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Article

Study of the Nature of the Destruction of Coatings Based on the ZrN System Deposited on a Titanium Alloy Substrate

by
Alexander Metel
1,
Alexey Vereschaka
2,*,
Catherine Sotova
1,
Anton Seleznev
1,
Nikolay Sitnikov
3,
Filipp Milovich
4,
Kirill Makarevich
5 and
Sergey Grigoriev
1
1
Department of High-Efficiency Machining Technologies, Moscow State University of Technology “STANKIN”, Vadkovsky Lane 3a, 127055 Moscow, Russia
2
Institute of Design and Technological Informatics of the Russian Academy of Sciences (IDTI RAS), Vadkovsky Lane 18a, 127055 Moscow, Russia
3
The State Scientific Centre Keldysh Research Center, Onezhskaya St., 8, 125438 Moscow, Russia
4
Materials Science and Metallurgy Shared Use Research and Development Center, National University of Science and Technology “MISiS”, Leninsky prospect 4, 119049 Moscow, Russia
5
Federal State Budget Educational Institution of Higher Education, MIREA—Russian Technological University, Vernadsky Avenue, 78, 119454 Moscow, Russia
*
Author to whom correspondence should be addressed.
Technologies 2024, 12(10), 179; https://doi.org/10.3390/technologies12100179
Submission received: 18 July 2024 / Revised: 18 September 2024 / Accepted: 27 September 2024 / Published: 30 September 2024
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Abstract

:
The fracture strength was compared in a scratch test of coatings based on the ZrN system with the introduction of Ti, Nb and Hf, which were deposited on a titanium alloy substrate. The coatings were deposited using Controlled Accelerated Arc (CAA-PVD) technology. In coatings that simultaneously include Zr and Ti, a nanolayer structure is formed, while in coatings without Ti, the formation of a monolithic single-layer structure is observed. The comparison was carried out according to two parameters: adhesion strength to the substrate and overall coating strength. The (Zr,Hf)N coating showed better resistance to destruction, but had worse adhesion to the substrate. As a result, although the coating is retained directly in the scribing groove, a large area of delamination and destruction is formed around the groove. The (Ti,Zr,Nb)N coating, with its somewhat lower strength, has a high adhesion to the substrate; no noticeable delamination is observed along the groove boundary. In this paper, not only is the fracture resistance of various coatings deposited on a titanium alloy substrate compared, but the nature of this fracture is also investigated depending on the composition of the coatings.

