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Article

Investigation of High-Temperature Oxidation of Homogeneous and Gradient Ni-Cr-Al Coatings Obtained by Detonation Spraying

by
Bauyrzhan Rakhadilov
1,2,
Laila Sulyubayeva
1,
Meruyert Maulet
1,*,
Zhuldyz Sagdoldina
1,
Dastan Buitkenov
1 and
Ainur Issova
3
1
Research Center «Surface Engineering and Tribology», Sarsen Amanzholov East Kazakhstan University, Ust-Kamenogorsk 070000, Kazakhstan
2
PlasmaScience LLP, Ust-Kamenogorsk 070000, Kazakhstan
3
Department Biochemical Engineering, International Engineering Technological University, Almaty 50060, Kazakhstan
*
Author to whom correspondence should be addressed.
Coatings 2024, 14(1), 11; https://doi.org/10.3390/coatings14010011
Submission received: 10 November 2023 / Revised: 10 December 2023 / Accepted: 18 December 2023 / Published: 20 December 2023
(This article belongs to the Special Issue Corrosion and Wear Resistant Alloy/Metal Coatings)
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Abstract

:
The high-temperature oxidation of homogeneous and gradient coatings based on Ni-Cr-Al obtained by detonation spraying is investigated. To assess the resistance to high-temperature oxidation of Ni-Cr-Al coatings, cyclic tests were carried out at a temperature of 1000 °C for 50 cycles. The assessment of high-temperature oxidizing ability was carried out by measuring the weight gain of samples after each cycle. After high-temperature oxidation tests, the morphology and chemical composition of the coating structure in the cross-section were investigated using SEM/EDS. The phase composition of the samples was studied by X-ray diffraction (XRD) phase analysis. Visual analysis of the sample surface under study after high-temperature oxidation showed that the surface of homogeneous or gradient Ni-Cr-Al coatings remained undamaged. The results of X-ray phase analysis showed the peaks of Al2O3 in Ni-Cr-Al gradient coatings are more expressed and intense compared to homogeneous coatings of Ni-Cr-Al. Gradient coatings also retain an increased chromium content compared to homogeneous Ni-Cr-Al coatings. This increased chromium content can slow down mixing or diffusion between different phases of the material at their boundary, which, in turn, contributes to increasing the resistance of the gradient coating to oxidation.

