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Article

Increase in Oxidation Resistance of MAR M-509 via LA-CVD Aluminizing

by
Wojciech J. Nowak
*,
Bernadeta Hader
,
Kamil Ochał
and
Bartek Wierzba
Department of Materials Science, Faculty of Mechanical Engineering and Aeronautics, Rzeszow University of Technology, Powstanców Warszawy 12, 35-959 Rzeszów, Poland
*
Author to whom correspondence should be addressed.
Coatings 2021, 11(11), 1306; https://doi.org/10.3390/coatings11111306
Submission received: 30 September 2021 / Revised: 21 October 2021 / Accepted: 26 October 2021 / Published: 27 October 2021
(This article belongs to the Special Issue Application of Coatings in Industry and Means of Transport)
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Abstract

:
Due to their excellent mechanical properties, Co-based alloys are one of the main candidates to replace Ni-based alloys in high temperature application. Knowledge about oxidation resistance of Co-based alloy MAR M-509 and the extent of its aluminizing on its oxidation resistance is limited. Therefore, in the present study, an aluminide layer was manufactured by low activity chemical vapor deposition (LA-CVD) on MAR M-509. Aluminized and uncoated alloys were investigated in terms of oxidation kinetics and oxidation resistance during isothermal and cyclic oxidation at 1000 and 1100 °C. Material in the as-cast and after exposure was analyzed using scanning electron microscopy (SEM), thermogravimetry (TG) and glow-discharge optical emission spectrometry (GD-OES). Obtained results allowed for elucidating of degradation mechanism including nitridation process of carbides for MAR M-509. It was found that aluminizing of MAR M-509 significantly decreases its oxidation kinetics by the factor of 2.5 and 1.5 at 1000 and 1100 °C respectively. Moreover, the suppression of identified degradation mechanism in case of aluminized alloy was found until occurrence of breakaway oxidation of the aluminide layer. It was also proposed that further increase in oxidation resistance can be successively achieved by an increase in aluminide layer thickness.

1. Introduction

Alloys used in aircraft engines or in stationary gas turbines (SGT) face harsh conditions, such as high temperature, aggressive gases and cyclic thermal loading. Thus, they need to possess good combinations of mechanical strength, microstructural stability and oxidation resistance. Ni-based alloys are the most common materials used in the hottest part of the gas turbines nowadays. However, the constant need of increase in gas turbines efficiency demands increasing of inlet gases temperature [1]. This in turn implies difficulties due to material limitation, which is mainly its melting temperature. Thus, the research for novel materials for application at high temperature is required. To ensure increased oxidation resistance, the protective coatings are applied on the surface of elements manufactured from Ni-based alloys, such as aluminide layers [2,3,4,5], MCrAlY-type coatings [6,7,8,9] or complete thermal barrier coatings (TBC) [10,11,12,13]. However, the research for alternative materials for potential replacement of Ni-based alloys is still required. The so-called high entropy alloys (HEAs) are promising candidates to replace Ni-based alloys in the hottest parts of gas turbines [14,15,16,17]. The proposed materials are TiAl alloys [18,19,20], MoSi2-based alloys or their composites [21,22,23] or Co-based alloys [24,25,26]. The major advantage of a Co-based alloy in comparison with Ni-based alloys are their better mechanical properties [27], higher melting temperature [28] and high resistance against corrosion and sulfidation [29,30]. Studies on oxidation behavior of Co-based superalloys revealed that they possess relatively high oxidation resistance [31,32,33,34,35]. It is known that aluminide layers increase high temperature oxidation of Ni-based alloys. Therefore, several attempts were made to produce aluminide layers on Co-based alloys, e.g., on Haynes 188 and WI-52 [36], and also to study the oxidation resistance of alloys such as AMS 5608 with an aluminide layer produced by pack-cementation [37] or DZ40M with aluminide layer made by low pressure chemical vapor deposition (LP-CVD) [38]. Among Co-based alloys, the family MAR M-509 is one of the most popular for high-temperature application. It is characterized by good mechanical properties, such as fatigue strength [39], thermomechanical fatigue [40,41] and good corrosion and erosion resistance [42]. However, studies on oxidation behavior of MAR M-509 are scant [43]. Moreover, no studies on the effect of aluminizing on oxidation resistance of MAR M-509 were done so far. Therefore, to fulfil this lack, the present study was done. In the present study, the oxidation behavior of an aluminized and uncoated MAR M-509 during isothermal and cyclic oxidation tests at 1000 °C and 1100 °C was conducted and compared.