1. Introduction

Products made of titanium and its alloys are widely used in various areas of modern industry. These materials are actively used in aircraft and rocket engineering, medicine and power engineering [1,2,3,4,5,6]. The intensive use of titanium alloys as structural materials is associated with such properties as a high strength with a relatively low specific gravity, good corrosion resistance (due to the spontaneously forming oxide film) and reasonable cost. During operation, parts made of titanium alloys experience various external influences, leading to their wear and, ultimately, failure. Such impacts include abrasive and cavitation wear, as well as corrosion. Abrasive wear is associated with the impact of particles that have greater hardness than titanium (for example, sand particles). Wear also occurs during the operation of friction pairs as a result of the formation and rupture of adhesive interaction zones. The natural oxide film formed on the surface of titanium is easily destroyed by friction due to high specific loads due to the high ductility of titanium [7,8]. The presence of zones with a destroyed oxide film increases the tendency for the possibility of active adhesive interaction to occur in local areas of contact between two surfaces. This high propensity for adhesion is also facilitated by the relatively low elastic modulus and low thermal conductivity of titanium and its alloys. Titanium alloys are prone to significant strengthening during plastic deformation; therefore, upon contact in a friction pair, a strengthened surface layer can form [9,10]. In addition to the above factors, it is worth noting that due to heating during friction, the diffusion of nitrogen and oxygen from the environment into the surface layer can be observed, due to which this layer is also strengthened. Due to the influence of these factors, damage on the contact surfaces of products made of titanium alloys can be quite deep and accompanied by tearouts of material fragments and the formation of adhesives, which, in turn, increase adhesion between the contact surfaces and intensify the wear process [10]. When titanium parts work in tandem with parts made of other metals and alloys, titanium sticks to the surface of the harder material, which increases the coefficient of friction and wear rate. When titanium works in tandem with a softer material, soft material sticks to the surface of titanium parts, which also leads to an increase in the coefficient of friction and increased wear [10].
One of the effective methods for eliminating these problems is the deposition of modifying coatings on the working surfaces of parts made of titanium alloys. The application Ьщысщцб of such coatings can extend the service life of parts made of titanium alloys and increase their reliability. These coatings must have the following properties:
  • High hardness and wear resistance;
  • Corrosion resistance and chemical passivity;
  • High strength of the adhesive bond with the titanium substrate;
  • Low adhesion to the contacting material in a tribological pair;
  • High strength.
One of the possible coating materials that meets the listed requirements is zirconium nitride (ZrN). The introduction of additional elements such as titanium (Ti), niobium (Nb) and hafnium (Hf) into the ZrN composition can further improve its properties. The ZrN coating itself has been studied in sufficient detail; its properties are described in a number of publications. Good wear-resistant properties and corrosion resistance in various environments are noted [11,12,13,14,15]. Another useful property of the ZrN coating is its strength and crack resistance, which make it possible to effectively resist brittle fracture [16,17,18,19,20], while this coating is characterized by fairly high heat resistance [21]. There is experience in the successful use of a ZrN coating to increase the wear resistance and corrosion resistance of parts made of various materials: stainless steel [17,18] and magnesium alloys [16], as well as titanium alloys of various compositions [14,22,23,24,25]. While the ZrN coating mainly has an fcc structure [26,27,28], under certain deposition conditions the formation of w-ZrN and h-ZrN phases is also observed [29]. The key parameters affecting the structure and properties of the ZrN coating include nitrogen pressure in the chamber [12,30,31] and substrate temperature [32,33]. Further improvement in the properties of the coating based on the ZrN system is ensured by increasing the complexity of its composition. The effect of the introduction of elements such as hafnium (Hf) and niobium (Nb) on the properties of the coating has been studied [34,35,36,37,38]. It was found that the introduction of Hf into the ZrN structure provides a noticeable increase in wear resistance and corrosion resistance [34,35,36,37,38,39,40]. In this case, an Hf content of more than 20 at% can reduce the oxidative resistance of the coating [41]. The introduction of Nb into the ZrN composition provides a similar effect. At the same time, in addition to increasing wear resistance, a decrease in the friction coefficient is also noted [37,42,43,44]. The low coefficient of friction may be due to the reduction in grain size and surface roughness [44]. The introduction of Nb increases the heat resistance of the coating [45,46]. A decrease in the level of residual stresses was also noted [47]. It was found that a high Nb content in the coating reduces corrosion resistance [37].
Another element, the introduction of which into the composition of the ZrN coating can improve its properties, is titanium (Ti). With the introduction of Ti, wear resistance increases, and the friction coefficient decreases [48,49,50,51,52,53]. Anti-corrosion properties are also improved [54,55]. A ZrN coating with introduced Ti has a better hardness and wear resistance not only compared to the standard ZrN coating, but also compared to the TiN coating [51,56,57,58], but it has a higher level of residual stresses [59].
Due to the difference in the mechanical properties of the coating and the substrate, it is rational to use a coating structure that includes a metal adhesion layer, which allows for good adhesion to both the titanium substrate and the coating [60,61,62,63].
The objective of this study was to compare an important parameter of the coatings, resistance to destruction during the scratch test. Coatings based on the ZrN system were selected, also including Hf, Nb and Ti in various combinations. In this way, ZrN, (Zr,Ti)N, (Zr,Hf)N, (Zr,Nb)N, (Ti,Zr,Hf)N and (Ti,Zr,Nb)N coatings deposited on titanium alloy Ti-6Al-4V were studied, an alloy which is widely used in various technological solutions. The scratch test was chosen as a research method, allowing one to evaluate not only the adhesion between the coating and the substrate, but also to study the nature of the destruction and strength characteristics of the coating.