1. Introduction

The capacity of materials to endure cyclic oxidation processes is a crucial characteristic, especially when operating under high temperatures. During real operation, components frequently encounter fluctuations in temperature. For instance, turbine blades utilized in aviation gas turbines typically operate within a temperature range of 900 to 950 °C on average; although, they frequently reach maximum temperatures surpassing 1100 °C. Subjecting components of aviation gas turbines to thermal cycles of heating and cooling can result in damage, subsequently raising maintenance costs due to the need to replace the affected parts. Regarding this matter, the advancement of specialized protective coatings designed to prevent high-temperature oxidation of aviation gas turbine components is crucial, carrying significant importance from both technical and economic standpoints within this industry. Such protective coatings possess the potential to extend the lifespan of components, decrease maintenance expenses, and enhance both the efficiency and safety of operations [1,2].
Ni-Cr-Al coatings find extensive application as bonding layers or as protective coatings safeguarding gas turbine components in high-temperature, oxidation, and hot corrosion environments in both power plants and aircraft engines [3]. Typically, Ni-Cr-Al coatings have a limited amount of aluminum and its insufficient presence during the service life is the primary cause of Ni-Cr-Al coatings’ quality deterioration. Excessive aluminum content, on the other hand, can lead to brittleness and potential cracks [4]. Moreover, at temperatures exceeding 1000 °C during the oxidation, the formation of oxide compounds like Ni (Cr, Al)2O4 (spinel) and NiO can occur. These compounds are considered potentially detrimental to coating durability due to rapid local volume increase [5]. Therefore, maintaining a stable aluminum content in Ni-Cr-Al coatings and developing methods for obtaining them are crucial steps in preventing the formation of mixed oxides and metastable aluminum oxides.
There are several ways to apply Ni-Cr-Al coatings to superalloys. Peng X. et al. created nanocomposite coatings consisting of Ni-Cr, Ni-Al, and Ni-Cr-Al-Al by concurrently depositing nickel along with chromium or aluminum nanoparticles. Due to the formation of a robust chromium or aluminum oxide film, these nanocomposite coatings exhibit exceptional resilience against oxidation and high-temperature corrosion [6,7]. Yang X. et al. conducted electroplating of Ni-Cr-Al nanocomposite coatings and proposed that, at high temperatures, the presence of Cr and Al particles aids in the creation of Cr2O3 and Al2O3, respectively. The determination of these oxide products was conducted by assessing the Cr/Al ratios, which resulted in different levels of resistance of the coating against high-temperature oxidation [8]. Efforts have been undertaken to utilize thermal spraying for the application of Ni-Cr-Al coatings, aiming to enhance the material’s resistance to oxidation [9]. Recently, a detonation spraying method has been developed, which is an alternative technology for coating Ni-Cr-Al. In comparison with other thermal spraying methods, those obtained using detonation spraying are characterized by a denser microstructure and better adhesion to the substrate due to high particle velocity and more efficient use of energy [10,11]. Thus, this method represents a promising way to obtain high-quality Ni-Cr-Al coatings.
To enhance the performance of and resistance to the destruction of coatings, the concept of functional gradient materials (FGMs) has been investigated [12,13,14,15,16,17,18,19]. Utilizing gradient coating structures offers a partial solution to the aforementioned problems, enabling a balance between high aluminum content and the ability to withstand loads [20]. Observations have shown that the formation of Al2O3 and Cr2O3 oxides during the initial stages of high-temperature corrosion, as well as the development of a mixed Cr2O3–Al2O3 oxide during testing, enhances the resistance of coatings to high-temperature corrosion and oxidation [21,22]. As a result, there is focused attention on Ni-Cr-Al coatings with a gradient structure [23,24,25].
In our previous work [26], we proposed a method for obtaining a gradient coating based on Ni-Cr-Al through detonation spraying. The uniqueness of this method lies in achieving the required gradient structure by adjusting the barrel filling volume with gas during the coating process. This allows us to control the distribution of the Ni-Cr-Al composite powder from the substrate to the coating surface. Heat-resistant and wear-resistant coatings, composed mainly of Ni and Cr particles, form on the surface of the substrate. Simultaneously, the concentration of Al gradually increases from the substrate to the surface, resulting in a significant amount of Al on the surface of the coatings. This intentional design facilitates the formation of a sufficient amount of Al2O3 on the coating surface. In our subsequent work [27], we compared the structure and properties of homogeneous and gradient coatings based on Ni-Cr-Al obtained through detonation spraying. The primary objective of this research is to explore the high-temperature oxidation of homogeneous and gradient coatings based on Ni-Cr-Al, obtained by detonation spraying.

