Journal of Nanomaterials
Volume 2016 (2016), Article ID 7124218, 8 pages
http://dx.doi.org/10.1155/2016/7124218

Research Article

Surface Microstructure of Nanoaluminized CoCrAlY Coating Irradiated by HCPEB

Zhiyong Han, Jian Han, and Zhenzhu Jing

Tianjin Key Laboratory for Civil Aircraft Airworthiness and Maintenance, Civil Aviation University of China, Tianjin 300300, China

Received 6 January 2016; Revised 16 March 2016; Accepted 12 April 2016

Academic Editor: Albano Cavaleiro

Copyright © 2016 Zhiyong Han et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

A thermal sprayed CoCrAlY coating was prepared by air plasma spray on the surface of Ni-based superalloy GH4169; then, a nanoscale aluminum film was deposited with electron beam vacuum deposition on it. The coatings irradiated by high-current pulsed electron beam were investigated. After HCPEB treatment, the Al film was remelted into the bond coat. XRD result shows that Al and Al₂O₃ phase were recorded in the irradiated and aluminized coatings, while Co-based oxides which originally existed in the initial samples disappeared. Microstructure observations reveal that the original coating with porosity, cavities, and inclusions was significantly changed after HCPEB treatment as compact appearance of interconnected bulged nodules. Moreover, the grains on the irradiated coating were very refined and homogeneously dispersed on the surface, which could effectively inhibit the corrosive gases and improve the coating oxidation resistance.

1. Introduction

With the rapid development of aerospace industry, hundreds of different types of coatings have been investigated to protect structural engineering materials from corrosion, wear, and erosion and to provide lubrication and thermal insulation [1–3]. Therefore, thermal barrier coatings (TBCs) have been extensively used for aircraft and industrial gas-turbine engines in the most demanding high-temperature environment because of the most complex structure and the excellent performance [4]. TBCs, typically, consist of the ceramic top coat (TC) (YSZ, ZrO₂-7-8 wt% Y₂O₃) and the metallic bond coat (BC) (MCrAlY, where M = Ni and/or Co) [5–7]. BC, the important constituent of TBC systems, could enhance the adhesion of the ceramic thermal barrier layer to the substrate and also provide oxidation protection to the substrate metal. However, during high-temperature service, thermal barrier coating systems would be influenced greatly on the thermal cycling that ultimately results in the TBC failure by spallation of the TC [8–10]. The main reason is that the oxidation of metallic elements of MCrAlY takes place in the BC which generates the thermally growth oxide (TGO). The formation and growth of TGO would lead to the maximum stress at the interface between TC and BC, which is the main factor in the failure of TBCs due to uncontrolled growth of TGO during thermal exposure in air [11, 12].

During the formation of TGO, mixed oxides of Cr and Co elements in the BC usually appear after the selective oxidation of Al element; then, an Al-depleted zone would be present beneath the oxide layer, which could shorten the service time of TBCs [13, 14]. Generally, the ideal TGO was formed as a slow- and steady-growing alpha-alumina oxide (α-Al₂O₃) which could provide an excellent diffusion barrier of oxygen and suppress further oxidation of BC [15]. Many researchers have investigated particularly the formation mechanisms of TGO to avoid the appearance of Al depletion [16, 17]. Consequently, through some modified methods to form the fine-grained structure and increase Al element concentration on the surface and subsurface of CoCrAlY coating, the selective oxidation of Al element could keep proceeding to avoid the formation of other oxides and improve the formation of α-Al₂O₃ layer.

Electron beam vacuum deposition (EBVD) has been extensively used to prepare a certain number of films, such as Al-Mn, Al-Cr, and TiO₂, because of their unique physical and chemical properties and technological applications including ultraviolet light absorbers and gas sensors [18–20]. Compared with the conventional electrochemical deposition of organic solvent and molten salt systems, EBVD has the advantages of high purity, less pollution, and good compactness [19]. In particular, many researchers have investigated in detail characteristics of pure Al film deposited by EBVD [21, 22]. Wang and Meng investigated the surface morphology, structure, adhesion, and corrosion resistance of Al and Al-Mn films deposited onto carbon steel by EBVD [21]. The deposited Al and Al-Mn films are smooth, compact, and uniform. The corrosion resistance of Al film in 3.5% NaCl solution increases with the film thickness and evaporation rate. Therefore, it is reasonable to deposit pure Al film by the way of EBVD on the surface of CoCrAlY coating.