2. Materials and Methods

In the present study, a Co-based superalloy MAR M-509, with the chemical composition given in Table 1, was investigated in terms of high temperature oxidation resistance. The chemical composition of the studied alloy was measured using spark emission optical spectrometer (Spark-OES) ARL 3460 made by Thermo Fisher Scientific (Ecublens, Switzerland). To study the extent of increase in the oxidation resistance, an aluminide layer on MAR M-509 via the low activity chemical vapor deposition (LA-CVD) method was manufactured using BERNEX BPXpro 325S equipment (IHI BERNEX AG, Olten, Switzerland). The gaseous atmosphere consisting of a mixture of AlCl3 and H2 was produced in an external generator and transferred into a retort where samples were placed. The process was performed at 1040 °C for 6 h. The oxidation rate of aluminized and uncoated MAR M-509 was analyzed during isothermal thermogravimetrical oxidation test using XERION X-tube vertical furnace made by Xerion Advance Heating Ofentechchnik GmbH (Freiberg, Germany). The isothermal oxidation test was performed at two temperatures, namely 1000 and 1100 °C in air for 48 h. For determining the oxidation resistance during cyclic oxidation test, a furnace SCZ 120/150 made by Czylok (Jastrzębie Zdrój, Poland) was employed. The used thermal cycle consisted of 2 h heating at pre-set temperature and subsequent 15 min cooling with pressurized air. The mass change measurement was done every 10 cycles. After oxidation, the selected samples were subjected to an analysis of the element distribution as a function of sputtering time (indirectly depth) using glow discharge optical emission spectrometer (GD-OES) made by Horiba Jobin Yvon (Longjumeau, France). The GD-OES depth profiles were quantified using the procedure described in references [44,45,46]. The cross-sections of studied samples were produced using standard metallographic procedure, described elsewhere [47,48]. Microstructure and chemical composition of samples in the as-coated as well as after oxidation was investigated on surface and cross-sections using scanning electron microscope (SEM) Hitashi S3400N (Hitahi, Tokyo, Japan).

3. Results

3.1. Microstructure of MAR M-509 in the As-Cast Condition

The microstructure of MAR M-509 in the as-cast condition is shown in Figure 1. As visible, the material reveals the presence of dendrtitic and interdendritic regions (Figure 1a). SEM/EDS elemental maps (Figure 2) showed that dendritic regions are enriched in Co, Cr and Ni, while in the interdendritic region, the bright precipitates are present (Figure 1b), which, based on SEM/EDS analysis, are Ta, Ti and Zr carbides (Figure 2).

3.2. Microstructure of MAR M-509 after CVD Aluminizing

The microstructure of aluminide layer formed on the MAR M-509 substrate during the aluminizing process at 1040 °C for 6 h is shown in Figure 3. The observed microstructure is typical for LA-CVD layers and consists of the outer aluminide layer, the interdiffusion zone (IDZ) and the substrate (Figure 3a). The carbides are visible in the substrate zone. The aluminide layer was identified as CoAl. Within the aluminide layer a formation of aligned pores in the middle of aluminide layer is observed (Figure 3b). The average thickness of the formed aluminide CoAl layer is about 10 µm. The GD-OES depth profile shown in Figure 4 revealed that in the outer layer, a co-enrichment in Co and Al is observed up to about 110 s of stuttering. This co-enrichment confirms the formation of CoAl phase on surface of MAR M-509 substrate. At deeper parts, i.e., for a sputtering time between 110 and 300 s, co-enrichment of Cr, C and W is observed. The latter zone is called the interdiffusion zone (IDZ). Below the IDZ (for a sputtering time higher than 300 s), the constant concentration of alloying elements is noted at the level of concentration in the base alloy.