2. Materials and Methods

For the deposition of coatings, a modernized VIT-2 ion-plasma unit was used (IDTI RAS—MSUT “STANKIN”, Moscow, Russia) [42,45,46,64,65,66,67,68]. Special Controlled Accelerated Arc (CAA-PVD) evaporators were used to reduce the formation of the microparticle phase [69,70,71]. The cathodes had the following compositions: Zr (99.98%) and Ti (99.99%), Zr-Nb (50:50%) and Zr-Hf (50:50%).
Before the technological process of coating deposition, the samples were prepared as follows:
  • Washing with ultrasonic stimulation in a special solution (about 45 min);
  • Washing in a stream of purified water (about 10 min);
  • Drying with a stream of purified air (about 15 min).
During coating deposition, the arc current of the titanium and zirconium cathodes was, respectively, 75 and 80 A. The arc current of the Zr-Nb (50:50%) and Zr-Hf (50:50%) cathodes was, respectively, 85 and 90 A. Other parameters of the deposition process for all samples were as follows: nitrogen pressure 0.42 Pa, voltage on substrate –150 V, tool rotation speed 0.7 rpm.
The studies were carried out using a scanning electron microscope (SEM) Carl Zeiss (Oberkochen, Baden-Württemberg, Germany) EVO 50, with EDX system X-Max—80 mm2 (OXFORD Instruments, Abingdon, Oxfordshire, UK). Hardness was measured on a nanotester SV-500 (Micro Scratch, Nanovea, Irvine, CA, USA), using a Berkovich indenter, at a maximum load of 20 mN. The average values were determined based on the results of 20 measurements.
The scratch test was carried out using a CB-500 tester (Micro Scratch, Nanovea, Irvine, CA, USA) in accordance with the ASTM C1624-22 method [72], measuring the load from 0 to 40 N.
Traditionally, the scratch test method is used to determine the adhesion strength of a coating and a substrate. However, this method also allows one to study the overall strength of the coating under the influence of a hard and sharp indenter. To some extent, this method makes it possible to simulate abrasive wear under the influence of small-sized and hard particles (for example, sand particles). Studying the nature of coating destruction under such an impact can be useful in determining the scope of application of coatings and their strength under various conditions of mechanical impact.
Coatings with a multilayer structure are destroyed during a scratch test by a mechanism that differs significantly from the destruction of monolayer coatings [73,74]. The interfaces between the layers provide a cohesive bond and can be destroyed by an indenter, while providing better resistance to destruction [74,75,76,77]. Thus, when scribing multilayer coatings, there is a repeated rupture of the cohesive bond between the nanolayers, and the acoustic emission signal that occurs during such a rupture is difficult to differentiate from that occurring when the entire coating is torn off the substrate. Thus, when analyzing the nature of destruction of multilayer coatings during a scratch test, it is worth considering first of all the results of visual observation, and not the acoustic emission signal. At the same time, the acoustic emission signal continues to play a certain role, allowing a better understanding of the nature of the coating destruction.

3. Results

Figure 1a shows the structures of the studied coatings. Coatings containing both titanium and zirconium have a nanolayer structure, while coatings that do not contain titanium have a monolithic structure. The coating thickness is 1.4–1.5 µm. The surface morphology of the coatings (Figure 1b) is quite identical, with a small amount of microparticles observed.
The (Zr,Hf)N and (Ti,Zr,Nb)N coatings have the highest hardness (HV 3350 ± 120 and HV 3110 ± 135 respectively). The average values among the studied coatings are for ZrN (HV 2993 ± 145), (Ti,Zr,Hf)N (HV 2860 ± 95) and (Zr,Ti)N (HV 2727 ± 86). The least hard coating was (Zr,Nb)N (HV 2336 ± 115).
Below are the quantitative results of the study of the coatings using the scratch test method (Figure 2). The values of the critical points LC1 and LC2 were determined by comparing the acoustic emission data and the results of studying the scribe groove using SEM. The (Ti,Zr,Nb)N and (Zr,Hf)N coatings showed the greatest strength, and the (Zr,Ti)N, (Ti,Zr,Hf)N and (Zr,Nb)N coatings deteriorated the fastest.
It is worth noting the features of the practical significance of points LC1 and LC2 for coatings with a multilayer structure. Point LC1 characterizes the load at which the first signs of coating destruction appear. For multilayer coatings, this usually means the beginning of the destruction of cohesive bonds between individual layers. In this case, the coating usually retains its operability, continuing to perform its functional properties. Point LC2 characterizes the complete destruction of the coating in the scribing groove area. In this case, the coating is completely lost and the indenter moves directly into contact with the substrate.
The strength of the coating is affected not only by the composition and thickness of the adhesive sublayer (for the (Zr,Hf)N and (Ti,Zr,Hf)N coatings, it is the same—Zr, Hf), but also by the properties of the main coating layer. The best resistance to destruction is shown by coatings that also have greater hardness. The values of the critical fracture load LC2 for the samples under study do not exceed 20 N, which is significantly lower compared to coatings deposited on a carbide or silicon substrate. Since the titanium substrate has relatively low hardness and good ductility, a zone of plastic deformation is formed during the scratch test. The coating deposited on the substrate is destroyed due to active crack formation.

