JP5681093B2 - Multilayer hard coating - Google Patents

Description

  The present invention is formed on the surface of a base material such as a sliding tool or a cutting tool that slides on other members such as jigs and punches for molding, jigs and tools that require wear resistance, and machine parts. Relates to a multilayer hard coating.

In order to improve the wear resistance and extend the tool life on the surface of a base material such as a sliding member or a cutting tool, for example, a film using a material such as TiB ₂ , B ₄ C, or SiC should be formed. Is generally done. Since the films formed using these materials are all extremely hard (˜40 GPa), they are called hard films and multilayer hard films (in particular, the one in which a plurality of the above-mentioned layers are laminated is called in this way). It is. Patent Documents 1 to 5 describe techniques for forming a hard coating or a multilayer hard coating with at least one layer of TiB ₂ , B ₄ C, and SiC.

In Patent Document 1, a TiB ₂ layer, a two-phase mixed layer of TiB ₂ and TiN phases, and a TiAlN layer are sequentially laminated on the surface of a tool base made of a cubic boron nitride-based ultrahigh pressure sintered material. It is described that a multilayer hard film is formed.

Patent Document 2 discloses a hard coating including at least one TiB ₂ layer having a fibrous microstructure in which fibrous grains having a predetermined diameter and length are oriented perpendicular to the surface of a cutting tool. It describes that it is formed on the surface of the substrate.

In Patent Document 3, a multilayer hard coating is formed by sequentially laminating a BCN layer, a B ₄ C layer, and a TiAlN layer on the surface of a tool base made of a cubic boron nitride-based ultrahigh pressure sintered material. The effect is described.

  Furthermore, Patent Document 4 describes that a hard film made of SiC is formed on the surface of a base material.

In Patent Document 5, a nitride or carbonitride of one or more elements selected from the group consisting of a group 4A element, a group 5A element, a group 6A element and Al formed on the surface of a base material is a main component. the hard film in which _{a, B 4 C, BN, TiB} 2, TiB, TiC, WC, SiC, at least is selected from the group consisting of SiN _{X (X} = 0.5~1.33) and Al ₂ O ₃ It describes that one kind of ultrafine compound is included.

  When a hard coating or a multilayer hard coating (hereinafter simply referred to as a multilayer hard coating) is formed as in Patent Documents 1 to 5, it is possible to improve wear resistance and the like. However, since the difference in hardness between the multilayer hard coating and the base material is large, the adhesion is poor, and the multilayer hard coating peels off from the surface of the base material, so that the life of the member can be sufficiently extended. There is a problem that is not always.

In order to solve such a problem, Patent Document 1 uses a cubic boron nitride-based ultrahigh pressure sintered material to improve the adhesion and to extend the life of the sliding member. Further, in Patent Document 3, the adhesion is further improved by forming a BCN layer between the surface of the tool base made of cubic boron nitride-based ultrahigh pressure sintered material and the B ₄ C layer. Longer life is achieved. In Patent Document 5, adhesion is improved by including TiB ₂ , B ₄ C, SiC, or the like in the hard coating, and the life of the sliding member is extended.

JP 2010-228032 A Japanese Patent No. 4184491 JP 2010-207922 A JP 2007-090483 A Japanese Patent No. 3914687

However, although the TiB ₂ layer and the B ₄ C layer described in Patent Documents 1 to 5 are excellent in hardness, there is a drawback that the oxidation resistance is not so high. Therefore, there is a problem that the member is oxidized and deteriorated due to a high temperature during sliding, and the life of the member (for example, the tool life for a cutting tool or the like) cannot be sufficiently achieved.
Moreover, although the SiC layer described in Patent Documents 4 and 5 is excellent in hardness and oxidation resistance, it is considered to have a defect that adhesion to the base material is low. Therefore, there is a problem that the life of the member cannot be extended.

  This invention is made | formed in view of the said situation, and makes it a subject to provide the multilayer hard film which can aim at the lifetime improvement of a member.

(1) The present invention is a multilayer hard coating formed on the surface of a substrate, and Ti _1-x Si _x (B _p C _q N _r ) [where 0.05 ≦ x ≦ 0.4, p ≧ 0, q ≧ 0, r> 0, p + q + r = 1], an A layer having a thickness of 100 nm or less, and Ti _1-agb B _a C _g N _b [provided that 0.2 ≦ a ≦ 0.5 , 0.3 ≦ b ≦ 0.6, 0 ≦ g ≦ 0.5], Si _1-cd C _c N _d [however, 0.2 ≦ c ≦ 0.5, 0.3 ≦ d ≦ 0.5 _{], B 1-ef C e} N f [ however, consists of one or more selected from 0.03 ≦ e ≦ 0.25,0.3 ≦ f ≦ 0.55], with a 20nm or less thick than 2nm and B layers, but are stacked a plurality of times state, and are total 500nm or more of the thickness of the laminated the a layer and the B layer, and the layer a lowermost, the surface and the B layer of the lowermost and wherein the mania Rukoto of the
Here, the “base material” is defined as a base material for a sliding member such as a jig, a tool, a machine part (including a mold, a die, and a punch) or a cutting tool. A “member” is defined as a substrate coated with a laminated hard film.