3.3. Air Oxidation Tests at 1000 °C

3.3.1. Isothermal Oxidation Test

The mass change plots obtained for studied aluminized and uncoated MAR M-509 during isothermal air exposure at 1000 °C showed the big difference between aluminized and uncoated material (Figure 5a). For uncoated MAR M-509, the measured mass change after 48 h of oxidation was equal to 1.3 mg·cm−2, while for aluminized MAR M-509, mass change after 48 h of exposure was 0.06 mg·cm−2. The logarithm of instantaneous oxidation rate k’w, calculated on the basis of the mass change plots shown in Figure 5a for uncoated MAR M-509, was equal to −11, while it was −13.5 for the aluminized one.
Analysis of the surface of specimens after an isothermal oxidation test showed that the Cr2O3 oxide scale was formed on the surface of uncoated MAR M-509, while the formation of Al2O3 was observed (Figure 6a,b, respectively) on the surface of the aluminized alloy. An investigation of the cross section of uncoated MAR M-509 confirmed the formation of external chromia scale; however, formation of AlN below the oxide scale was observed (Figure 6c). On top of the aluminized MAR M-509, formation of the Al2O3 oxide scale was found. Below the external alumina scale, local formation of Al-depleted phase described as Co(Cr, Ni) was observed (Figure 6d). The presence of IDZ and carbides is noted as well.

3.3.2. Cyclic Oxidation Test

Mass change plot obtained on aluminized and uncoated MAR M-509 during cyclic air oxidation test at 1000 °C is shown in Figure 7a. It is found that for uncoated alloy, the strong increase in mass change is observed up to about 400 cycles (800 hot hours). Above 400 cycles, a drop in mass change is observed. For aluminized MAR M-509, the constant increase in mass change is observed until the end of the cyclic oxidation test, i.e., up to 980 cycles (1960 hot hours—Figure 7a). However, the magnified mass change plot shown in Figure 7b revealed that up to around 700 cycles, the slope of mass change curve observed for aluminized MAR M-509 changes from the slope marked by pink dashed line to the slope marked by brown dashed line (Figure 7b). SEM/EDS analysis of the surface of the exposed samples revealed that on top of uncoated MAR M-509, co-oxide was formed (Figure 8a), while on top of the aluminized alloy, formation of alumina scale is found (Figure 8b). Analysis of the cross-section of uncoated MAR M-509 showed that in the very outer part of the oxide scale, co-oxide is formed. Below the outer co-oxide layer, formation of Co/Cr/Ni-mixed oxide is observed. Additionally, the intensive formation of AlN is visible (needle-like-shaped precipitates below the external oxide scale in Figure 8c). Formation of chromia scale was not observed. In the case of aluminized MAR M-509, formation of Al2O3 oxide scale on top of the remnants of the aluminide layer is found (Figure 8d). However, a local alumina scale spallation is noted (Figure 8b,d). Moreover, no presence of CoAl is observed, and only Co(Cr, Ni) in the zone of aluminide layer is observed.
Macroscopic investigation of an aluminized MAR M-509 showed two types of regions on the sample surface. Namely, a grey colored region in the middle of the sample and blueish regions closer to the edge of the sample are found (marked by yellow arrow as “Breakaway oxidation” on Figure 9a. The latter is the indication of a so-called “breakaway oxidation” phenomenon. Figure 9b shows the edge between the region where protective alumina oxide scale is formed and the region where “breakaway oxidation” occurred. The SEM/EDS elemental map shown in Figure 9c confirmed the formation of an alumina scale in the center of the sample (left side of images in Figure 9c), while in the region where “breakaway oxidation” occurred, enrichment of Co, Ni and Cr is found (right-hand side of images in Figure 9c). Analysis of the cross-section of aluminized MAR M-509 in the region of breakaway showed a local destruction of Al2O3 (Figure 10a) and overgrowing of Al2O3 by chromia oxide scale (Figure 10b). Formation of chromia scale is accompanied by the occurrence of internal precipitates of Al2O3 (Figure 10b).