3.1. ZrN Coating

This coating has an average critical fracture value among the studied samples (LC2 = 15 N). Figure 3 shows a general view of the scribing groove and a view of the characteristic areas of destruction of the ZrN coating. When the critical load LC2 is reached, the coating actively collapses, with the formation of chips along the scribing groove (Figure 3b–e). In addition to cracking, the peeling of coating fragments from the substrate is also observed (Figure 3d,e). In this case, the broken fragments of the coating are pressed into the substrate material under the influence of a moving indenter (Figure 3c,d). The dominant mechanism of destruction of this coating is spallation failure [78].
Consider a cross-section of a coated sample taken perpendicular to the direction of the scribing groove in the area close to point LC2 (Figure 4). In the areas immediately adjacent to the scribing groove (Figure 4b,c,e,f), the peeling of coating fragments from the substrate is observed. In this case, the coating in these areas is affected by shear forces (indicated by arrows), while the coating in the groove itself is affected predominantly by compressive stresses. Fragments of the coating are pressed into the substrate material (Figure 4c). In areas slightly further from the scribing groove, the coating can maintain a strong adhesive bond to the substrate even with noticeable plastic deformations (Figure 4c,d). Delamination of the coating from the substrate is accompanied by the chipping of nanometric fragments of the coating from the interface with the substrate (Figure 4b,f). The right inset shows how the coating is formed, covering the initial defect of the substrate surface (fragment B3 in Figure 4c).

3.2. (Zr,Ti)N Coating

The (Zr,Ti)N coating showed low resistance to destruction in the scratch test (Figure 5). Even at low loads, peeling of the coating from the substrate is observed along the boundaries of the scribing groove (Figure 5b,f). Directly in the furrow, the coating cracks, and the coating elements are pressed into the substrate material. With increasing loads in the furrow, the coating is completely destroyed, and along the edges of the furrow, peeling of the coating from the substrate is observed (Figure 5c–e). Despite the peaks of acoustic emission at loads of 7…9 N, no real destruction of the coating is observed; this surge in emissions may be associated with the rupture of the cohesive bond between the coating nanolayers (including in the inner region of the coating, without delaminations reaching the surface [79]).
The indenter, when moving, forms a field of compressive stresses in the coating, which is necessary to destroy the adhesive bonds with the substrate. At the same time, a field of bending stresses is formed, which can be high enough to cause cohesive destruction of the coating before the destruction of the adhesive bond with the substrate occurs [80]. The dominant mechanism of destruction of this coating is tension failure [78].
An analysis of a transverse section made perpendicular to the scribing groove in the area where the critical load LC1 is reached confirms the rather low adhesion between the coating and the substrate (Figure 6a,b). Extended delamination can be seen, and in the area of the interface between the coating and the substrate, coloring of the coating is observed with the formation of a nanometric-sized fragment. A similar type of destruction is also observed in samples with ZrN and (Ti,Zr,Hf)N coatings.

3.3. (Zr,Hf)N Coating

The nature of destruction of the (Zr,Hf)N coating is characterized by a certain duality. On the one hand, the coating remains in the scribing furrow up to the maximum load (20 N). On the other hand, already at insignificant (about 4 N) loads on the surface of the coating, the formation of cracks is observed (Figure 7b), and at a load of the order of 7 N, peeling of coating fragments from the substrate begins along the boundaries of the furrow, while in the furrow itself such peelings do not occur. Thus, assessing the strength of this coating during a scratch test is somewhat difficult. From the point of view of acoustic emissions, the destruction of this coating (point LC2) occurs at a load of 18 N. At this load, the coating in the groove itself is preserved (that is, it has a high compressive strength). But extensive areas of destruction and delamination form along the furrow. These areas are the most extensive among all the studied coatings. One can make an assumption (which requires additional research) that the (Zr,Hf)N coating itself has a fairly high strength, but rather low adhesion to the substrate. This coating is characterized by a destruction mechanism in the form of tension failure in combination with spallation failure [78].
Thus, to simplify the model, we can consider the coating as an elastic beam (Figure 7f) resting on two supports (marked as S). Under the influence of force F1 applied from the indenter, the beam bends, and forces F2 (tearout forces) act at the ends of the beam. If the F2 value is greater than the strength of the adhesive bond with the substrate, the coating detaches from the substrate. Of course, the real model is much more complex; it is obvious that factors of plastic deformation and shear force can also have an influence, but the authors consider the proposed model acceptable for a qualitative explanation of the process. Another reason for the poor adhesion of the coating to the substrate may be the formation of the possible Zr, Ti, Hf intermetallic sublayer discussed above.
The above assumptions are largely confirmed by examining a cross-section taken perpendicular to the scribe groove in the area close to point LC2 (Figure 8). In particular, the coating in the area of the bottom of the scribe groove (area D, Figure 8a) maintains its integrity (despite several transverse cracks). There are no signs of the peeling of the coating from the substrate in this area. At the same time, at the boundaries of the groove (areas B and C, Figure 8a,b), the peeling of the coating from the substrate is observed, and behind the delamination area there is an area in which the coating is completely absent.

