**3. Oxide particle embedded metallic systems**

Metal – oxide dispersed systems are well known for excellent mechanical properties because of high strength of the reinforcing ceramic oxide phases. Dispersion of hard oxide particles also enhances the surface properties, such as hardness and wear resistance, which are critical for tribological applications. The oxide particles also improve high temperature creep strength of the metallic materials by acting as obstacles to dislocations, reducing the deformation along the grain boundaries due to the diffusion processes or grain boundary rolling mechanism by pinning the grain boundaries. Thus the oxide particle embedded metallic systems have a vital role in many applications. Their processing is usually done in many routes depending on the type of application as well as the amount of material required. Here, we will briefly go through some of these techniques to introduce the reader to different processing routes. However, for more information one can refer to the literature and review articles on composite processing techniques. Following is the list of a few approaches usually employed to develop the metal – oxide composite systems (Kainer, 2006).

**Powder processing route**: In this approach, metal and oxide powders are blended together using different methods (eg: ball milling or mechanical alloying) and then compacted and sintered or consolidated into required shapes or bulk solids.

**Melting route**: There are different number of processes fall under this category that involve molten metals. This route is usually applied to low melting metal matrix composites, in which the metal ingots or pieces are melted and then the oxide particles are dispersed in the molten metal prior to solidification.

**Electrodeposition**: The oxide particles are suspended in an electrolyte which helps develop the matrix coating. Suspension of oxide particles along with continuous stirring in the electrolyte can embed the particles in the metal matrix during electrodeposition process.

**Vapor deposition**: Physical vapor deposition techniques (eg: electron beam evaporation, sputtering etc.) can be used to develop composite coatings using multiple targets in codeposition approach with intermittent reactive deposition process.

found to be more useful. Most of the high temperature coatings and oxide dispersion strengthened (ODS) alloys are embedded with highly stable oxide phases, which can provide mechanical stability as well as enhance the corrosion and oxidation resistance. In addition to the oxide dispersoids, ODS alloys employ alloying elements (eg: Cr, Al etc.) in such a way that the oxide layers are formed on the surfaces as well as at the grain boundaries at high temperatures during the operation, which then act as protective layers from the corrosion point of view. The oxide dispersoids in the ODS alloys can provide

Here, we will touch base on the corrosion phenomenon of oxide layer and oxide particle assisted corrosion behavior of metallic materials at low and high temperature applications with a brief review, and a case study will be presented on the corrosion phenomenon of oxide particle embedded high temperature composite coatings developed by thermal spray

Metal – oxide dispersed systems are well known for excellent mechanical properties because of high strength of the reinforcing ceramic oxide phases. Dispersion of hard oxide particles also enhances the surface properties, such as hardness and wear resistance, which are critical for tribological applications. The oxide particles also improve high temperature creep strength of the metallic materials by acting as obstacles to dislocations, reducing the deformation along the grain boundaries due to the diffusion processes or grain boundary rolling mechanism by pinning the grain boundaries. Thus the oxide particle embedded metallic systems have a vital role in many applications. Their processing is usually done in many routes depending on the type of application as well as the amount of material required. Here, we will briefly go through some of these techniques to introduce the reader to different processing routes. However, for more information one can refer to the literature and review articles on composite processing techniques. Following is the list of a few approaches usually employed to develop the metal – oxide composite systems (Kainer,

**Powder processing route**: In this approach, metal and oxide powders are blended together using different methods (eg: ball milling or mechanical alloying) and then compacted and

**Melting route**: There are different number of processes fall under this category that involve molten metals. This route is usually applied to low melting metal matrix composites, in which the metal ingots or pieces are melted and then the oxide particles are dispersed in the

**Electrodeposition**: The oxide particles are suspended in an electrolyte which helps develop the matrix coating. Suspension of oxide particles along with continuous stirring in the electrolyte can embed the particles in the metal matrix during electrodeposition process.

**Vapor deposition**: Physical vapor deposition techniques (eg: electron beam evaporation, sputtering etc.) can be used to develop composite coatings using multiple targets in co-

mechanical stability with improved creep resistance.

**3. Oxide particle embedded metallic systems** 

sintered or consolidated into required shapes or bulk solids.

deposition approach with intermittent reactive deposition process.

molten metal prior to solidification.

technique.