3.4. Air Oxidation Tests at 1100 °C

3.4.1. Isothermal Oxidation Test

The mass change measured for uncoated and aluminized MAR M-509 during isothermal air oxidation at 1100 °C for 48 h is shown in Figure 11a. Uncoated MAR M-509 showed a rapid mass gain and the measured mass change after 48 h is 3.4 mg × cm−2 and for aluminized alloy this is 0.7 mg × cm−2 (Figure 11a). The logarithm of instantaneous oxidation rate k’w calculated on the basis of data shown in Figure 11a reached a value of −10 for uncoated alloy, while −11.6 for the aluminized one after 48 h of exposure.
Analysis of the surface of uncoated MAR M-509 showed that the alloy formed Cr2O3 oxide scale; however, a number of places where spallation occurred can be found (Figure 12a). In the case of aluminized MAR M-509 after isothermal air exposure at 1100 °C for 48 h formation of Al2O3 oxide scale is observed; however, many places of its spallation are also found (Figure 12b). SEM/BSE image of the cross-section of uncoated alloy after exposure is shown in Figure 12c. It is visible that the chromia scale is formed on the surface of the sample; however, several cracks formed within the external chromia scale (Figure 12c). On the cross-section of an aluminized MAR M-509, the remnants of alumina scale on top of the aluminide layer can be found as well as places where the alumina scale spalled off (Figure 12d). It is also visible that the aluminide layer no longer consists of CoAl, but rather Co(Al). The remnants of IDZ can still be found below the Co(Cr, Ni) layer.

3.4.2. Cyclic Oxidation Test

The mass change curves obtained for uncoated MAR M-509 during cyclic air oxidation at 1100 °C showed an increase up to 10 cycle and a rapid mass loss after 10 cycles and at the end of the test, i.e., after 50 cycles (100 hot hours), the measured mass change is −0.6 mg·cm−2. In contrary, for aluminized MAR M-509, the constant increase in mass gain is found till the end of cyclic oxidation test. At the end of the test, the mass change measured for aluminized alloy is 1.6 mg·cm−2 (Figure 13). Mass change curve obtained for aluminized MAR M-509 shown in Figure 13 does not show so clear change its slope as in Figure 7b. However, a macroscopic image of aluminized MAR M-509 after exposure revealed the occurrence of breakaway oxidation.
SEM/BSE images of the surface of oxidized uncoated MAR M-509 after cyclic oxidation test at 1100 °C showed that the alloy formed Cr/Co-mixed alloy on its surface. Moreover, a number of places indicating oxide scale spallation are observed (Figure 14a). SEM observation of the cross section of uncoated MAR M-509 confirmed the formation of Cr/Co mixed oxide scale in the very outer surface. Below the outer oxide scale, the extensive formation of AlN is found (Figure 14c). Moreover, formation of light-grey precipitates, indicated by a red arrow, and dark-grey precipitates, indicated by a blue arrow, is observed (Figure 14c). In the cross-section of aluminized MAR M-509 (Figure 14), formation of an Al2O3 external oxide scale is found. The aluminide layer is identified as Co(Cr, Ni). Moreover, no IDZ is observed.