  As described above, in the present invention, a multi-layer structure is formed by laminating the A layer having high hardness and excellent oxidation resistance and the B layer having a crystallinity that is low when deposited and having a structure close to amorphous. Thus, a hard film (multilayer hard film) is realized. That is, crystal growth of the A layer is interrupted at the interface of the B layer having a structure close to amorphous. Therefore, the crystal grain size of the A layer is difficult to increase, and the crystal grains are refined. Since the A layer in which the crystal grains are miniaturized has higher hardness, the hardness of the multilayer hard coating also becomes higher. Further, the B layer contains a predetermined amount of nitrogen (N), so that it has excellent lubricity and adhesion with the A layer and has high hardness. Therefore, by laminating the A layer and the B layer a plurality of times and setting the thickness to 500 nm or more, it is possible to reliably improve the wear resistance and oxidation resistance as the multilayer hard coating. As a result, the lifetime of the member can be extended.

(2) The multilayer hard coating described in (1) includes a vacuum arc evaporation source attached with a target for forming the A layer and a sputtering evaporation source attached with a target for forming the B layer in the same chamber. The substrate is rotated so as to pass a plurality of times in front of the vacuum arc evaporation source and the sputtering evaporation source in the chamber, and the vacuum arc evaporation source and the sputtering evaporation source are simultaneously It is preferable to discharge and laminate the A layer and the B layer on the surface of the substrate a plurality of times.

  If it does in this way, not only can A layer and B layer be laminated | stacked rapidly, but a multilayer hard film can be formed, but the adhesiveness in the interface of A layer and B layer can be improved.

(3) the multilayer hard coating according to (1) or (2), on the _{surface, M 1-y Al y (} B a C b N c O d) [ However, 0.05 ≦ y ≦ 0 .8, 0 ≦ a ≦ 0.2, 0 ≦ b ≦ 0.4, 0.5 ≦ c ≦ 1, 0 ≦ d ≦ 0.2, M represents a group 4A element, a group 5A element, a group 6A element, Si And one or more elements selected from Y and Y] are preferably formed.

(4) In the multilayer hard coating according to (3), the combination related to the composition of the underlayer is AlCr (CN), TiAl (CN), TiCrAl (CN), AlCrSi (CN), TiAlSi (CN), or TiCrAlSi (CN) is preferred.

  Thus, when the base layer described in (3) or (4) is formed on the surface of the base material, these adhesions can be further improved. As a result, the life of the substrate can be further extended.

(5) In the multilayer hard coating according to (1), the base material is preferably a cutting tool and / or a sliding member, (6) preferably a cutting tool, and (7) a sliding member. It is preferable.
If it does in this way, the abrasion resistance and oxidation resistance of a cutting tool or a sliding member can be improved reliably. As a result, it is possible to extend the life of these.

(8) Furthermore, in the multilayer hard coating described in (1), it is preferable that the A layer and the B layer are alternately laminated.
If it does in this way, the abrasion resistance and oxidation resistance as a multilayer hard membrane | film | coat can be improved more reliably. As a result, the lifetime of the member can be further increased.

  ADVANTAGE OF THE INVENTION According to this invention, the multilayer hard membrane | film | coat which can aim at the lifetime improvement of a member can be provided.

It is a schematic cross section explaining the multilayer hard coat concerning a 1st embodiment of the present invention. It is a schematic cross section explaining a multilayer hard coat concerning a 2nd embodiment of the present invention. It is a schematic block diagram of the film-forming apparatus.

Hereinafter, a mode (embodiment) for carrying out the present invention will be described in detail with reference to FIGS.
The present invention is a multilayer hard coating formed on the surface of a member, and a first embodiment thereof is shown in FIG. FIG. 1 is a cross-sectional view of a member 10 such as a cutting tool or a sliding member.
As shown in FIG. 1, the multilayer hard coating 1 according to the first embodiment has an A layer 11 and a B layer 12 laminated on the surface of a substrate 2 a plurality of times, preferably alternately.

The A layer 11 is made of Ti _1-x Si _x (B _p C _q N _r ) [where 0.05 ≦ x ≦ 0.4, p ≧ 0, q ≧ 0, r> 0, p + q + r = 1]. .

