阅读说明：本技术 从陶瓷靶沉积的立方富铝AlTiN涂层 (Cubic aluminum-rich AlTiN coatings deposited from ceramic targets ) 是由 西瓦·芬妮·库玛·亚拉曼奇利 丹尼斯·库拉波夫 佐佐木智也 久保田和幸 于 2019-11-11 设计创作，主要内容包括：本发明披露了一种用于生产富铝Al-(x)Ti-(1-x)N基薄膜的非反应性PVD涂覆工艺,该薄膜具有基于薄膜中的铝钛总量的大于75原子％的铝含量,并且该薄膜具有立方晶体结构和柱状微观结构,其中,陶瓷靶被用作富铝Al-(x)Ti-(1-x)N基薄膜的材料源。(The invention discloses a method for producing Al rich in aluminum x Ti 1‑x Non-reactive PVD coating process of N-based thin films with an aluminum content of more than 75 at% based on the total amount of aluminum and titanium in the thin film and with a cubic crystal structure and a columnar microstructure, wherein a ceramic target is used as the aluminum-rich Al x Ti 1‑x A source of N-based thin film material.)

1. Non-reactive PVD coating process for producing Al rich in aluminum_xTi_1-xAn N-based film having greater than 75 atom% based on the total amount of aluminum and titanium in the filmThe cubic crystal structure and the columnar microstructure, wherein a ceramic target is used as the aluminum-rich Al_xTi_1-xA source of N-based thin film material.

2. The coating process according to claim 1, wherein the ceramic target is formed in the form of a nitride and/or an oxide and/or a carbide.

3. Coating process according to claim 1 or 2, wherein a negative bias voltage is applied to the substrate to be coated, wherein the bias voltage applied to the substrate is less than 120V, preferably less than 100V, in particular less than 80V.

4. Coating process according to any one of the preceding claims, wherein the ceramic target comprises Al and Ti, wherein the aluminium content based on the total amount of aluminium and titanium within the target is more than 50 atomic%.

5. The coating process according to any one of the preceding claims, wherein the coating is performed without using a reactive gas.

6. Coating process according to any one of the preceding claims, wherein AlN₈₀TiN₂₀Is used as the aluminum-rich Al_xTi_1-xA target material of an N-based film.

7. Coating process according to one of the preceding claims, wherein a sputtering technique, in particular a HiPIMS or arc PVD coating process, is used as the non-reactive PVD coating process.

8. Coating process according to any one of the preceding claims, wherein the ceramic target also comprises other elements than aluminium and titanium, preferably transition metals, more preferably Zr and/or Nb and/or Ta.

9. The coating process according to one of the preceding claims,a plurality of Al-rich_xTi_1-xThe N-based films are deposited on top of each other to produce a multilayer film.

10. Coating process according to any one of the preceding claims, wherein the substrate temperature is between 100 ℃ and 350 ℃, preferably between 150 ℃ and 250 ℃, in particular between 200 ℃ and 250 ℃.

11. Aluminum-rich Al_xTi_1-xN-based thin film having an aluminum content of more than 75 atomic% based on the total amount of aluminum and titanium in the thin film, a cubic crystal structure and a columnar microstructure, producible by the process according to one of claims 1 to 10.

12. The aluminum-rich Al of claim 11_xTi_1-xN-based thin films, wherein the layer thickness is greater than 200nm, preferably greater than 300nm, in particular greater than 500 nm.

13. The aluminum-rich Al of claim 11 or 12_xTi_1-xAn N-based film, wherein the film has a surface roughness R of less than 0.8 μm, preferably less than 0.7 μm_z。

14. The aluminum-rich Al of any of claims 11 to 13_xTi_1-xAn N-based thin film, wherein the cubic structure comprises grains having an average grain size of more than 15 nm.

15. The aluminum-rich Al of any of claims 11 to 14_xTi_1-xAn N-based thin film, wherein the thin film has an aluminum content of greater than 76 atomic%, preferably greater than 80 atomic%, more preferably greater than 85 atomic%, based on the total amount of aluminum and titanium in the thin film.

16. The aluminum-rich Al of any of claims 11 to 15_xTi_1-xAn N-based thin film, wherein the thin film contains a metal element other than aluminum and titanium, preferably a transition metal, more preferablyIs Zr and/or Nb and/or Ta.