4. Discussion

Considering the chemical composition of the studied Co-based alloy, namely MAR M-509, it is expected to form outer chromia scale, due to the relatively high Cr content, which is almost 23 wt.%. The obtained results confirmed that the studied uncoated alloy forms chromia scale during isothermal exposure for a relatively short time (up to 50 h) at both studied temperatures, i.e., at 1000 and 1100 °C. The obtained value of the mass change for uncoated MAR M-509 during exposure at 1000 °C for 48 h is comparable to the mass changes of other chromia forming alloys [49,50]. Chromium oxide is treated as a protective oxide scale [51]; however, as is known from the literature, its growth rate is higher than that for alumina scale [52]. Such a trend was also observed in the present study. Namely, the value of instantaneous apparent parabolic oxidation rate constant k’w at the end of exposure at 1000 °C of aluminized MAR M-509 was two orders of magnitude smaller than for uncoated MAR M-509. A similar trend was observed during exposure at 1100 °C, where the difference between the value of k’w for aluminized and uncoated MAR M-509 was 1.5 orders of magnitude. Thus, slowly growing alumina scale increases the oxidation resistance of the studied Co-based superalloy MAR M-509. During cyclic exposure of uncoated MAR M-509, mainly Cr2O3-based oxide on its surface was formed. This leads to higher mass change as compared with coated sample. The faster oxide scale growth resulted in faster oxide scale thickening. As the result, the oxide scale formed on uncoated MAR M-509 reached a “critical oxide scale thickness” [53] after about 400 cycles of cyclic exposure. As consequence an oxide scale spallation occurred, which is visible in the mass change plot as a drop in mass change for uncoated MAR M-509 (Figure 7b). Such a drop in mass change was not observed for aluminized MAR M-509 due to the slower growth rate of Al2O3 in comparison with Cr2O3. However, as shown in the present study during the cyclic oxidation test, an increase in oxidation resistance by CVD aluminizing is limited. It was shown that the growth of alumina scale causes transformation of the phases present on the aluminide layer from CoAl into Co(Al) (i.e., Figure 6d). This transformation is caused by the depletion of Al from CoAl layer. The constant growth of Al2O3 led to reach so called “critical oxide thickness” [53], above which a crack formation and its propagation is the only way to relax the stresses within the formed oxide scale. This, in turn, combined with thermal cycling, caused oxide scale spallation and re-growth. The latter caused faster Al-depletion. Together with Al-depletion from the Co-aluminide layer, a diffusion of elements such as Cr and Ni from the underlying substrate into depleted Co-aluminide layer occurred. After depletion of Al-reservoir from the aluminide layer, another elements present in the layer becomes oxidized, such as Co, Cr and Ni, which finally leads to the occurrence of breakaway oxidation. The growth rate of Co-, Cr- and Ni-oxide is much higher than for Al-oxide; thus, when the aforementioned elements become oxidized, a slope of mass change curve increases significantly. Such situation is visible in Figure 7b; namely, a change in mass change curve slope for aluminized MAR M-509 is observed at about 700 cycles. As shown during the cyclic oxidation test performed at 1000 °C, the Al-reservoir present in the 10-µm aluminide layer efficiently protected the alloy up to the 730th cycle, i.e., 1460 hot hours. Thus, aluminizing of MAR M-509 slowed down its oxidation kinetics by 2.5 times during exposure at 1000 °C and ensured the protection against the rapid oxidation up to 1460 h. A similar trend was observed during exposure at 1100 °C, namely, for uncoated MAR M-509, an oxide scale spallation was observed (mass loss in Figure 13), while for the aluminized sample, oxidation kinetics were decreased by a factor of 1.5. Further increasing of the oxidation resistance can be achieved by increasing the thickness of the CoAl layer.