Since the A layer 11 requires high hardness and oxidation resistance, as described above, the atomic ratio (atomic fraction) of Si (silicon) in Ti _1-x Si _x is 0.05 to 0.4. It is necessary to. When the atomic ratio of Si in Ti _1-x Si _x is less than 0.05, the oxidation resistance is lowered, and the life of the member 10 is not extended. Further, when the atomic ratio of Si in Ti _1-x Si _x exceeds 0.4, the material becomes amorphous and the hardness of the A layer 11 is lowered, so that the life of the member 10 is not extended. The atomic ratio of Si in Ti _1-x Si _x is preferably 0.1 to 0.3.

The A layer 11 is based on nitride (-N), but B (boron) and / or C () as defined by B _p (p ≧ 0) and C _q (q ≧ 0). Carbon) can optionally be included. The atomic ratio of B is preferably 0.3 or less, and the atomic ratio of C is preferably 0.6 or less. If the atomic ratio of B and C is less than this, sufficient hardness can be maintained.

As will be described later, the A layer 11 has an effect of increasing the hardness (crystal grain refining effect) by crystal grains being refined by the B layer. In the present invention, the thickness needs to be 100 nm or less in order to refine crystal grains of Ti _1-x Si _x (B _p C _q N _r ). When the thickness of the A layer 11 exceeds 100 nm, the crystal grain refining effect does not occur and the hardness decreases. The A layer 11 is preferably 10 to 50 nm, and more preferably 10 to 20 nm.

  In addition, the A layer 11 can improve the adhesion between the base material 2 and the B layer 12. Therefore, it is preferable that the lowermost layer of the multilayer hard coating 1 forms the A layer 11 between the surface of the substrate 2 and the lowermost B layer 12 closest to the substrate 2.

B layer _{12, Ti 1-agb B a C} g N b [ however, 0.2 ≦ a ≦ 0.5,0.3 ≦ b ≦ 0.6,0 ≦ g ≦ 0.5], Si 1- _cd C _c N _d [where 0.2 ≦ c ≦ 0.5, 0.3 ≦ d ≦ 0.5], B _1-ef C _e N _f [where 0.03 ≦ e ≦ 0.25, 0.3 ≦ f ≦ 0.55].

Since the B layer 12 is one or more types selected from the above-mentioned options, in addition to the one selected from these options, the B layer 12 includes two types selected as appropriate, and all three types. can do.
In addition, as for the case where the B layer 12 is composed of two types from the above-mentioned options, the combination concerning the composition is SiCN and TiBN, the case of SiCN and TiBCN, the case of TiBN and BCN, the case of TiBCN and BCN, the case of BCN and SiCN Can be mentioned. When the B layer 12 constituting the multilayer hard coating 1 includes two types of B layers 12, it can be formed by two types of SiCN, TiBCN, and BCN, respectively, and the B layer 12 constituting the multilayer hard coating 1. For example, the B layer 12 of SiCN and the B layer 12 of TiBN can be used.

  For example, the configuration of the multilayer hard coating 1 in which the B layer 12 having a combination of composition of two types, SiCN and TiBN, is formed on the surface of the substrate 2 as follows: TiSi (BCN) (A layer 11) / TiBN (B layer 12 ) / TiSi (BCN) (A layer 11) / SiCN (B layer 12), and when the B layer 12 composed of all three types is formed, the structure of TiSi (BCN) is formed on the surface of the substrate 2. (A layer 11) / TiBN (B layer 12) / TiSi (BCN) (A layer 11) / SiCN (B layer 12) / TiSi (BCN) (A layer 11) / BCN (B layer 12) .

  Of the above-described options for configuring the B layer 12, TiBN and TiBCN are not necessarily high in hardness because they include BN bonds having a lubricating action, but the combination of the composition is composed of TiSi (BCN) and a multilayer structure. A sufficiently high hardness can be obtained by forming.

When the atomic ratio of B in Ti _{1 -agb} B _a C _g N _b is 0.2 to 0.5, an excellent lubricating action can be obtained, so that the life of the member 10 can be extended. When the atomic ratio of B in Ti _{1 -agb} B _a C _g N _b is less than 0.2, a lubricating action cannot be obtained, and the hardness also decreases. Therefore, the lifetime of the member 10 is not extended. The atomic ratio of B in the _{Ti 1-agb B a C g} N b is lowered hardness exceeds 0.5. Therefore, the lifetime of the member 10 is not extended.