17. The aluminum-rich Al of any of claims 11 to 16_xTi_1-xAn N-based film, wherein the film is formed by at least two aluminum-rich Al films deposited in an overlapping manner_xTi_1-xAn N-based thin film is formed in a multilayer structure.

18. Use of a structure according to any of claims 11 to 17 for the manufacture of tools, in particular cutting tools or shaping tools.

Technical Field

The invention relates to aluminum-rich Al_xTi_l-xDeposition of an N coating having an aluminum content with x greater than 0.75 (in atomic percent fraction) and exhibiting cubic phases with columnar structures, wherein a ceramic target is used as a material source for coating deposition.

The invention allows the synthesis of aluminium-rich AlTiN coatings using PVD methods with an aluminium content higher than 75 at%, and even higher than 78 at% (considering the sum of the aluminium content and the titanium content as 100%; thus when for example Al is expressed_xTi_1-xThe aluminum content in the N coating is 80 atomic%, which means that x ═ 0.80), and the columnar microstructure is reliably exhibited.

Background

Currently available aluminum-rich AlTiN coatings (thin film type) with aluminum contents higher than 75 atomic% and showing cubic crystal structure and columnar microstructure are known to be synthesized by LP-CVD process. These types of coatings have gained considerable attention because of their compatibility with coatings having a lower aluminum content, such as Al₀.₆₇Ti_0.33N coatings are expected to show superior wear protection. This excellence is expected for cutting tools, forming tools and components in a wide range of applications.

The term "film" in the context of the present invention should be understood to mean a coating or layer having a thickness in the range of nanometers to several micrometers.

The term "aluminum-rich AlTiN" in the context of the present invention should be understood to mean an AlTiN coating or layer which contains an aluminum content which is higher than the titanium content. In particular, the invention is then intended to mean an aluminium-rich AlTiN coating or layer having an Al/Ti ratio (aluminium content in atomic percent/titanium content in atomic percent) greater than 3.

Historically, it has been known that metastable cubic phases with up to 70 atomic percent of aluminum in AlTiN films can be grown using PVD methods.

EP2247772B1 discloses a multilayer structure comprising two different layers, specifically comprising cubic structures (Ti)_l-xAlx) N layers, where 0.3 < x < 0.95, and MeN layers of cubic structure, where Me is one or more of the following metal elements: ti, Zr, Hf, V, Nb, Ta, Mo and Al. But according to EP2247772B1 (Ti) contained in a multilayer structure_1-xAl_x) The thickness of the N layer is less than 20 nm.

EP2926930B1 discloses a method for depositing a hard coating (Al)_xTi_1-x) Method of N (0.5. ltoreq. x. ltoreq.0.8), but (Al)_xTi_1-x) The N-coating comprises both cubic and hexagonal phases.

US10184187B2 discloses a method for generating (M)_1-xAl_xN) layer, wherein x is 0.7-0.85, but contains a wurtzite phase, wherein the wurtzite phase content is between 1 and 35 wt.% (in wt.%).

Furthermore, WO2019/048507a1 discloses a method of growing cubic aluminum-rich AlTiN. Here, the inventors have tested the possibility of synthesizing aluminum-rich altins with an aluminum content higher than 75 atomic% using a reactive PVD process, where the HiPIMS technique is employed by adjusting a predetermined set of process parameters within a specific range. These process parameters include, for example, power density and pulse length. According to the reactive PVD process as described in WO2019/048507a1, a very important parameter is the nitrogen partial pressure. Cubic phases have been shown to form only within a narrow range of values of nitrogen partial pressure. If the nitrogen pressure is lower or higher than a value within this specific range, an undesirable hexagonal phase is formed. This complicates the process because the optimum partial pressure must always be calibrated for each specific target used and also depends on target weight or thickness. It means that the amount of nitrogen consumption and thus the partial pressure of nitrogen required to produce the desired coating will vary depending on the target lifetime. In addition, high (in absolute value) negative substrate bias voltages are required to form cubic phases (e.g., greater than 120V) to produce Al₈₀Ti₂₀And N is added. This is achieved byThe use of such high bias voltage values results in films that when grown exhibit very high internal stresses (typically inherent compressive stresses if deposited by PVD), which can cause peeling of the coating, especially due to increased coating thickness.

The use of ceramic targets is circumvented as their use is known to lead to cracking during target vaporization via sputtering or arc discharge processes due to their inherent brittleness and to influence repeated thermal cycling of the target. Cracked targets cannot be used in arc discharge processes because the arc will penetrate the crack and cause damage to the deposition chamber components. Also, cracked targets cannot be properly used for the sputtering process.