As observed during the isothermal oxidation test, the uncoated MAR M-509 formed a relatively protective Cr2O3 oxide scale. However, in parallel, an intensive formation of nitrides in the deeper part of the alloy is also observed (e.g., Figure 6c, Figure 12c or Figure 14c). Since nitrides formation is relatively extensive and may affect the degradation mechanism of MAR M-509, it is worth to investigate and discuss this issue in more detail. From Figure 1, it is clear that in the alloy microstructure, a number of TaCs are found. SEM/EDS analysis of these carbides suggests that they also contain Ti and Zr. However, taking into account the fact that the EDS peaks for Ta, Ti and Zr partly overlap and in the literature these carbides in the MAR M-509 are identified as TaC, it is assumed that also in the present case, TaC are present in the alloy microstructure in the as-cast conditions. The results obtained in the present work showed that the carbides degrade during oxidation of uncoated MAR M-509 (see, e.g., Figure 6c, Figure 8c or Figure 12c). Moreover, as shown in Figure 14c, the new microstructural features are formed during exposure (the precipitates highlighted by red and blue arrows). The SEM/EDS elemental mapping of precipitate marked by red arrow shown in Figure 15 allows to identify this precipitate as CrN. Moreover, it can be clearly seen that the needle-like-shaped precipitates are AlN (Figure 16). SEM/EDS point analysis (not shown here) revealed that the precipitate, marked by the blue arrow, is identified as oxidized CrN. Note that the CrN precipitate is deeper than oxidized CrN. To explain this phenomenon, the simplified calculations of diffusion coefficients for nitrogen and oxygen in pure Co were done for 1000 °C and 1100 °C. At 1000 °C calculated diffusion coefficient for nitrogen was equal to 9.05 × 10−9 cm2·s−1, while for oxygen this was equal to 2.46 × 10−10 cm2·s−1. At 1100 °C, calculated values for diffusion coefficient for nitrogen was equal to 5.98 × 10−8 cm2·s−1 and for oxygen this was equal to 1.63 × 10−9 cm2·s−1. The diffusion coefficients for oxygen and nitrogen were estimated from the available literature data, mainly from the solubility of oxygen in cobalt, parabolic rate constants of cobalt oxide [54], the diffusion coefficient of cobalt [55] and from Gibbs energy of oxygen and nitride [56]. The results clearly show that the diffusion coefficients for nitrogen are one order of magnitude higher than for oxygen at both temperatures; thus, due to this fact, during oxidation, a front of nitridation is expected before oxidation. In the other words, the nitride formation is expected at higher depths in the material and oxidation is expected to be placed closer to the surface of the material. This is illustrated in Figure 16, where the interface between nitridation and oxidation front is shown. The SEM/BSE image is taken in such positioning that the upper part of the image is closer to the surface of the studied material. Observation of the map for N and O clearly confirms the statements made above, namely that nitrogen is concentrated at the bottom part of the map (near the center of the sample), while oxygen is concentrated in the upper part (closer to sample surface). This means that the dark precipitates present in the near surface region are Al-oxides, while nitrides are present in the deeper part. An interesting observation was made in the near-carbide region, namely, near the interface between carbide and matrix, a nearly continuous grey phase has grown (Figure 17). Through these phases, an SEM/EDS line-scan was performed (Figure 18). The obtained results clearly showed that a co-enrichment of Cr and N is observed in the region of grey phases. The observed carbon content is at the level of its content in the matrix (Figure 18b). This suggests the formation of chromium nitrides or carbonitrides at the edge of TaC. As the explanation, a preferential diffusion of nitrogen at the two phases boundary (in this case carbides and matrix) is assumed. Preferential diffusion of nitrogen via a two-phase boundary can be caused by the fact that such boundaries are called easy diffusion paths. On the other hand, there is no Cr in the carbide—it is present in the matrix. Preferential diffusion of nitrogen along the carbide/matrix interface causes local increase in nitrogen concentration. It is known that Cr is a strong nitride former; thus, due to the difference in chemical potential, Cr diffuses toward places with a higher nitrogen concentration (in this case the edge of the carbide) and forms stable nitride or carbonitride. Thus, the following mechanism for carbide degradation is proposed: carbides become nitrides at first and become subsequently oxidized. As shown in the present work, aluminizing of MAR M-509 successfully suppressed such a degradation mechanism at least until the beginning of breakaway oxidation.