Further, the atomic ratio of N in the _{Ti 1-agb B a C g} N b is at 0.3 to 0.6, it is possible to obtain an excellent lubricating effect. When the atomic ratio of N in Ti _{1 -agb} B _a C _g N _b is less than 0.3, a lubricating action cannot be obtained, and the hardness also decreases. Therefore, the lifetime of the member 10 is not extended. When the atomic ratio of N in Ti _1-agb B _a C _g N _b exceeds 0.6, the hardness decreases, so the life of the member 10 does not extend.

The atomic ratio of C in the _{Ti 1-agb B a C g} N b is 0.5 or less, it is possible to obtain a high hardness. When _{Ti 1-agb B a C g} N b atomic ratio of C in is more than 0.5, while the B layer 12, not bound to a metal element and B, the unreacted C are precipitated, B layer 12 hardness decreases. Therefore, the lifetime of the member 10 is not extended.

  Of the above-mentioned options for configuring the B layer 12, SiCN contains Si and N, and thus has high affinity with TiSi (BCN) of the A layer 11 and excellent adhesion.

When the atomic ratio of C in Si _1-cd C _c N _d is 0.2 to 0.5, high hardness can be obtained. The hardness decreases in both cases where the atomic ratio of C in Si _1-cd C _c N _d is less than 0.2 and exceeds 0.5. Therefore, the lifetime of the member 10 is not extended.

In addition, when the atomic ratio of N in Si _{1 -cd} C _c N _d is 0.3 to 0.5, a lubricating action and high hardness can be obtained. The hardness decreases in both cases where the atomic ratio of N in Si _{1 -cd} C _c N _d is less than 0.3 and exceeds 0.5. Therefore, the lifetime of the member 10 is not extended.

  Of the above-mentioned options for configuring the B layer 12, the hardness is not necessarily high because the BCN includes a BN bond having a lubricating action, but it is sufficient to form a multilayer structure with the A layer 11 including TiSi (BCN). High hardness can be obtained.

The atomic ratio of C in B _1-ef C _e N _f is a 0.03 to 0.25, it is possible to obtain a high hardness. Hardness decreases in any of the case where the atomic ratio of C in B _1-ef C _e N _f exceeds if and 0.25 of less than 0.03.

The atomic ratio of N in B _1-ef C _e N _f is the is from 0.3 to 0.55, it is possible to obtain a lubricating action. Hardness decreases in any of the case where the atomic ratio of N in B _1-ef C _e N _f exceeds if and 0.55 of less than 0.3. Moreover, there is a possibility that the lubricating action is insufficient. Therefore, the lifetime of the member 10 is not extended. The atomic ratio of N in B _1-ef C _e N _f is preferably 0.05 to 0.2.

  The thickness of the B layer 12 is 2 nm or more and 20 nm or less. When the thickness of the B layer 12 is in such a range, the hardness of the A layer 11 can be increased due to the effect of crystal grain refinement. When the thickness of the B layer 12 is less than 2 nm, the adjacent A layer 11 cannot be controlled well, and the crystal grains of the A layer 12 are not sufficiently refined. Therefore, the hardness of the A layer 12 is lowered, and the hardness of the multilayer hard coating 1 is also lowered accordingly. Therefore, the lifetime of the member 10 is not extended. On the other hand, when the thickness of the B layer 12 exceeds 20 nm, the hardness of the entire multilayer hard coating 1 is lowered because the B layer 12 is too thick. Therefore, the lifetime of the member 10 is not extended. The thickness of the B layer 12 is preferably 5 nm or more and 10 nm or less.

It is preferable that the plurality of A layers 11 and B layers 12 are alternately stacked with the thicknesses described above.
The number of repetitions of the A layer 11 and the B layer 12 may be, for example, 5 times or more, but may be 15 times or more, 263 times or more.
In addition to the A / B / A / B, the A layer 11 and the B layer 12 are repeatedly formed in such a manner that A / B1 / A / B2 / A / B3 are laminated. It is also possible to switch the composition of the B layer 12 within the specified film thickness range of the B layer 12 such as A / B1 ′ / B2 ′ / B3 ′ / A.

  The total thickness of the laminated A layer 11 and B layer 12 is 500 nm or more from the viewpoint of extending the life of the member 10. When the total thickness of the laminated A layer 11 and B layer 12 is less than 500 nm, the portion exhibiting wear resistance becomes thin, and the life of the member 10 is not extended. The longer the total thickness of the stacked A layer 11 and B layer 12 is, the longer the life is. However, this effect does not extend when the thickness exceeds approximately 5000 nm. Therefore, the upper limit of the total thickness of the laminated A layer 11 and B layer 12 is preferably about 5000 nm.