2. Materials and Methods

To obtain homogeneous and gradient coatings based on Ni-Cr-Al, the low-alloy heat-resistant boiler steel 12Kh1MF (DIN 14MoV63) was chosen as the substrate. The chemical composition of this heat-resistant low-alloy steel, 12Kh1MF (DIN 14MoV63), according to GOST 20072, is given in Table 1. The samples were cut to a size of 15 × 15 × 3 mm. Before the coating was applied, the substrate surfaces were grounded from all six sides using MIRKA sanding paper to a grain size of 1200 to achieve a uniform and flat surface. Then, they were sandblasted from all six sides to create better adhesion of the sprayed coating.
To obtain coatings based on Ni-Cr-Al, a powder mixture consisting of 16 wt% Ni, 64 wt% Cr, and 20 wt% Al was used. Before usage, the powder mixture underwent preliminary mechanical activation in a PULVERISETTE 23 planetary ball mill. The mechanical activation process lasted for 2 h at a frequency of 30 Hz. The Ni-Cr powders (20 wt% Ni, 80 wt% Cr; Polema JSC, Tula, Russia) and Al (Al > 99.99 wt%; Polema JSC, Tula, Russia) with a particle size of 30–45 µm were employed. The composition of the powder was 80 wt% Ni-Cr and 20 wt% Al.
The coating was obtained at the CCDS 2000 detonation unit [28]. A general view of the installation is shown in Figure 1. The coating is applied using a detonation gun, where the barrel is filled with an explosive gas mixture. Then, an exact dose of gunpowder is fed into the barrel, which is then detonated with an electric spark. This leads to the heating of the powder particles to the state of melting, after which they are ejected at high speed to the surface of the part located in front of the detonation gun. Upon contact, micro-welding occurs, ensuring a strong attachment of the powder to the surface of the part at the molecular level. After each shot, the barrel is cleaned of detonation residues using nitrogen. To achieve the required coating thickness, successive series of shots are used, during which the object can be moved using a manipulator. Oxygen-acetylene mixtures O2/C2H2 = 1856 were used as explosive gas. A homogeneous Ni-Cr-Al coating was obtained, filling 50% of the barrel volume. Gradient coatings were obtained by reducing the barrel filling volume with gas from 50% to 25%. Our previously published work [26] provides a detailed description of the procedure for acquiring a gradient coating. Homogeneous and gradient Ni-Cr-Al coatings were applied to all six sides of the substrates. Table 2 shows the modes of obtaining homogeneous and gradient coatings based on Ni-Cr-Al [27].
The investigation focused on studying the cyclic oxidation characteristics of both uniform and graded coatings based on Ni-Cr-Al. This study involved subjecting the coatings to 50 cycles at a temperature of 1000 °C in an air environment. Each cycle consisted of a 1-h heating period followed by a 20 min cooling phase at room temperature. Prior to initiating the experiments, the samples were photographed and their mass was measured using scales sensitive to 0.01 mg. During the initial cycle, two samples were placed in a heat-resistant crucible capable of withstanding temperatures of up to 2500 °C, introduced into the furnace, and the heating time was counted. After heating for 1 h, the samples, along with their crucibles, were removed from the furnace and allowed to cool for 20 min. Subsequently, the individual heated samples were weighed and the increase in weight was recorded. For subsequent cycles, the samples in their crucibles were once again positioned within the muffle furnace and the aforementioned sequence of 1 h heating, 20 min. cooling, and weight measurement procedures was repeated. The evaluation of the samples’ ability to oxidize at high temperatures was determined by measuring the increase in weight gain of the samples during the cycles.
To determine the formed phases, present in the coating after a high-temperature oxidation test, the X-ray diffraction (XRD) method was used using an X’PertPRO diffractometer (Max-Planck-Gesellschaft, Munich, Germany) with Cu-Kα radiation (λ = 1.54 Å) at a voltage of 40 kV and a current of 30 mA. Diffractograms were analyzed using the HighScore program and measurements were carried out in the range of 2θ from 20° to 90°, with a step of 0.02° and a counting time of 0.5 s per step. After the tests, the morphology of the TBC cross-section was analyzed using backscattered electrons (BSEs) at accelerated voltages on the scanning electron microscope JSM-6390LV (Jeol, Tokyo, Japan). The porosity in the coatings was evaluated on SEM images using a special program Altami Studio 1.5 [29].