3.4. (Zr,Nb)N Coating

The (Zr,Nb)N coating showed a fairly low value of the critical fracture load LC2. However, the nature of the destruction of this coating has significant differences from the previously considered (Zr,Ti)N coating, which also showed rather low resistance to destruction in the scratch test. It is obvious that the (Zr,Nb)N coating has good adhesion strength to the substrate; no noticeable delamination of this coating from the substrate is observed even at extreme loads (Figure 9). Along the scribing groove, the formation of several cracks is observed, directed at an acute angle to the direction of movement of the indenter. The destroyed fragments of the coating in the scribing furrow are pressed into the substrate material (Figure 9d–f). Since the coating is characterized by active crack formation, the acoustic emission signal is full of peaks, starting from minimum loads; however, the destruction of the coating (point LC1) according to visual data begins at a load of about 9 N. In this coating, bending causes conformal cracking [78].
Data on the high strength of the adhesive bonds between the coating and the substrate are confirmed when studying a transverse section made perpendicular to the scribing groove (Figure 10a–c). Detachment of the coating from the substrate is not observed even under conditions of extreme plastic deformation. Directly in the scribing furrow, both transverse and longitudinal cracks are formed in the coating structure, as well as cracks of a combined type (Figure 10c,d).

3.5. (Ti,Zr,Hf)N Coating

Complete destruction of the (Ti,Zr,Hf)N coating (critical load LC2) is observed already at a load of 12 N. This coating has one of the lowest resistances to destruction among the studied samples. A general view of the ribbing groove and characteristic areas of destruction are shown in Figure 11. When destroyed, a network of cracks is formed in this coating, and peeling of coating fragments from the substrate is also observed in areas adjacent to the scribing groove (Figure 11d,e). Despite the acoustic emission data, the destruction of this coating (point LC1) begins at loads of about 7 N. The dominant mechanism of destruction of this coating is tension failure [78].
A study of a transverse section passing through a ribbing groove is presented in Figure 12. In Figure 12a, there is a shaft of plastic deformation of the substrate at the boundary of the scribing groove (left side of the image). The shaft formed as a result of plastic deformation floats onto the coating. On the other (right) side, you can see the imprinting of coating fragments into the substrate material. The destruction of the coating occurs both as a result of the formation of cracks (oblique and transverse, see Figure 12b,e) and as a result of detachment from the substrate (Figure 12b–d).

3.6. (Ti,Zr,Nb)N Coating

The sample with (Ti,Zr,Nb)N coating has the maximum LC2 value among the studied samples. At the initial stage of coating destruction, cracks begin to form in the scribing groove and at its boundaries (Figure 13b,c). At the boundary of the groove, cracks are formed, directed at an acute angle to the direction of movement of the indenter and having a length of 10–15 μm. In the furrow itself, smaller cracks are formed, directed perpendicular to the furrow. In the area of the end of the groove (corresponding to the fracture load LC2, Figure 13d–g), cracking is also observed, while no significant delamination of the coating from the substrate is observed. It is obvious that this coating has good adhesion to the substrate. The presence of multiple acoustic emission peaks in this coating may be due to the active formation of cracks in its structure. Since this coating has a multilayer structure, cracks forming in the surface layers can be inhibited in the areas of interlayer interfaces, and, thus, the destruction of the coating is slowed down [79]. In reality, the destruction of the coating (point LC1) begins at a load of about 9 N (see area A in Figure 13a). This coating is characterized by a mechanism of destruction in the form of tension failure [78].
Data on good adhesion to the substrate are also confirmed by the results obtained when studying a transverse section running perpendicular to the scribing groove (Figure 14). In particular, even under conditions of significant plastic deformation of the substrate, the adhesive bond between the coating and the substrate is maintained (Figure 14a,b). In this case, transverse cracks are formed in the coating, passing into the substrate (Figure 14a).