Next, a second embodiment of the present invention will be described.
FIG. 2 is a cross-sectional view of the member 20 such as a cutting tool or a sliding member. As shown in FIG. 2, the multilayer hard film according to the second embodiment is between the surface of the base material 2 and the multilayer laminated film 1, preferably between the surface of the base material 2 and the A layer 11 which is the lowest layer. An underlayer 13 is formed.

Such undercoat layer _{13, M 1-y Al y (} B a C b N c O d) [ However, 0.05 ≦ y ≦ 0.8,0 ≦ a ≦ 0.2,0 ≦ b ≦ 0.4 0.5 ≦ c ≦ 1, 0 ≦ d ≦ 0.2, and M is one or more elements selected from Group 4A elements, Group 5A elements, Group 6A elements, Si and Y].

  Examples of the 4A group element include Ti (titanium), Zr (zirconium), and Hf (hafnium). Examples of the 5A group element include V (vanadium), Nb (niobium), and Ta (tantalum). Examples of the 6A group element include Cr (chromium), Mo (molybdenum), and W (tungsten).

  Preferable examples of the combination relating to the composition of the underlayer 13 include AlCr (CN), TiAl (CN), TiCrAl (CN), AlCrSi (CN), TiAlSi (CN), and TiCrAlSi (CN). Needless to say, the underlayer 13 selected from these is configured with the above-described atomic ratio.

  Preferred examples of the combination relating to the composition of the underlayer 13 are as described above, but the underlayer 13 that can be used in the present invention is not limited to these. For example, a combination of TiAlN, TiN, AlCrN, TiCrAlN, TiAlSiN, AlCrSiN, TiCrAlSiN, NbAlN, or HfAlN may be used.

Such undercoat layer 13, from the viewpoint of hardness and oxidation resistance, as mentioned above, preferably with 0.05 to 0.8 atomic ratio of Al (aluminum) in the M _1-y Al y. By forming the base layer 13, it is possible to further improve the adhesion between the base material 2 and the multilayer hard coating 1. Both when the atomic ratio of Al in the M _1-y Al _y exceeds the case of less than 0.05 and 0.8, as compared with the case the atomic ratio of Al in the M _1-y Al _y is within the numerical range mentioned above In addition, the hardness and oxidation resistance are slightly inferior, so the effect of extending the life is diminished. The atomic ratio of Al in the M _1-y Al _y is more preferably 0.1 to 0.6.

  The underlayer 13 is based on M nitride having an N atomic ratio of 0.5 to 1, and can optionally contain B, C, and O. The atomic ratio of B can be 0 to 0.2, the atomic ratio of C can be 0 to 0.4, and the atomic ratio of O (oxygen) can be 0 to 0.2. . When B, C, and O are included at this atomic ratio, the adhesion between the base material 2 and the multilayer hard coating 1 can be further enhanced.

  If the thickness of the underlayer 13 is approximately 50 nm or more, it has an effect of improving adhesion, but is preferably 100 nm or more, and more preferably 500 nm or more. The thickness of the underlayer 13 is preferably 2000 nm or less.

As shown in FIG. 3, the multilayer hard coating 1 described as the first embodiment and the second embodiment includes a vacuum arc evaporation source 101 with a target for forming the A layer 11 and a target for forming the B layer 12. The sputtering evaporation source 102 attached can be formed using the film forming apparatus 100 provided in the same chamber 103. Specifically, the substrate 2 is rotated so as to alternately pass in front of a plurality of vacuum arc evaporation sources 101 and sputtering evaporation sources 102 in the chamber 103, and the vacuum arc evaporation source 101 and the sputtering evaporation source 102 are discharged simultaneously. Then, the A layer 11 and the B layer 12 can be laminated on the surface of the substrate 2 a plurality of times, preferably alternately.
The substrate 2 can be rotated by being attached to a stage 105 that is rotatably provided in the chamber 103.
The vacuum arc evaporation source 101 can be suitably used as long as it is a cathode discharge type arc ion plating evaporation source.
The sputtering evaporation source 102 is also called an unbalanced magnetron sputtering evaporation source, and for example, UBMS 202 manufactured by Kobe Steel can be suitably used.
In FIG. 3, the film forming apparatus 100 including two vacuum arc evaporation sources 101 and two sputtering evaporation sources 102 is shown, but three of each may be provided and arranged alternately.

  The multilayer hard coating 1 formed in this way can increase the adhesion between the plurality of A layers 11 and B layers 12. Further, the A layer 11 and the B layer 12 can be laminated only by rotating the substrate 2 and passing the front of the vacuum arc evaporation source 101 and the sputtering evaporation source 102 a plurality of times, preferably alternately. That is, the A layer 11 and the B layer 12 can be laminated quickly and easily.