It is well known that high-current pulsed electron beam (HCPEB) has been proved to be a powerful tool to modify surface microstructure and performance of materials recently, which has the comparative advantage of purer energy transport process and higher efficiency than the pulsed ion beam and laser beam [23–25]. During the transient irradiation process, a high electron beam energy (10⁸–10⁹ W/cm²) is instantly deposited in a thin layer to form the affected zone with extremely high-temperature gradient [26]. There are lots of physical processes, which are heating, melting followed by rapid solidification, surface smoothing, and finishing as well as evaporation condensation, on the surface of coating after irradiation. Currently, numerous researchers have studied surface modification of different materials after HCPEB irradiation. Hao et al. found that the coarse surface of arc-sprayed FeCrAl coating was changed as discrete bulged nodules with smooth and compact appearance while the high-temperature corrosion resistance got worse after irradiation [27]. Cai et al. investigated the thermal sprayed YSZ coatings subjected to HCPEB and found that the very fine grains formed on the surface and high-temperature oxidation resistance was significantly improved after irradiation [26].

In this paper, a nanoscaled Al film was deposited on the thermal sprayed CoCrAlY coating with EBVD technique. With that, the coatings were subjected to a HCPEB irradiation process. The modified microstructure and surface roughness were characterized with an attempt to observe the effect of remelted surface with Al and comprehend the influence of Al depletion after HCPEB irradiation.

2. Experimental

Ni-based superalloy GH4169 (Cr 19.62, Fe 17.75, Nb + Ta 5.08, Mo 3.03, Ti 1.08, Al 0.58, Si 0.17, and Ni balance, wt%) used as the substrate was cut into rectangular specimens of approximately 12 × 8 × 2 mm. Co-23Cr-13Al-0.5Y powder of size 5~50 μm was used for the bond coating. To eliminate the residual oil contamination and surface oxides, all of the substrate materials were blasted by 60-mesh white corundum using 8070P-B type blasting machine before deposition, which could obtain the required surface roughness for coating adhesion. After that, CoCrAlY powder was deposited on the substrate using Praxair 3710 type APS equipment. Corresponding spraying parameters are shown in Table 1. The coating thickness was about 200 μm.

Table 1: Air plasma spraying parameters.

Parameter
Voltage (V)
Current (A)
Powder feed rate (rmp)
Spray distance (mm)
Spray rate (mm/s)
Primary gas (psi)
Secondary gas (psi)
Carrier gas (psi)

CoCrAlY coating
38
750
2.5
85
450
60
110
40

High purity Al particles of size Φ3 × 3 mm were deposited on the CoCrAlY coating to generate Al film of ~600 nm thickness by using DZS-500 type EBVD equipment. The EBVD deposition was carried out under the following parameters: vacuum 2.6 × 10⁻⁶ Torr, electron beam gun voltage 8 KV, electron beam current 270 mA, and the evaporation duration 80 min. Then, the coated samples were irradiated at room temperature with 10 and 20 pulses using a Hope-1 type HCPEB source, respectively. The HCPEB irradiation was carried out under the following conditions: the electron energy 25 KeV, current pulse duration 1.5 μs, energy density 4 J/cm², and vacuum 3.8 × 10⁻⁵ Torr. More details about the principle of HCPEB system are in [28].

The surface microstructure of the initial and irradiated samples was generally performed by using 1530VP type scanning electron microscope (SEM) and energy dispersive spectrometer (EDS). The phase structure of the coatings with and without Al film deposition before and after irradiation was examined using Rigaku D/max 2500/pc type X-ray diffraction (XRD) with CuKα radiation. Additionally, three-dimensional laser scanning microscope (LSM) of type LEXT-OLS4000 3D was carried out to obtain the surface roughness of the samples.

In order to distinguish the different coatings with and without Al films and before and after HCPEB irradiation and describe more detailed investigations of surface microstructure, four kinds of coating systems were marked as A, B, C, and D, as shown in Table 2:

(1)Coating A represents the initial APS CoCrAlY coating.(2)Coating B represents the APS CoCrAlY coating irradiated by HCPEB with 20 pulses.(3)Coating C represents the nanoaluminized CoCrAlY coating irradiated by HCPEB with 10 pulses.(4)Coating D represents the nanoaluminized CoCrAlY coating irradiated by HCPEB with 20 pulses.

Table 2: Four kinds of experimental coating system.