4. Discussion

The impact of the indenter on the coating during the scratch test can be described as the sum of the impact of three components: the indentation component (plastic deformation, including plastic deformation of the substrate), the internal stress component, and the friction component [81]. Thus, two factors have a key influence on the destruction of the coating: the strength of the coating and the adhesion strength of the coating and the substrate. With different combinations of these factors, four different behaviors of the coating under external influence can be assumed:
  • Low strength and poor adhesion to the substrate (the coating collapses and peels off);
  • Enough strength with poor adhesion to the substrate (the coating peels off);
  • Low strength with enough adhesion to the substrate (the coating is destroyed);
  • Enough strength with enough adhesion to the substrate (the coating can resist destruction for enough time).
Let us analyze the resistance to destruction and the nature of destruction of all the studied coatings (Table 1). The (Ti,Zr,Nb)N coating has the best resistance to destruction. The (Zr,Hf)N coating, which has the greatest hardness and resistance to destruction, has the problem of poor adhesion to the substrate. Upon solving this problem, the (Zr,Hf)N coating has high application potential.

5. Conclusions

1. The greatest hardness (3100–3300 HV) is found in the (Zr,Hf)N and (Ti,Zr,Nb)N coatings.
2. In coatings that simultaneously include Zr and Ti, a nanolayer structure is formed, while in coatings without Ti, the formation of a monolithic single-layer structure is observed.
3. A comparison of two coatings, (Ti,Zr,Nb)N and (Zr,Hf)N, which formally have the best resistance to destruction during the scratch test among the samples under study, shows a significant difference in the mechanism of their destruction. The (Zr,Hf)N coating looks more durable, but has worse adhesion to the substrate. As a result, although the coating is retained directly in the scribing groove, a large area of delamination and destruction is formed around the groove.
4. The (Ti,Zr,Nb)N coating, although possibly lower in strength, has a high strength of adhesive bond with the substrate; no noticeable delamination is observed along the groove boundary.
5. The task of further research will be to increase the adhesion of the (Zr,Hf)N coating, which has high strength. Improved adhesion can be achieved by changing the composition of the adhesive sublayer (for example, by using pure Zr or a Zr-Ti mixture).

Author Contributions

Conceptualization, A.M. and A.V.; Methodology, A.V., C.S., A.S., F.M. and N.S.; Resources, S.G.; Data curation, C.S. and K.M.; investigation, C.S., N.S., A.S., F.M. and K.M.; Writing—original draft preparation, A.V. and C.S.; Writing—review and editing, A.V., C.S., S.G. and A.M.; Project administration, C.S. All authors have read and agreed to the published version of the manuscript.

Funding

This work is funded by the state assignment of the Ministry of Science and Higher Education of the Russian Federation, project No FSFS-2021-0006.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The original contributions presented in the study are included in the article, further inquiries can be directed to the corresponding author.

Acknowledgments

The study used equipment from the Center for Collective Use of Moscow State Technological University STANKIN (agreement no. 075-15-2021-695, 26/07/2021).

Conflicts of Interest

The authors declare no conflicts of interest.