3. Results and Discussion

Prior to the high-temperature cyclic oxidation test, the porosity of the coatings was measured. The porosity of homogeneous and gradient Ni-Cr-Al coatings was about 1%. Bala N. et al. reported that the porosity, which was in the range of 1 to 3.5%, has a positive effect on the resistance to oxidation [30].
Table 3 shows the surface of the samples before and after the high-temperature cyclic oxidation test (10, 20, 30, 40, 50 cycles) at a temperature of 1000 °C. Prior to the high-temperature cyclic oxidation test, a sample with a homogeneous Ni-Cr-Al coating had a smoother gray surface and a sample with a gradient Ni-Cr-Al coating had a rough dark gray surface. The color of the homogeneous Ni-Cr-Al coating changed from grayish to dark gray after the first hour of exposure and this color remained until the 10th cycle. After the 20th cycle, small bubbles appeared on the surface of the coating and, by the 50th cycle, oxide layers formed along the edges. The Ni-Cr-Al gradient coating did not change color after one cycle; simply, dark oxide layers appeared in one corner and, by the 50th cycle, their number increased. After the 20th cycle, the Ni-Cr-Al coated samples acquired a grayish-green hue. The results show that the surface of the samples with coatings of homogeneous Ni-Cr-Al or gradient Ni-Cr-Al remains undamaged. The surface morphology of homogeneous and gradient coatings based on Ni-Cr-Al after high-temperature cyclic oxidation at 1000 °C is shown in Figure 2. In addition to scale, some bulk products could be detected; these products mainly consist of Cr2O3.
The results of X-ray phase analysis after testing for high-temperature cyclic oxidation (25 and 50 cycles) of samples coated with Ni-Cr-Al are shown in Figure 3 and Figure 4. The results show that, regarding the phases formed on the surface of homogeneous and gradient Ni-Cr-Al coatings, after 25 test cycles, homogeneous Ni-Cr-Al coatings consist of the oxides CrNi3, Cr2O3, Al2O3, Al8Cr5, NiCr2O4, and NiO and gradient Ni-Cr-Al coatings consist of CrNi3, Cr2O3, Al2O3, NiCr2O4, and NiO. Regarding the phases formed on the surface of homogeneous and gradient Ni-Cr-Al coatings, after 50 cycles, both coatings consist of the oxides CrNi3, Cr2O3, Al2O3, Al8Cr5, NiCr2O4, and NiO. The formation of Al2O3 on the coating surface may be due to the interaction of aluminum and oxygen near the surface. Other oxide compounds are formed as follows: the growth of the Al2O3 layer slows down at a certain stage of oxidation, which leads to the formation of significant amounts of Cr2O3 and NiO on the surface. Thus, due to solid-phase reactions between the oxides of Al2O3 (or Cr2O3) and NiO, a complex oxide NiCr2O4 (spinel) is formed. In a further discussion of these oxide compounds, we outlined the CNS abbreviation, which will be used by other researchers [31,32,33,34,35]. Prior to testing for high-temperature cyclic oxidation, the homogeneous Ni-Cr-Al coating consisted of the CrNi3 phase and the Ni-Cr-Al gradient coating consisted of the CrNi3, Al, and NiAl phases [26]. Accordingly, X-ray phase analysis shows that protective oxides, such as Cr2O3 and Al2O3, are formed on the surface of Ni-Cr-Al coatings, which may have higher resistance to high-temperature oxidation [21,22]. The results of XRD phase analysis showed that the peaks of Al2O3 in gradient coatings of Ni-Cr-Al are more pronounced and intense compared to homogeneous coatings of Ni-Cr-Al. Samples coated with Ni-Cr-Al acquired a grayish-green color after 20 cycles (Table 3), probably due to the formation of Cr2O3, which was also confirmed in the literature [36,37].
Figure 5 shows the change in the mass of uncoated samples, as well as samples coated with Ni-Cr-Al as a result of high-temperature cyclic oxidation tests. Samples with homogeneous and gradient coatings of Ni-Cr-Al showed a slight increase in mass after the second cycle and this increase continued until the completion of the fiftieth cycle. A sample with a homogeneous Ni-Cr-Al coating showed a smaller weight gain than a sample with a gradient Ni-Cr-Al coating. This can be explained as follows: the Al2O3 film formed on the surface of samples with homogeneous and gradient Ni-Cr-Al coatings was stable enough to prevent further oxidation and reduce weight gain. However, the aluminum content on the surface of the homogeneous Ni-Cr-Al coating decreased, which led to the formation of light oxides, such as CSN. Meanwhile, both aluminum oxide and light mixed oxides of CSN were formed on the surface of samples with gradient coatings of Ni-Cr-Al. This is confirmed by XRD analysis (Figure 4). Visual observation also shows that more oxides formed on the surface of the gradient coating. Thus, the weight gain of samples with homogeneous and gradient coatings based on Ni-Cr-Al differs.
A study of the microstructure of coatings after testing for high-temperature cyclic oxidation was carried out. SEM images of cross sections of homogeneous and gradient Ni-Cr-Al coatings after testing are shown in Figure 6. As can be seen in the image, the average thickness of the coating after the tests is 140–160 µm while, before the tests, it was 90–110 µm [27]. After the high-temperature cyclic oxidation test, the Ni-Cr-Al coatings did not show cracks and delamination. The microstructure of the coating is characterized by a high content of oxides and low porosity (about 1%). In Figure 5, areas with porosity are indicated with arrows, as well as areas with oxide content. According to the literature review, we can also state that the dark gray color represents the Al2O3 phase while the light gray shades correspond to other oxides [10,11,12]. Figure 6a shows that as a result of 50-h cyclic oxidation, approximately 8 µm of a continuous CSN layer is formed on the surface of a homogeneous Ni-Cr-Al coating, which is consistent with the results of XRD analysis (Figure 3). Figure 6b shows that a large amount of Al2O3, with the presence of CNS on the surface, is formed on the surface of the Ni-Cr-Al gradient coating.
Figure 6 also shows the spectra reflecting the regions selected for the determination of the elemental composition of Al, Cr, Ni, and O by the EDS method. The results are shown in Table 4. The EDS data indicate that there is no Al content in Spectrum 1 of a homogeneous Ni-Cr-Al coating (Figure 6a) while the contents of the Ni and Cr elements are 87 and 12.5 wt%, respectively. This indicates that the outer layers of oxides are formed mainly from CSN, which is confirmed by the results of XRD analysis (Figure 4). In a homogeneous Ni-Cr-Al coating in Spectral Region 2, an aluminum content of 35.1 wt% is observed, which most likely contributes to the internal oxidation of the coating. The Al content in Spectrum 1 of the Ni-Cr-Al gradient coating is 38 wt% (Figure 6b). This indicates a more intensive formation of protective phases of Al2O3 on the coating surface. It is known that the Al2O3 phase is the most preferred in the Ni-Cr-Al coating due to its stability and excellent oxidation resistance [38]. The gradient coating retains a high content of Cr (Spectra 2, 3) compared with the homogeneous coating of Ni-Cr-Al (Spectra 2, 3). An increased chromium content can slow down mixing or diffusion between different phases of the material at their interface, which, in turn, slows down the destruction of the gradient coating and improves its resistance to oxidation [32].
The elemental mapping analysis and the results of the linear scanning of the elements Ni, Cr, Al, and O for homogeneous and gradient coatings of Ni-Cr-Al after testing for high-temperature cyclic oxidation are shown in Figure 7. Figure 5a shows that the aluminum content increases towards the substrate surface, as well as that the elements that compose the coatings are evenly distributed at a distance of 100 µm from the surface to the coating. Further changes in the content can be explained by the depletion of aluminum. This is confirmed by the results of the SEM and EDS points. Figure 6b shows a clear gradient distribution of aluminum from the substrate to the coating surface with a high content of aluminum, which is consistent with the results of the XRD and EDS analyses.