Coating
A
B
C
D

Preparation procedure(s)
As-sprayed CoCrAlY coating
As-sprayed CoCrAlY coating + 20 pulses
As-sprayed CoCrAlY coating + Al + 10 pulses
As-sprayed CoCrAlY coating + Al + 20 pulses

3. Results and Discussion

The XRD results of the coatings are shown in Figure 1. Coating A, the initial CoCrAlY coating, was composed mainly of β-CoAl and γ-Co solid solution phases. Meanwhile, a small amount of oxides, Al₂O₃ and Co-based oxides, was recorded on the surface of the initial coating. After 20-pulse HCPEB irradiation, oxides disappeared on account of the special selective surface purification effect of HCPEB treatment [29]. Besides, coatings C and D, after Al film deposition and HCPEB irradiation, consisted mostly of β-CoAl, γ-Co solid solution phases, Al phase, and little Al₂O₃ phase. Moreover, it was found that the content of Al increased while γ-Co was reduced with increasing the pulses of HCPEB irradiation correspondingly according to the comparison between coatings C and D. Significantly, Al element was from the nanoscaled Al film on the CoCrAlY coating and the CoAl compound. Then, the superficial Al element was agglomerated with O element to form more stable Al₂O₃ phase. Accordingly, the peaks of Al₂O₃ phase were recorded. It is worth noting that after HCPEB irradiation the XRD peaks were slightly shifted, indicating that residual stress existed in the coating owing to the rapid cooling [30]. Besides, the variation of chemical gradients and evaporation of Al element in the coating surface also could lead to the peaks shifting [31–33].

Figure 1: XRD patterns of coating A, B, C, and D.

Figure 2 provides the morphology of coating A, the initial thermal sprayed CoCrAlY coating, which has the typical feature of APS coating. The surface was highly rough and loose, and a large number of structural defects like nonmolten particles, spray angles, large cavities, and cracks were observed scatting on the surface, and all these drawbacks were shown in Figure 2(a). The splash-type particles can be seen in region B and the magnified image in the top right of Figure 2(a) and the large cavities in region A. During thermal spray process, coating materials were heated to the melted or high plastic deformation temperature by the plasma flame and then deposited on the surface of the substrate with the gas flow flying at high velocities. Therefore, APS CoCrAlY coating has the wavy lamellar structure with many interlaces and porosities featured by numerous deformation particles interlacing and overlapping together, as shown in Figure 2(b). However, the large cavities and microcracks among the particles can allow the greater penetration of molten salts or corrosive gases to destroy the coating and severely affect the formation of TGO and, eventually, result in the spallation and failure for the entire coating system.

(a)

(b)

Figure 2: Surface morphology (a) and cross-sectional image (b) of coating A.

Figure 3 shows the surface SEM morphology of coating B, coating C, and coating D. It can be seen that the coatings with and without Al film deposition before and after irradiation present rather different surface character compared with the initial one.

(a)

(b)

(c)

Figure 3: Surface SEM images of (a) coating B, (b) coating C, and (c) coating D.

After 20 pulses of irradiation without Al film deposition, as shown in Figure 3(a), the coarse surface was improved to a certain extent. The surface defects, like large particles, spray angles, cavities, and cracks, were partly modified and melted obviously and replaced by the discrete bulged nodules with a glossy and compact appearance, which was the common feature of many HCPEB treated metal materials surface. Therefore, similar structures were observed in experiments with the coatings, coatings C and D, under Al deposition and HCPEB irradiation. With Al deposition under 10 pulses of irradiation (Figure 3(b)), the coating surface was remelted entirely and presents two distinct characters, which seemed like “hills (region C) and valleys (region D),” respectively. Simultaneously, a small quantity of cavities were also observed dispersedly in the surface, which was on account of the local sublayer melting and eruption through the surface. As the HCPEB irradiation was further increased to 20 pulses, as shown in Figure 3(c), the discrete bulged “hills” began to agglomerate and merge together to form the larger and connected relatively nodules. Meanwhile, the surface became more smooth and dense, while the cavities and cracks became less and smaller.

Figure 4 reveals further detailed analysis of the surface morphology of coating D. The EDS analysis was carried out on the typical “hills and valleys,” which were bulged nodules and sunken pits marked as A and B in Figure 4(a), respectively. The results of point A, as shown in Figure 4(b), clearly reveal that the bulged nodules were composed mainly of the elements Co, Cr, and Al. However, the point B, “valley,” was made up of the elements Al, O, and Y (Figure 4(c)). The higher content of Al means that the black district might consist of pure Al and Al₂O₃. Besides, the content of element Y reveals that the selective oxidation of Y was also available in the surface black oxides, which may form YAlO₃ oxides and has an important influence on the growth of TGO and its adherence force [34, 35].