  As shown in FIG. 3, the film forming apparatus 100 includes a vacuum pump (not shown), a gas supply mechanism 104, the stage 105, the heater 106, the bias power source 107, and the sputtering power source 108. And an arc power source 109.

In the film forming apparatus 100, gases such as Ar, N ₂ , and CH ₄ are supplied from the gas supply mechanism 104 into the chamber 103 according to the film forming process to be performed. Note that MFC1 to MFC4 shown in FIG. 3 are mass flow meters. The inside of the chamber 103 is adjusted to a required degree of vacuum by a vacuum pump (not shown). The substrate 2 for forming the A layer 11 and the B layer 12 is attached to the stage 105. The substrate 2 attached to the stage 105 is heated by the heater 106.

One sputtering evaporation source 102 is attached with at least one selected from TiB ₂ , SiC and B ₄ C as a target for forming the B layer 12. The other sputtering evaporation source 102 is attached with the same target or a different target selected from the above options.

A target for forming the A layer 11 and a target for the underlayer 13 are attached to the vacuum arc evaporation source 101 in preparation for forming the underlayer 13.
For example, one vacuum arc evaporation source 101 has a target made of any one of Ti _0.8 Si _0.2 , Ti _0.95 Si _0.05 , Ti _0.9 Si _0.1 , Ti _0.7 Si _0.3 , Ti _0.6 Si _0.4 and Ti _0.8 Si _0.2 B _0.1. It is attached.
Also, for example, the other vacuum arc evaporation source 101 includes Ti _0.5 Al _0.5 , Ti, Ti _0.9 Al _0.1 , Ti _0.1 Al _0.9 , Al _0.5 Cr _0.5 , Ti _0.2 Cr _0.2 Al _0.6 , Ti _0.5 Al _0.47 Si _0.03 , A target made of any one of Al _0.45 Cr _0.5 Si _0.05 , Ti _0.2 Cr _0.2 Al _0.55 Si _0.05 , Nb _0.5 Al _0.5 , Hf _0.7 Al _0.3 and (Ti _0.5 Al _0.5 ) C is attached.

  A bias voltage is applied to the stage 105 by the bias power source 107. This bias voltage is applied to the substrate 2 attached to the stage 105. The potential of the sputtering evaporation source 102 is controlled by the sputtering power source 108 so that atoms, ions, or clusters are generated from the sputtering evaporation source 102. The electric potential of the vacuum arc evaporation source 101 is controlled by the arc power source 109 so that atoms, ions, or clusters are generated from the vacuum arc evaporation source 101.

  The film forming apparatus 100 further includes a filament type ion source 110, a heating AC power source 111 used for AC heating of the ion source 110, and a discharge source for causing the ion source 110 to discharge. Although the DC power source 112 is provided, the multilayer hard coating 1 can be formed without using the ion source 110.

In forming the B layer 12, introduction of C and N into the B layer 12 is performed by decomposing a gas such as N ₂ and CH ₄ supplied from the gas supply mechanism 104 described above.

  The multilayer hard coating 1 according to the present invention described above is a slide that slides against other members such as cutting tools, molding dies, punches and other jigs and tools that require wear resistance. When formed on the surface of the substrate 2 such as a moving member or a cutting tool, the members 10 and 20 can have a long life because of excellent hardness and oxidation resistance.

  Hereinafter, the content of the present invention will be described more specifically with reference to examples in which the effects of the present invention have been confirmed.

  Various films described below were formed on the surface of the substrate. As the base material, a mirror-finished cemented carbide substrate (JIS-P type) and a cemented carbide insert (ADCT 1505 PDFR-HM grade IC28 manufactured by ISCAR) were used.

  The formation of the coating on the surface of the substrate is performed by using a plurality of arc ion plating evaporation sources (diameter 100 mmφ; hereinafter referred to as “AIP evaporation source”) and a plurality of sputtering evaporation sources (diameter 6 inches φ; hereinafter referred to as “SP evaporation source”). The film forming apparatus having a No. of Tables 1 to 3 is included in the AIP evaporation source of this film forming apparatus. A base layer target and / or an A layer target are attached in the combinations shown in Nos. 1 to 73, and Nos. The target for B layer was attached with the combination shown to 1-73. In forming the film, the AIP evaporation source for forming the A layer and the sputter evaporation source for forming the B layer were adjusted alternately.

  And the base layer, A layer, and B layer were formed with the thickness (nm) shown to Tables 4-6, the repetition frequency of A layer and B layer, and the sum total (nm) of the thickness of A layer and B layer. In addition, "-" in Tables 1-3 indicates that no target is attached, and "-" in Tables 4-6 indicates that no layer is formed. In addition, No. Nos. 48, 66, 72 and 73 formed films using a film forming apparatus provided with three sputtering evaporation sources.