5. Conclusions

In the present work, the influence of aluminizing of Co-based superalloy MAR M-509 on its oxidation resistance was studied. Based on presented results, the following conclusions can be formulated:
  • During the short-term isothermal oxidation test, uncoated MAR M-509 forms an external oxide scale based on Cr2O3 accompanied by intensive formation of nitrides below the outer oxide scale. The formed nitrides were mainly identified as AlN.
  • It was observed that internal nitridation plays an important role in the material degradation mechanism due to significant participation in the destabilization of strengthening precipitates, which are TaC via the formation of CrN at the edge of carbides, which becomes oxidized at a later stage.
  • Aluminizing of MAR M-509 increases the oxidation resistance of MAR M-509 by decreasing the oxidation rate by a factor of 2.5 at 1000 °C and 1.5 at 1100 °C.
  • The aluminide CoAl layer on MAR M-509 suppressed the observed degradation mechanism, including nitridation until the occurrence of breakaway oxidation.
  • Aluminide layer with thickness of 10 µm provided increased oxidation resistance of MAR M-509 up to 730 cycles, i.e., 1460 hot hours at 1000 °C. At this stage, breakaway oxidation was observed.
  • It is proposed that a further increase in oxidation resistance of MAR M-509 can be achieved by increasing the thickness of the produced CoAl layer.

Author Contributions

Conceptualization, W.J.N.; methodology, W.J.N.; validation, W.J.N. and B.W.; formal analysis, W.J.N.; investigation, W.J.N., B.H. and K.O.; resources, W.J.N.; data curation, W.J.N. and B.W.; writing—original draft preparation, W.J.N.; writing—review and editing, W.J.N.; project administration, W.J.N.; funding acquisition, W.J.N. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded in whole or in part by the National Science Centre, Poland, Grant No. 2020/39/B/ST8/00334. For the purpose of Open Access, the author has applied a CC-BY public copyright license to any Author Accepted Manuscript (AAM) version arising from this submission.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data are available from the corresponding author upon reasonable request.

Conflicts of Interest

The authors declare no conflict of interest. The funders had no role in the design of the study; in the collection, analyses or interpretation of data; in the writing of the manuscript, or in the decision to publish the results.