(a)

(b)

(c)

(d)

(e)

Figure 4: Surface morphology of coating D, (a) magnified image; (b) EDS of point A; (c) EDS of point B; (d) high-magnification of bulged nodules; (e) EDS of point C.

Another important aspect is about the vaporization particles which were observed closely adherent to the surface of the smooth bulged nodules from the high-magnification image, as shown in Figure 4(d). Moreover, the diameter of these bubbles was in a range of tens to hundreds of nanometers, and the size of the biggest bubble was about eight hundred nanometers, which was actually called the refined grains and had a significant effect on the elements diffusion and surface roughness. The EDS analysis of the bubble was shown in Figure 4(e). It is obvious that these refined grains were mainly γ-Co nanoscaled bubbles in which the element Cr was solid dissolved, and they also contained the elements of oxygen and alumina.

The SEM images of the cross-sectional coating D were shown in Figure 5. As shown in Figure 5(a), the cross-sectional image was featured by obvious three distinct regions, which were the unaffected CoCrAlY coating in the middle, the substrate at the bottom, and the melted refined region at the upper part. Also, the middle region had the same feature, typical lamellar structures with many interlaces and porosities, as the initial coating (Figure 2(b)). Nevertheless, the upper region was featured by the wavy melted layer with refined structure, as observed in Figure 5(b). The melted layer of coating D, measuring about 12 μm, was completely free from embedded oxidation and pores. Homogeneously, the melted layers of coating B and coating C were about 6.41 and 8.31 μm, respectively, as shown in Figure 6. Consequently, it is essential that Al film deposition and HCPEB irradiation can homogenize the highly nonuniform microstructures which resulted from the As-sprayed CoCrAlY coating.

(a)

(b)

Figure 5: Cross-sectional SEM image of coating D (a) and magnified image (b).

(a)

(b)

Figure 6: Cross-sectional magnified LSM images of coating B (a) and coating C (b).

It can be found that Al film deposition and HCPEB irradiation had very significant effect on the surface modification of the thermally sprayed CoCrAlY coating. As mentioned above, after irradiation, the surface of the coating was characterized by distinct bulged nodules and sunken pits, which could account for the “evaporation” mode. During the electron energy irradiation, the surface melted and the melting sites agglomerated and merged together to form the discontinuously bulged nodules. Besides, as the energy intensified, evaporation of matrix took place and the vapor rapidly removed from the surface and then redeposited to generate the nonscale bubbles eventually [35, 36]. As for coatings C and D, the melting and evaporation of surface matrix would be more and faster because of the aluminum film with low melting point, so the bulged nodules on the surface appear larger and continue. Additionally, the nanoscale refined grains adhered to the bulged nodules could effectively increase the rate of aluminum diffusion to generate the uniform and compact TGO and improve the oxidation of thermal barrier coating finally.

4. Conclusions

The surface microstructure of as-sprayed CoCrAlY coating, with and without aluminum deposition, before and after HCPEB irradiation, was characterized by means of XRD, SEM, and EDS. The main conclusions could be summarized as follows:

(1)After HCPEB irradiation, Co-based oxides of the initial coating disappeared, while Al and Al₂O₃ phase were detected in the coatings with aluminum deposition, which meant that nanoscaled Al film could be melted in the surface of CoCrAlY coating.(2)The initial surface structural defects, large particles, spray angles, cavities, and cracks, were melted and replaced by the successional bulged nodules with glossy and compact appearance under HCPEB treatment and Al deposition. With the increasing HCPEB pulses, the discrete bulged structures began to agglomerate and merge together to form the larger and connected relatively nodules.(3)The black sunken sites between the bulged nodules were composed mainly of Al₂O₃ and YAlO₃ oxides, and the melted layer of coatings B, C, and D were about 6.41, 8.31, and 12 μm, respectively.(4)Abundant nanoscale bubbles (40–850 nm), refined grains, were observed to homogeneously disperse on the irradiated aluminized coating surface on account of evaporation process. The refined structure played a significant role in the resistance of oxidation and corrosion of coating.

Competing Interests

The authors declare that they have no competing interests.

Acknowledgments

This work was supported by the National Natural Science Foundation of China (U1333107).

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