These layers were formed as follows.
First, after the cleaned base material was introduced into the apparatus, the pressure in the chamber was reduced to 1 × 10 ⁻³ Pa or less, and the base material was heated to 500 ° C. Thereafter, sputter cleaning using Ar (argon) ions was performed. Next, N ₂ gas was introduced to bring the inside of the chamber to 4 Pa.

In this state, the underlayer was formed, or the A layer and the B layer were alternately formed as shown in Tables 4 to 6 without forming the underlayer.
The underlayer was formed by performing arc discharge at a current value of 150 A in the presence of N ₂ gas (in No. 62, a smaller amount of CH ₄ gas was introduced).
Then, Ar and nitrogen were introduced into the chamber at a flow rate ratio of 1: 1 (in the case of Nos. 15 to 17, a smaller amount of CH ₄ gas was introduced), the inside of the chamber was set to 4 Pa, and the base attached to the stage While rotating the material, arc discharge was performed for a short time to form a thin A layer, and sputter discharge was performed at 2 kW to form a thin B layer.
In forming the A layer and the B layer, the number of repetitions and the thickness of each layer were controlled by changing the rotation speed of the substrate to about 1 to 10 rpm or changing the input power to each evaporation source.

  No. The hardness was evaluated using a substrate made of cemented carbide having a film formed under the conditions described in Nos. 1 to 73. The life (tool life) as a tool was evaluated using the cemented carbide insert in which a film was formed under the conditions described in 1 to 73.

  The hardness was measured with a Vickers hardness meter (load 0.25 N).

The tool life is determined by a composite effect due to various factors such as the hardness and oxidation resistance of the film, the adhesion between the substrate and the film, and the strength of the substrate. Therefore, the tool life was evaluated by a cutting test. The cutting test was performed by attaching a cemented carbide insert with a coating to an end mill and dry turning the work material under the following conditions. The conditions for dry turning are as follows.
<Conditions for dry turning>
Work Material: AISI 316
Cutting speed: 180 m / minute feed: 0.14 mm / blade depth cutting: 4.5 mm
Lubrication: Dry

  Evaluation of hardness and tool life is shown in Tables 7-9. In Tables 7 to 9, no. The relative value in the case of using a cemented carbide insert formed with a film under the condition of 1 as a standard sample and assuming the tool life as 100% is shown. That is, the higher the relative value, the longer the life.

As shown in Tables 7-9, no. 7-11, 13-20, 23, 24, 27, 30, 31, 35, 38, 41, 44, 46-66, 68-73 satisfy the requirements of the present invention, so the hardness is high. No. which is a standard sample (conventional example) in which the layer and the B layer are not formed. The tool life was longer than 1.
In particular, no. In Nos. 49 to 66, 68 to 71, and 73, a base layer was formed on the surface of the base material, so that the hardness and the tool life were further improved. Among these, No. 49～51,53,55～66,68～71,73 _{is, M 1-y Al y (} B a C b N c O d) [ However, 0.05 ≦ y ≦ 0.8,0 ≦ a ≦ 0.2, 0 ≦ b ≦ 0.4, 0.5 ≦ c ≦ 1, 0 ≦ d ≦ 0.2, M is one selected from 4A group element, 5A group element, 6A group element and Si, Y As a result, the hardness and tool life were even better.

  In contrast, no. 1 to 6, 12, 21, 22, 25, 26, 28, 29, 32 to 34, 36, 37, 39, 40, 42, 43, 45, 67 satisfy at least one of the requirements of the present invention. The result was poor hardness and / or tool life.

Specifically, no. In Nos. 2 to 4, since the A layer was not formed and only the B layer was used, the hardness was equal to or lower than that and the tool life was short.
No. In No. 5, the B layer was not formed and only the A layer was used, so the tool life was short.
No. In No. 6, since the A layer did not contain Si (the atomic ratio of Si was 0), the hardness was low and the tool life was short.
No. No. 12, since the atomic ratio of Si in the A layer exceeded 0.4, the hardness was low and the tool life was short.
No. In No. 21, since the thickness of the A layer exceeded 100 nm, the hardness was low and the tool life was short.
No. No. 22 has a thickness of B layer of less than 2 nm. Compared to 1, tool life was also short.
No. In No. 25, since the thickness of the B layer exceeded 20 nm, the hardness was low and the tool life was short.