2006).

**Spray deposition**: Different number of processes have evolved in this category in which a stream of molten metal droplets are deposited on a substrate to build the matrix layer; and for composites, the oxide particles are co-sprayed to embed them in the matrix layers.

**Reactive formation**: In this approach, selective oxidation of certain phases in the bulk structures with exothermic reactions results in the in-situ formation of composites.

As listed above there are several approaches available for processing metal – oxide systems, and their corrosion properties are going to be dependent on the processing technique employed too. For example, the processing defects like porosity, improper bonding between the matrix and the oxide dispersoids, and their interfacial properties can influence the corrosion behavior quite extensively. Wetting of the oxide particles becomes a critical factor in some of the processing approaches to deal with the particle - matrix bonding. Fig. 4 shows a schematic for interfacial bonding of the second phase particles with matrix along the grain boundaries and triple junctions. In addition, high temperatures in some of the processing techniques may cause an interfacial reaction between the metal matrix and the dispersed second phase particles, thereby the interfacial stability and its properties play an increasingly important role in the corrosion. It is also possible that the interfaces could become prone to corrosion attack by providing preferential sites. In spray deposition approach splat boundaries, porosity, and distribution of the oxide particles may play an important role in deciding the corrosion properties. Added to that, the microstructures of the composites could also vary from process to process. The effect of some of these parameters on the corrosion of different metal – oxide systems is discussed in brief in the following sections.

Fig. 4. Schematic for interfacial bonding of second phase particles at grain boundaries and triple junctions.

Corrosion of Metal – Oxide Systems 277

Presence of rare earth oxides was proved to enhance the corrosion resistance of Ni composites also. It was reported that the Ni matrix reinforced with micron CeO2 particles possessed good corrosion resistance compared to Ni – ZrO2, Ni – partially stabilized ZrO2 (PSZ), and pure Ni coatings (Qu et al., 2006). Although the corrosion process usually proceeds along the grain boundaries, in the case of Ni – CeO2 composites the corrosion path was observed to be preferentially along the Ni/CeO2 interfaces, instead of Ni grain boundaries. Along with that, higher corrosion resistance of CeO2 was also observed to enhance the corrosion resistance of Ni/CeO2 interface. Also, codeposition of CeO2 particles induced the formation of small equiaxed Ni grains, which resulted in the corrosion along less straight paths and thus lowering the corrosion rates in Ni - CeO2 composites (Aruna et al., 2006). It is also considered that when CeO2 nanosized particles are embedded in the nickel matrix, the corrosion path is more seriously distorted as compared to micro-sized particles, which is favorable for corrosion resistance. In fact, the fine grain structure arising from the co-electrodeposition of CeO2 nanoparticles also promotes good corrosion resistance

Aruna et al. (2009) showed enhanced performance of wear and corrosion characteristics of Ni based composite coatings by embedding with alumina yttria doped cubic zirconia (AZY, (1−*x*)Al2O3–8 mol% yttria stabilized *x*ZrO2 (*x* = 10 wt%)) particles. The higher Warburg resistance of Ni - AZY and enhanced corrosion resistance was attributed to possible difference in mass transport phenomena in the Ni –AZY composites compared to the pure Ni with increased resistance of Ni grain boundaries in presence of AZY particles and

In other examples, Li et al. (2005) demonstrated the effect of the type of oxide particles dispersed on the corrosion behavior of Ni composites. Li et al. (2005) developed nanocomposite coatings consisting of TiO2 in the form of anatase and rutile in Ni matrix via electrochemical deposition technique, and showed improved corrosion properties of Ni – TiO2 composites compared to the pure Ni; however, the improvement in corrosion resistance was predominant in the case of anatase dispersed Ni composites. Improved corrosion resistance of Ni – TiO2 composites was attributed to the inhabitant behavior of TiO2 particles at the grain boundaries and triple junctions, which are the usual sites for corrosion attack. With an increase in the amount of TiO2, a decrease in the corrosion rates was also demonstrated because of the increased number of inhabited sites, which reduce penetration of the corrosive solution into the composite coatings. On the other hand, Ni - Al2O3 composite coatings (Erler et al., 2003) reported to show poor corrosion resistance compared to the monolithic Ni. Szczygieł and Kołodziej (2005) indicated that the lower corrosion resistance of Ni - Al2O3 could be due to poor bonding between the oxide particles and the matrix, which can increase the possibility of dissolution of loosely held Al2O3 (alumina) particles at high potentials and result in more nickel exposure to the electrolyte for corrosion attack. In another study by Aruna et al. (2011) the corrosion properties of Al2O3 embedded Ni composites showed the oxide phase dependent corrosion performance. Their studies indicated that the corrosion resistance of Ni - Al2O3 was better than the corrosion resistance of Ni – Al2O3 as well as the Ni – and Al2O3 mixture; however, the reason for

