18 | 江门市楚材科技有限公司 | A kind of cermet material |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6299467A (en) * | 1985-10-25 | 1987-05-08 | Hitachi Carbide Tools Ltd | Surface-coated sintered hard alloy |
| JPS6458402A (en) * | 1987-08-25 | 1989-03-06 | Dijet Ind Co Ltd | Coated tip for cutting work |
| JPH01129971A (en) * | 1987-11-13 | 1989-05-23 | Sumitomo Electric Ind Ltd | Manufacture of coated cutting tool |
| JPH0215139A (en) * | 1988-03-11 | 1990-01-18 | Kyocera Corp | Ticn-base cermet and its manufacture |
-
1990
- 1990-12-27 JP JP2416055A patent/JP2828512B2/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6299467A (en) * | 1985-10-25 | 1987-05-08 | Hitachi Carbide Tools Ltd | Surface-coated sintered hard alloy |
| JPS6458402A (en) * | 1987-08-25 | 1989-03-06 | Dijet Ind Co Ltd | Coated tip for cutting work |
| JPH01129971A (en) * | 1987-11-13 | 1989-05-23 | Sumitomo Electric Ind Ltd | Manufacture of coated cutting tool |
| JPH0215139A (en) * | 1988-03-11 | 1990-01-18 | Kyocera Corp | Ticn-base cermet and its manufacture |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110373593A (en) * | 2019-07-01 | 2019-10-25 | 南京理工大学 | A kind of titanium carbonitride based composite metal ceramic material microwave sintering process |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2828512B2 (en) | 1998-11-25 |
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