No. No. 26 has an atomic ratio of B in TiBN forming the B layer of less than 0.2. In No. 28, since the atomic ratio of B in TiBN forming the B layer exceeded 0.5, both the hardness was low and the tool life was short.
No. No. 29 has an atomic ratio of N in TiBN forming the B layer of less than 0.3. In No. 33, since the atomic ratio of N in TiBN forming the B layer exceeded 0.6, both the hardness was low and the tool life was short.
No. No. 32 had a low hardness and a short tool life because the atomic ratio of C in TiBCN forming the B layer exceeded 0.5.
No. No. 34 has an atomic ratio of C in SiCN forming the B layer of less than 0.2. In No. 36, since the atomic ratio of C in SiCN forming the B layer exceeded 0.5, both the hardness was low and the tool life was short.
No. 37, the atomic ratio of N in SiCN forming the B layer is less than 0.3. No. 39 had a low hardness and a short tool life because the atomic ratio of N in SiCN forming the B layer exceeded 0.5.
No. No. 40 does not contain C in the BCN forming the B layer (the atomic ratio of C is 0). No. 42 had a low hardness and a short tool life because the atomic ratio of C in the BCN forming the B layer exceeded 0.25.
No. No. 43 has an atomic ratio of N in the BCN forming the B layer of less than 0.3. In No. 45, since the atomic ratio of N in the BCN forming the B layer exceeded 0.55, both the hardness was low and the tool life was short.
No. No. 67 had a short tool life because the total thickness of the A layer and the B layer was less than 500 nm.

  As mentioned above, although the content of this invention was demonstrated in detail by the form and Example for inventing, the content of this invention is not limited to an above-described content. The contents of the present invention should be broadly interpreted based on the description of the scope of claims, and can be modified, changed, and the like without departing from the spirit of the present invention. Needless to say, the present invention includes such modifications and changes.

DESCRIPTION OF SYMBOLS 1 Multilayer hard film 11 A layer 12 B layer 13 Underlayer 2 Base material 10, 20 Member

Claims (8)

A multilayer hard coating formed on the surface of the substrate,
Ti _1-x Si _x (B _p C _q N _r ) [where 0.05 ≦ x ≦ 0.4, p ≧ 0, q ≧ 0, r> 0, p + q + r = 1], and a thickness of 100 nm or less An A layer having
Ti _1-agb B _a C _g N _b [where 0.2 ≦ a ≦ 0.5, 0.3 ≦ b ≦ 0.6, 0 ≦ g ≦ 0.5], Si _1-cd C _c N _d [However, 0.2 ≦ c ≦ 0.5,0.3 ≦ d ≦ 0.5], B 1-ef C e N f [ However, 0.03 ≦ e ≦ 0.25,0.3 ≦ f B layer consisting of one or more selected from ≦ 0.55] and having a thickness of 2 nm or more and 20 nm or less;
Are stacked several times,
Der total 500nm or more of the thickness of the laminated the A layer and the B layer is, and,
Multilayer hard coating wherein the A layer of the lowermost, wherein the Ru mania and bottom of the B layer and the surface. The multilayer hard coating according to claim 1,
Using a film forming apparatus having a vacuum arc evaporation source with a target for forming the A layer and a sputtering evaporation source with a target for forming the B layer in the same chamber, the vacuum arc is generated in the chamber. The substrate is rotated so as to pass a plurality of times in front of the evaporation source and the sputtering evaporation source, and the vacuum arc evaporation source and the sputtering evaporation source are simultaneously discharged to form the A layer and the B on the surface of the substrate. A multilayer hard film characterized by laminating a plurality of layers. The multilayer hard coating according to claim 1 or 2,
On the surface,
_{M 1-y Al y (B} a C b N c O d) [ However, 0.05 ≦ y ≦ 0.8,0 ≦ a ≦ 0.2,0 ≦ b ≦ 0.4,0.5 ≦ c ≦ 1, 0 ≦ d ≦ 0.2, M is an underlayer containing a group 4A element, group 5A element, group 6A element, one or more elements selected from Si and Y]. Characteristic multilayer hard coating. The multilayer hard coating according to claim 3,
A multilayer hard coating characterized in that the combination relating to the composition of the underlayer is AlCr (CN), TiAl (CN), TiCrAl (CN), AlCrSi (CN), TiAlSi (CN), or TiCrAlSi (CN). The multilayer hard coating according to claim 1,
A multilayer hard coating, wherein the substrate is a cutting tool and / or a sliding member. The multilayer hard coating according to claim 1,
A multilayer hard coating, wherein the substrate is a cutting tool. The multilayer hard coating according to claim 1,
A multilayer hard coating, wherein the substrate is a sliding member. The multilayer hard coating according to claim 1,
A multilayer hard coating, wherein the A layer and the B layer are alternately laminated.

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