Objects of the invention

It is an object of the present invention to mitigate or overcome one or more of the difficulties associated with the prior art. In particular, it is an object of the present invention to provide a PVD coating process which allows cubic phase (Al) to be carried out in a simple, reliable and environmentally friendly manner_xTi_1-x) And (3) producing the aluminum-rich film with the N-type structure.

Specification

The inventors have determined not to use a target in which the metallic AlTi target contains reactive N₂Is evaporated or sputtered, but a non-reactive PVD process is used, where a ceramic AlTiN target is sputtered or evaporated without any reactive gas in the coating chamber.

Thus, in a first aspect of the invention, a method for producing Al rich in aluminum is disclosed_xTi_1-xNon-reactive PVD coating process of N-based thin films with an aluminum content of more than 75 atomic% based on the total amount of aluminum and titanium in the thin film and with a cubic crystal structure and a columnar microstructure, wherein a ceramic target is used as for the aluminum-rich Al_xTi₁-_xA source of N-based thin film material.

By employing the configuration of the present invention, it is unexpectedly possible to produce aluminum-rich AlTiN films grown in cubic phase, but with a larger parameter window and thus a broader parameter effective range, including a much lower substrate bias voltage than when using a reactive process involving a metal target and nitrogen as the reactive gas.

The cubic crystal structure and the columnar microstructure according to the present invention mean a pure cubic structure and a pure columnar microstructure are preferred. However, this does not mean that small or trace amounts, preferably less than 1 atomic%, relative to the total mass of aluminum titanium in the film, may also have different phases or structures. The present invention further defines a non-reactive coating process, preferably a coating process in which a bias of less than 120V is applied to the substrate to prevent cracking (in this regard, the term "cracking" is used to refer to peeling or delamination of the coating).

The invention also relates to the use of a ceramic target that also contains other elements for producing A1TiN coatings (AlTiN films) containing other elements or components. Thus, in the example of the first aspect, the ceramic target may also comprise other components, such as oxides, carbides, silicides or borides, in addition to nitrides.

In another example of the first aspect, a negative bias voltage is applied to the substrate to be coated, wherein the bias voltage applied to the substrate is less than 120V, preferably less than 100V, especially less than 80V.

In another example of the first aspect, the ceramic target comprises Al and Ti, wherein the aluminum content based on the total amount of aluminum and titanium within the target is greater than 50 atomic%.

In another example of the first aspect, the coating is performed in the absence of a reactive gas. Since the process according to the invention does not require any nitrogen gas flow to be injected in the coating chamber, the process is stable and relatively simple, with a wide parameter effective range.

In another example of the first aspect, AlN₈₀TiN₂₀Is used as Al rich in Al_xTi_1-xA target material of an N-based film. According to this example, stable discharge was obtained although the AlN phase portion was predominant and it had semiconductive properties. In addition, coating growth in cubic form at lower substrate bias can be produced, for example, by using a-80V bias, Al can be produced with aluminum content up to x-0.78_xTi₁-xN. Unexpectedly, the inherent stresses in such coatings are much lower than when using reactive PVD methods. Although ceramic targets are known to suffer from cracking during sputtering and arc discharge because of their inherent brittleness and repeated thermal cycling, the process of the present invention can be unexpectedly performed without target cracking by using targets having high AlN content (greater than 50 atomic%). In particular, AlN as compared with AlN having a composition of₅₀TiN₅₀Has the component AlN₈₀TiN₂₀Does not crack and allows a stable and reproducible coating process to be performed. In other words, cracks may be suppressed by using higher AlN content in the AlNTiN target, especially when using AlN₈₀TiN₂₀Good results (no cracks) were observed with ceramic targets.

In another example of the first aspect, a sputtering technique, in particular a HiPIMS or arc PVD coating process, is used as the non-reactive PVD coating process. In particular the above-mentioned crack suppression (e.g. by using an AlNTiN ceramic target having an AlN content higher than the TiN content, e.g. AlN₈₀TiN₂₀) It is possible to carry out the deposition of a coating of the coating according to the invention from a ceramic target using the arc PVD technique.

In another example of the first aspect, the ceramic target further comprises other elements, such as other metallic elements than aluminum and titanium, preferably any other transition metal, more preferably Zr and/or Nb and/or Ta.