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Figure 1. (a) Structure (TEM) and (b) surface morphology (SEM) of the studied coatings.
Figure 1. (a) Structure (TEM) and (b) surface morphology (SEM) of the studied coatings.
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Figure 2. Results of determining the values of critical points of destruction of the coatings LC1 and LC2 using the scratch test method.
Figure 2. Results of determining the values of critical points of destruction of the coatings LC1 and LC2 using the scratch test method.
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Figure 3. Destruction of the ZrN coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) destruction of the coating in the area of the end of the groove (area B), (d) area of destruction of the coating C, (e) area of destruction of the coating D.
Figure 3. Destruction of the ZrN coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) destruction of the coating in the area of the end of the groove (area B), (d) area of destruction of the coating C, (e) area of destruction of the coating D.
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Figure 4. Study of the nature of the destruction of the ZrN coating during a scratch test on a transverse section in the area close to point LC2: (a) general view of a cross-section through a scribing groove, (b) peeling of a coating fragment under the influence of shear stresses, (c) pressing of coating fragments into the substrate in a scribing groove and destruction of the coating in the area adjacent to the groove, (d) preservation of the adhesive bond between the coating and the substrate with noticeable plastic deformation, (e,f) peeling of the coating from the substrate, with chipping of nanofragments of the coating in the area of the interface with the substrate.
Figure 4. Study of the nature of the destruction of the ZrN coating during a scratch test on a transverse section in the area close to point LC2: (a) general view of a cross-section through a scribing groove, (b) peeling of a coating fragment under the influence of shear stresses, (c) pressing of coating fragments into the substrate in a scribing groove and destruction of the coating in the area adjacent to the groove, (d) preservation of the adhesive bond between the coating and the substrate with noticeable plastic deformation, (e,f) peeling of the coating from the substrate, with chipping of nanofragments of the coating in the area of the interface with the substrate.
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Figure 5. Destruction of the (Zr,Ti)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of the beginning of coating destruction (point LC1), (c) area of complete coating destruction (point LC2), (d,e) coating destruction in the area of the end of the groove (area B), (f) area where the coating begins to fail.
Figure 5. Destruction of the (Zr,Ti)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of the beginning of coating destruction (point LC1), (c) area of complete coating destruction (point LC2), (d,e) coating destruction in the area of the end of the groove (area B), (f) area where the coating begins to fail.
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Figure 6. Study of the nature of destruction of the (Zr,Ti)N coating during a scratch test on a transverse section in the area close to point LC2: (a,b) destruction of the coating due to the destruction of the adhesive bond between the coating and the substrate.
Figure 6. Study of the nature of destruction of the (Zr,Ti)N coating during a scratch test on a transverse section in the area close to point LC2: (a,b) destruction of the coating due to the destruction of the adhesive bond between the coating and the substrate.
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Figure 7. Destruction of the (Zr,Hf)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) the initial area of furrow formation, cracking of the coating, (c) the beginning of the destruction of the coating (point LC2), (d) the area of complete destruction of the coating (point LC2), (e) the nature of the destruction of the coating in the end area scribing grooves, (f) delamination formation scheme, in which the coating is treated as an elastic beam.
Figure 7. Destruction of the (Zr,Hf)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) the initial area of furrow formation, cracking of the coating, (c) the beginning of the destruction of the coating (point LC2), (d) the area of complete destruction of the coating (point LC2), (e) the nature of the destruction of the coating in the end area scribing grooves, (f) delamination formation scheme, in which the coating is treated as an elastic beam.
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Figure 8. Study of the nature of destruction of the (Zr,Hf)N coating during a scratch test on a transverse section in the area close to point LC2: (a) formation of through-transverse cracks in the coating structure, (b) peeling of the coating from the substrate in the area adjacent to the scribing groove.
Figure 8. Study of the nature of destruction of the (Zr,Hf)N coating during a scratch test on a transverse section in the area close to point LC2: (a) formation of through-transverse cracks in the coating structure, (b) peeling of the coating from the substrate in the area adjacent to the scribing groove.
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Figure 9. Destruction of the (Zr,Nb)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) end of the scribing furrow, (d–f) destruction of the coating in the area of the end of the furrow.
Figure 9. Destruction of the (Zr,Nb)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) end of the scribing furrow, (d–f) destruction of the coating in the area of the end of the furrow.