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Figure 1. Microstructure of MAR M-509 in the as-cast conditions at (a) low magnification and (b) high magnification of the red-dashed box in figure (a).
Figure 1. Microstructure of MAR M-509 in the as-cast conditions at (a) low magnification and (b) high magnification of the red-dashed box in figure (a).
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Figure 2. SEM/BSE elemental distribution maps obtained from MAR M-509 in the as-cast condition.
Figure 2. SEM/BSE elemental distribution maps obtained from MAR M-509 in the as-cast condition.
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Figure 3. Microstructure of an aluminide coating on MAR M-509 taken at (a) low magnification and (b) high magnification of the red-dashed box in figure (a).
Figure 3. Microstructure of an aluminide coating on MAR M-509 taken at (a) low magnification and (b) high magnification of the red-dashed box in figure (a).
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Figure 4. GD-OES depth profile of an aluminized MAR M-509.
Figure 4. GD-OES depth profile of an aluminized MAR M-509.
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Figure 5. Mass change plot (a) and log k’w (b) obtained during isothermal air oxidation at 1000 °C for 48 h of an aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
Figure 5. Mass change plot (a) and log k’w (b) obtained during isothermal air oxidation at 1000 °C for 48 h of an aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
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Figure 6. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after isothermal air oxidation at 1000 °C for 48 h.
Figure 6. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after isothermal air oxidation at 1000 °C for 48 h.
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Figure 7. Mass change plot obtained during cyclic oxidation test at 1000 °C (a) and the enlarged part of the plot showing a change in the slope of curve obtained for an aluminized MAR M-509 (b).
Figure 7. Mass change plot obtained during cyclic oxidation test at 1000 °C (a) and the enlarged part of the plot showing a change in the slope of curve obtained for an aluminized MAR M-509 (b).
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Figure 8. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after cyclic air oxidation at 1000 °C for 1000 cycles.
Figure 8. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after cyclic air oxidation at 1000 °C for 1000 cycles.
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Figure 9. Images showing (a) the macroscopic picture of aluminized MAR M-509 after cyclic oxidation up to 1000 cycles, (b) the SEM/BSE image of surface at the border between region covered by protective oxide scale and breakaway oxidation and (c) the corresponding SEM/EDS elemental map from the aforementioned region.
Figure 9. Images showing (a) the macroscopic picture of aluminized MAR M-509 after cyclic oxidation up to 1000 cycles, (b) the SEM/BSE image of surface at the border between region covered by protective oxide scale and breakaway oxidation and (c) the corresponding SEM/EDS elemental map from the aforementioned region.
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Figure 10. Microstructure of aluminized MAR M-509 in the region of breakaway occurrence shown at (a) low magnification and (b) high magnification.
Figure 10. Microstructure of aluminized MAR M-509 in the region of breakaway occurrence shown at (a) low magnification and (b) high magnification.
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Figure 11. Mass change plot (a) and log k’w (b) obtained during isothermal air oxidation at 1100 °C for 48 h of an aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
Figure 11. Mass change plot (a) and log k’w (b) obtained during isothermal air oxidation at 1100 °C for 48 h of an aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
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Figure 12. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after isothermal air oxidation at 1100 °C for 48 h.
Figure 12. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after isothermal air oxidation at 1100 °C for 48 h.
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Figure 13. Mass change plot obtained during cyclic oxidation test at 1100 °C of aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
Figure 13. Mass change plot obtained during cyclic oxidation test at 1100 °C of aluminized MAR M-509 and reference alloy (uncoated MAR M-509).
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Figure 14. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after cyclic air oxidation at 1100 °C in air.
Figure 14. SEM/BSE images of surface of (a) MAR M-509 and (b) aluminized MAR M-509, with corresponding cross-sections of (c) MAR M-509 and (d) aluminized MAR M-509 after cyclic air oxidation at 1100 °C in air.
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Figure 15. SEM/EDS elemental maps obtained in the region below the outer oxide scale formed on uncoated MAR M-509.
Figure 15. SEM/EDS elemental maps obtained in the region below the outer oxide scale formed on uncoated MAR M-509.
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Figure 16. SEM/EDS elemental maps obtained in the region marked by a red arrow in Figure 15.
Figure 16. SEM/EDS elemental maps obtained in the region marked by a red arrow in Figure 15.
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Figure 17. SEM/BSE image of the near-carbide region on uncoated MAR M-509 after cyclic oxidation at 1100 °C.
Figure 17. SEM/BSE image of the near-carbide region on uncoated MAR M-509 after cyclic oxidation at 1100 °C.
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Figure 18. SEM/BSE image showing the location of the SEM/EDS line-scan through the carbide and near-carbide region (a) and the results of line-scan showing elements concentration expressed in at.% (b).
Figure 18. SEM/BSE image showing the location of the SEM/EDS line-scan through the carbide and near-carbide region (a) and the results of line-scan showing elements concentration expressed in at.% (b).
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Table
Table 1. Measured chemical composition of the studied alloy MAR M-509.
Table 1. Measured chemical composition of the studied alloy MAR M-509.
ElementCNiCrWTaZrTiFeAlSiCo
Content in wt.%0.559.8222.886.893.790.350.180.160.250.05BAL.
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Nowak, W.J.; Hader, B.; Ochał, K.; Wierzba, B. Increase in Oxidation Resistance of MAR M-509 via LA-CVD Aluminizing. Coatings 2021, 11, 1306. https://doi.org/10.3390/coatings11111306

AMA Style

Nowak WJ, Hader B, Ochał K, Wierzba B. Increase in Oxidation Resistance of MAR M-509 via LA-CVD Aluminizing. Coatings. 2021; 11(11):1306. https://doi.org/10.3390/coatings11111306

Chicago/Turabian Style

Nowak, Wojciech J., Bernadeta Hader, Kamil Ochał, and Bartek Wierzba. 2021. "Increase in Oxidation Resistance of MAR M-509 via LA-CVD Aluminizing" Coatings 11, no. 11: 1306. https://doi.org/10.3390/coatings11111306

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