4. Conclusions

In this research paper, the study of the high-temperature oxidative characteristics of homogeneous and gradient coatings based on Ni-Cr-Al obtained by detonation spraying was carried out. The conducted research leads to the following conclusions:
  • The results of X-ray phase analysis showed that after high-temperature oxidation, the protective oxides Cr2O3 and Al2O3 are formed, as well as the secondary oxides NiCr2O4 and NiO. The results showed that the surface of the samples with coatings of homogeneous Ni-Cr-Al or gradient Ni-Cr-Al remains undamaged. A sample with a homogeneous Ni-Cr-Al coating showed a smaller weight gain than a sample with a gradient Ni-Cr-Al coating;
  • The results of the elemental analysis showed that after the cyclic high-temperature oxidation of the near-surface layer, the CSN content of the homogeneous coatings is higher compared to that of the gradient coating. Ni-Cr-Al gradient coatings retain a high chromium content compared to homogeneous coatings, which can slow down mixing or diffusion between different phases of the material at the interface. This, in turn, contributes to an increase in the resistance of gradient coatings to oxidation.

Author Contributions

Data curation, A.I.; methodology, L.S.; project administration, D.B.; writing—original draft, B.R. and M.M.; writing—review and editing, Z.S. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Science Committee of the Ministry of Science and Higher Education of the Republic of Kazakhstan (Grant No. AP09058568).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Data are contained within the article.