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Figure 10. Study of the nature of destruction of the (Zr,Nb)N coating during a scratch test on a transverse section in the area close to the point LC2: (a,b) strong adhesion to the substrate is maintained under significant plastic deformations of the substrate, (c,d) nature of crack formation in the coating.
Figure 10. Study of the nature of destruction of the (Zr,Nb)N coating during a scratch test on a transverse section in the area close to the point LC2: (a,b) strong adhesion to the substrate is maintained under significant plastic deformations of the substrate, (c,d) nature of crack formation in the coating.
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Figure 11. Destruction of the (Ti,Zr,Hf)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) destruction of the coating in the area of the end of the groove (area B), (d) area of destruction of the coating C, (e) area of destruction of the coating D.
Figure 11. Destruction of the (Ti,Zr,Hf)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b) area of complete destruction of the coating (point LC2), (c) destruction of the coating in the area of the end of the groove (area B), (d) area of destruction of the coating C, (e) area of destruction of the coating D.
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Figure 12. Study of the nature of destruction of the (Ti,Zr,Hf)N coating during a scratch test on a transverse section in the area close to point LC1: (a) general view of a transverse section through the scribing groove, (b) a plastic deformation shaft at the boundary of the scribing groove, (c–e) the nature of the coating destruction—cracking and peeling from the substrate, (f) plastic deformation and cracking in the coating in the scribing groove.
Figure 12. Study of the nature of destruction of the (Ti,Zr,Hf)N coating during a scratch test on a transverse section in the area close to point LC1: (a) general view of a transverse section through the scribing groove, (b) a plastic deformation shaft at the boundary of the scribing groove, (c–e) the nature of the coating destruction—cracking and peeling from the substrate, (f) plastic deformation and cracking in the coating in the scribing groove.
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Technologies 12 00179 g013aTechnologies 12 00179 g013b
Figure 13. Destruction of the (Ti,Zr,Nb)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b,c) the area where cracking begins in the coating, (d) area of complete destruction of the coating, (e) failure of the coating at the end of the furrow (area B), (f) failure area of coating E, (g) area of failure of coating F.
Figure 13. Destruction of the (Ti,Zr,Nb)N coating during the scratch test: (a) acoustic emission signal (top) and general view of the scribing groove (bottom), (b,c) the area where cracking begins in the coating, (d) area of complete destruction of the coating, (e) failure of the coating at the end of the furrow (area B), (f) failure area of coating E, (g) area of failure of coating F.
Technologies 12 00179 g013aTechnologies 12 00179 g013b
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Figure 14. Study of the nature of destruction of the (Ti,Zr,Nb)N coating during a scratch test on a transverse section in the area close to point LC2: (a) the adhesive bond between the coating and the substrate is maintained even with significant plastic deformations in the substrate and the formation of transverse cracks, (b) preservation of the adhesion of the coating and the substrate under conditions of plastic deformation.
Figure 14. Study of the nature of destruction of the (Ti,Zr,Nb)N coating during a scratch test on a transverse section in the area close to point LC2: (a) the adhesive bond between the coating and the substrate is maintained even with significant plastic deformations in the substrate and the formation of transverse cracks, (b) preservation of the adhesion of the coating and the substrate under conditions of plastic deformation.
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Table 1. Assessment of the strength of the coatings against fracture during scratch testing.
Table 1. Assessment of the strength of the coatings against fracture during scratch testing.
Coating StrengthAdhesion Strength to SubstrateNature of DestructionCoating
LowLowDestruction of the coating in the furrow, detachment from the substrate along the edges of the furrowZrN
(Ti,Zr,Hf)N
LowHighDestruction of the coating in the furrow, without noticeable detachment from the substrate along the edges of the furrow(Zr,Nb)N
HighLowThe coating remains in the furrow but flakes off and breaks down along the edges of the furrow(Zr,Ti)N
(Zr,Hf)N
HighHighThe coating remains in the furrow and is slightly destroyed along the edges of the furrow(Ti,Zr,Nb)N
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Metel, A.; Vereschaka, A.; Sotova, C.; Seleznev, A.; Sitnikov, N.; Milovich, F.; Makarevich, K.; Grigoriev, S. Study of the Nature of the Destruction of Coatings Based on the ZrN System Deposited on a Titanium Alloy Substrate. Technologies 2024, 12, 179. https://doi.org/10.3390/technologies12100179

AMA Style

Metel A, Vereschaka A, Sotova C, Seleznev A, Sitnikov N, Milovich F, Makarevich K, Grigoriev S. Study of the Nature of the Destruction of Coatings Based on the ZrN System Deposited on a Titanium Alloy Substrate. Technologies. 2024; 12(10):179. https://doi.org/10.3390/technologies12100179

Chicago/Turabian Style

Metel, Alexander, Alexey Vereschaka, Catherine Sotova, Anton Seleznev, Nikolay Sitnikov, Filipp Milovich, Kirill Makarevich, and Sergey Grigoriev. 2024. "Study of the Nature of the Destruction of Coatings Based on the ZrN System Deposited on a Titanium Alloy Substrate" Technologies 12, no. 10: 179. https://doi.org/10.3390/technologies12100179

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