In another example of the first aspect, the plurality of aluminum-rich AlxTi₁-xN-based thin films are deposited on top of each other to manufacture a multilayer thin film.

In another example of the first aspect, the substrate temperature is between 100 ℃ and 350 ℃, preferably between 150 ℃ and 250 ℃, in particular between 200 ℃ and 250 ℃.

In a second aspect, an aluminum-rich Al is disclosed_xTi_1-xAn N-based thin film having an aluminum content of more than 75 atomic% based on the total amount of aluminum and titanium in the thin film, a cubic crystal structure and a columnar microstructure, and can be produced by the above-described process.

In addition to the second aspectIn one example, Al is rich in Al_xTi_1-xThe thickness of the N-based film is 200nm or more, preferably 300nm or more, particularly 500nm or more.

According to a preferred embodiment of the invention, Al is rich in aluminum_xTi_1-xThe thickness of the N-based thin film is between 0.5 μm and 20 μm.

"aluminum-rich Al" in the context of the present invention_xTi_1-xN-based film "is to be understood as a coating comprising at least one aluminum-rich Al_xTi_1-xN coating, where x > 0.75, or a coating comprising a coating predominantly containing Al_xTi_1-xAt least one layer of N, wherein x > 0.75, wherein, in both cases, the thickness of said at least one layer is preferably 200nm or more. In addition, Al is rich in aluminum_xTi_1-xThe N-based thin film may be formed of one layer and thus a single layer, or may be formed of more than one layer and thus a plurality of layers.

In another example of the second aspect, the film has a surface roughness R7 of less than 0.8 μm, preferably less than 0.7 μm.

In another example of the second aspect, the cubic structure comprises grains having an average grain size in excess of 15 nm.

In another example of the second aspect, the Al-rich Al is based on the total amount of Al and ti in the film_xTi_1-xThe N-based thin film has an aluminum content of greater than 76 atomic%, preferably greater than 80 atomic%, more preferably greater than 85 atomic%.

In another example of the second aspect, the aluminum-rich Al_xTi_1-xThe N-based thin film contains other metal elements than aluminum and titanium, preferably a transition metal, more preferably Zr and/or Nb and/or Ta.

In another example of the second aspect, the film may comprise at least two aluminum-rich Al layers deposited one on top of the other_xTi_1-xThe N-based thin film is formed in a multilayer structure.

In a third aspect, a use of the aforementioned structure for manufacturing a tool, in particular a cutting tool or a shaping tool, is disclosed. The above description should not be taken as limiting the invention, but merely as exemplifications for a more detailed understanding of the invention.

Detailed Description

Fig. 1 shows a schematic diagram (a) of the changes in w-AlN fraction, nitrogen consumption (growth rate/unit time) in relation to nitrogen partial pressure, and XRD spectra (b) at different nitrogen partial pressures.

FIG. 2 shows a schematic representation of the w-AlN fraction in relation to the substrate bias voltage (a), and from Al at different substrate bias voltages₈₀Ti₂₀XRD spectrum (b) of the AlTiN coating synthesized by the target.

Fig. 3 shows a schematic diagram of a combined deposition setup used to grow a film from a ceramic target.

Fig. 4 shows an optical photograph and SEM micrograph of the TiNAlN ceramic target.

Figure 5.1 shows the film grown using a combinatorial approach to ceramic targets.

Figure 5.2 shows the film grown using a combinatorial approach to ceramic targets.

Figure 5.3 shows a film grown using a ceramic target.

Figure 6 shows films grown using metal and ceramic targets.

FIG. 7 illustrates the use of AlN₇₇TiN₂₃Film grown on the target.

Detailed Description

The following drawings are intended to aid in the understanding of the invention and are not intended to limit the invention.

FIG. 1 shows the partial pressure of nitrogen versus Al₈₀Ti₂₀Influence of the structural evolution of the AlTiN coating synthesized with a metal target at a substrate temperature of 200 ℃ and an argon partial pressure of 0.2 Pa. (a) Fractional w-AlN related to partial pressure of nitrogen, N₂The consumption (growth rate/unit time) varied. The noted text represents the reactive gas partial pressures corresponding to the metallic, transitional, and combined sputtering modes. (b) The XRD spectra at different partial pressures of nitrogen, 0.09, 0.11, 0.13 and 0.15Pa, correspond to 1, 2, 3 and 4, respectively.