Conflicts of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

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Coatings 14 00011 g001
Figure 1. A general view of computerized detonation complex CCDS2000.
Figure 1. A general view of computerized detonation complex CCDS2000.
Coatings 14 00011 g001
Coatings 14 00011 g002
Figure 2. Surface SEM images of the homogeneous (a) and gradient (b) coatings based on Ni-Cr-Al after 50 cycles of high-temperature cyclic oxidation at 1000 °C.
Figure 2. Surface SEM images of the homogeneous (a) and gradient (b) coatings based on Ni-Cr-Al after 50 cycles of high-temperature cyclic oxidation at 1000 °C.
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Coatings 14 00011 g003
Figure 3. Results of X-ray diffractometric analysis after 25 cycles of the high-temperature cyclic testing of homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
Figure 3. Results of X-ray diffractometric analysis after 25 cycles of the high-temperature cyclic testing of homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
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Coatings 14 00011 g004
Figure 4. Results of X-ray diffractometric analysis after 50 cycles of the high-temperature cyclic testing of homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
Figure 4. Results of X-ray diffractometric analysis after 50 cycles of the high-temperature cyclic testing of homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
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Coatings 14 00011 g005
Figure 5. Weight gain of the samples upon oxidation testing after 50 cycles at 1000 °C.
Figure 5. Weight gain of the samples upon oxidation testing after 50 cycles at 1000 °C.
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Coatings 14 00011 g006
Figure 6. Cross-sectional structure after 50 cycles of high-temperature oxidation testing at 1000 °C of the homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
Figure 6. Cross-sectional structure after 50 cycles of high-temperature oxidation testing at 1000 °C of the homogeneous (a) and gradient (b) Ni-Cr-Al coatings.
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Coatings 14 00011 g007
Figure 7. Elemental mapping analyses and a corresponding EDS line-scan analysis of the homegenouse (a) and gradient (b) Ni-Cr-Al coatings after 50 cycles of high-temperature oxidation testing.
Figure 7. Elemental mapping analyses and a corresponding EDS line-scan analysis of the homegenouse (a) and gradient (b) Ni-Cr-Al coatings after 50 cycles of high-temperature oxidation testing.
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Table 1. Chemical composition of 12Kh1MF steel (percent of weight).
Table 1. Chemical composition of 12Kh1MF steel (percent of weight).
CSiMnNiSPCrMoVCu
0.1–0.150.17–0.370.4–0.7to 0.3to 0.025to 0.030.9–1.20.25–0.350.15–0.3to 0.2
Table 2. The modes of obtaining homogeneous and gradient coatings based on Ni-Cr-Al [27].
Table 2. The modes of obtaining homogeneous and gradient coatings based on Ni-Cr-Al [27].
NameRatio
O2/C2H2		Barrel Filling Volume, %Spraying
Distance, mm		Shot Number
Homogeneous Ni-Cr-Al coating1.85650%25020
Gradient Ni-Cr-Al coating1.85650%2505
40%5
30%5
25%5
Table 3. Surface observations before and after high-temperature cyclic oxidation testing after 10, 20, 30, 40, and 50 cycles at 1000 °C.
Table 3. Surface observations before and after high-temperature cyclic oxidation testing after 10, 20, 30, 40, and 50 cycles at 1000 °C.
Sample NameTest Time at 1000 °C
Before
Oxidation Test		After 10 CycleAfter 20 CycleAfter 30 CycleAfter 40 CycleAfter 50 Cycle
Homogeneous
Ni-Cr-Al		Coatings 14 00011 i001Coatings 14 00011 i002Coatings 14 00011 i003Coatings 14 00011 i004Coatings 14 00011 i005Coatings 14 00011 i006
Gradient
Ni-Cr-Al		Coatings 14 00011 i007Coatings 14 00011 i008Coatings 14 00011 i009Coatings 14 00011 i010Coatings 14 00011 i011Coatings 14 00011 i012
Table 4. Chemical compositions (% mass) of homogeneous (a) and gradient (b) Ni-Cr-Al coatings after 50 cycles of high-temperature oxidation testing.
Table 4. Chemical compositions (% mass) of homogeneous (a) and gradient (b) Ni-Cr-Al coatings after 50 cycles of high-temperature oxidation testing.
NameElementAl, Mass %Cr, Mass %Ni, Mass %O, Mass %Total, Mass %
(a) Homogeneous Ni-Cr-Al coatingSpectrum 1-12.587.00.5100.00
Spectrum 235.120.57.137.3100.00
Spectrum 32.241.828.227.9100.00
(b) Gradient Ni-Cr-Al coatingSpectrum 138.413.59.039.1100.00
Spectrum 24.532.742.420.5100.00
Spectrum 32.568.23.825.5100.00
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MDPI and ACS Style

Rakhadilov, B.; Sulyubayeva, L.; Maulet, M.; Sagdoldina, Z.; Buitkenov, D.; Issova, A. Investigation of High-Temperature Oxidation of Homogeneous and Gradient Ni-Cr-Al Coatings Obtained by Detonation Spraying. Coatings 2024, 14, 11. https://doi.org/10.3390/coatings14010011

AMA Style

Rakhadilov B, Sulyubayeva L, Maulet M, Sagdoldina Z, Buitkenov D, Issova A. Investigation of High-Temperature Oxidation of Homogeneous and Gradient Ni-Cr-Al Coatings Obtained by Detonation Spraying. Coatings. 2024; 14(1):11. https://doi.org/10.3390/coatings14010011

Chicago/Turabian Style

Rakhadilov, Bauyrzhan, Laila Sulyubayeva, Meruyert Maulet, Zhuldyz Sagdoldina, Dastan Buitkenov, and Ainur Issova. 2024. "Investigation of High-Temperature Oxidation of Homogeneous and Gradient Ni-Cr-Al Coatings Obtained by Detonation Spraying" Coatings 14, no. 1: 11. https://doi.org/10.3390/coatings14010011

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