FIG. 2 shows the effect of substrate bias voltage on the structural evolution of AlTiN alloys using metal targets. (a) w-AlN fraction related to substrate bias voltage. Data extracted from the XRD spectrum (F w-AlN: wurtzite phase intensity/Sigma (cubic)Phase strength + wurtzite phase strength). (b) From Al at different substrate bias voltages 80V, 120V and 200V₈₀Ti₂₀XRD spectrum of the target synthesized AlTiN coating.

Fig. 3 shows a schematic diagram of a combinatorial deposition setup for growing a film from a ceramic target.

Fig. 4 shows optical and SEM micrographs of the TiNAlN ceramic target, as received and after 6 depositions. Note that TiN₅₀AlN₅₀The target shows cracks, while TiN₂₀AlN₈₀Such cracks are not shown after repeating the process several times.

Figure 5.1 shows the film grown using the combined approach of ceramic targets. (a) Batch processing parameters, (b) membrane composition at different locations of the substrate support, and (c) X-SEM micrographs and XRD patterns. And annotating: s < - > substrate peak, C < - > cubic peak and W < - > wurtzite phase. As shown in fig. 5.1, the following coating parameters were used: the power density is 1kW/cm²Pulse time 5ms, nitrogen partial pressure 0Pa (which corresponds to nitrogen flow 0sccm), and argon flow 40 sccm.

Figure 5.2 shows the film grown using the combined approach of ceramic targets. (a) Batch processing parameters, (b) membrane composition at different locations of the substrate support, and (c) X-SEM micrographs and XRD patterns. And annotating: s < - > substrate peak, C < - > cubic peak and W < - > wurtzite phase. As shown in fig. 5.2, the following coating parameters were used: the power density is 1kW/cm²Pulse time 5ms, nitrogen partial pressure 0Pa (nitrogen flow 0sccm), and argon flow 300 sccm.

Figure 5.3 shows films grown using ceramic targets, (a) batch parameters, (b) film composition at different locations on the substrate support, and (c) X-SEM micrographs and XRD patterns. And annotating: s- > base material peak, C- > cubic phase, W- > wurtzite phase. As shown in fig. 5.3, the following coating parameters were used: the power density is 1kW/cm²Pulse time 5ms, nitrogen partial pressure 0Pa (nitrogen flow rate: 0sccm), and argon partial pressure 60 Pa.

In the examples given in fig. 5.1, 5.2 and 5.3, the substrate to be coated is held by a gripper system placed in an Ingenia S3p type coating machine manufactured by Oerlikon Balzers. For these examples, a clamping system comprising two rotatable clamping members is used. A first rotatable gripper part, called turntable, is placed in the middle of the coating chamber in a known manner to produce a first rotation. On the turntable, a second rotatable gripper part is mounted in a known manner to cause a second rotation. The substrate to be coated is held in a second rotatable chuck member. The rotational speed of the turntable is 30 seconds per revolution, as shown in the respective fig. 5.1, 5.2 and 5.3. However, the type of coater and fixture system used should not be construed as limiting the invention. Likewise, the coating parameters used for the examples shown in fig. 5.1, 5.2 and 5.3 should not be understood as limiting the invention.

Figure 6 shows films grown using metal and ceramic targets under three different conditions. As shown in fig. 6, the conditions used in the upstream are: a mixture of argon pressure 0.1Pa and nitrogen pressure 0.04Pa, a temperature of 200 ℃ and a voltage of 150V. However, the conditions used in the middle row are: 60s argon flow, 300 ℃ temperature and 150V voltage. The conditions used in the downlink were: 40s argon flow, 300 ℃ temperature and 80V voltage. Note that cubic phase can be obtained with ceramic targets at aluminum concentrations as high as 78 atomic%, using only 80V bias. For metallic targets, high bias voltages above 120V are required to grow cubic phases.

The micrographs from left to right are: lower, middle and upper chambers.

Based on the above example and combinatorial design experiments, a ceramic target with 77 atomic% Al was selected to test the homogeneity of cubic phase growth along the length of the turntable.

An additional feature of coatings grown according to this method is a relatively low surface roughness with a value Ra of 0.03. + -. 0.01. mu.m and Rz of 0.6. + -. 0.01. mu.m. Fig. 7 below shows the measured profiles of the coating surfaces before (a) and after (b) the cano milling, and (c) the coatings grown using the method of the present invention.