At high-temperatures the corrosion failure of a material system results from failure of its protective oxide scale. Different researchers have proved that addition of a small amount of

as compared to coarse grain structure (Qu et al., 2006).

such behavior was not explained.

thereby hindered the diffusion of chloride ions (Aruna et al., 2009).

## **4. Overview of corrosion phenomena of metal – Oxide systems**

Although, the metal matrix composites are well suited for mechanical, tribological and high temperature applications, it is to be clearly noted that their corrosion aspects could be considerably different, as well as complex, compared to the monolithic metallic systems. Corrosion of metal matrix composites could arise due to different reasons, such as electrochemical and chemical interaction between the constituent phases, microstructural effects, and possibly from processing related issues too (Cramer & Covino, 2005). Usually, composites have higher tendency to corrode because of the multiphase structure with metal matrix. If the second phase structure is conductive a galvanic cell can be formed within the system. For example, metallic composites reinforced with graphite or semi-conducting silicon carbide could undergo severe corrosion compared to the pure metals. Galvanic corrosion is not a problem if the second phase dispersoids are insulating, for example, oxide particles.

It is also very important that the second phase particles be uniformly distributed in the metal matrix. The effect of oxide particle size, volume fraction and their pretreatment can also influence the corrosion phenomenon. The other important factors that can contribute to the corrosion are surface morphology, porosity, stresses, bonding, defects at the matrix and dispersoid interfaces, crystallographic structure, and the type of oxide phase dispersed. For example, bonding between Al and Al2O3 (alumina) plays a crucial role in the corrosion of Al - Al2O3 composites. Usually the corrosion rate of the composites is measured by weight loss and the corrosion studies conducted on Al - Al2O3 composites in NaCl solution for prolonged periods showed considerable weight loss due to pits or microcrevice formation in the matrix near the particle-matrix interfaces, as well as from the particle dropout. The corrosion via pit initiation and propagation was determined to be due to the weak spots in the air-formed Al2O3 film because of the discontinuities and the second phase particles (Nunes & Ramanathan, 1995). In the case of 6061-T6 alloy mixed with 10 vol% Al2O3, poor corrosion resistance was reported to be due to poor bonding at the matrix and oxide particle interfaces (Bertolini et al., 1999). The Al alloys AA 6061 and AA 2014 embedded with Al2O3 particles exhibited stress-corrosion cracking when subjected to three-point beam bending along with alternate or continuous exposure to NaCl solution (Monticelli et al., 1997). Although addition of Al2O3 may seem to be detrimental in terms of corrosion resistance of Al alloys, with the combination of wear and corrosive conditions, the corrosion resistance of 6061 and 7075 Al alloys was observed to improve with the Al2O3 second phase dispersion (Fang et al., 1999; Varma & Vasquez, 2003) along with the enhancement of wear resistance. In marine biological applications, the microbial corrosion was also reported to occur in the Al - Al2O3 composites due to biofilm formation at the interfaces of Al and Al2O3 particles (Vaidya et al., 1997). In environmental and marine biological applications, the protective chromium oxides are not very benign because of their toxicity and as a result usage of chromia coatings is restricted. However, different rare earth oxides were proposed as alternatives for protection of Al alloys because of their cathodic inhibition properties (Aramaki, 2001; Hamdy et al., 2006; Hinton et al., 1986, 1987; Lin et al., 1992). Usually rare earth oxides are very useful for aerospace applications because of their high temperature oxidation resistance. According to Hamdy et al., (2006) CeO2 (ceria) treated Al alloys exhibited improved corrosion resistance due to oxide layer thickening. Muhamed & Shibli (2007) also showed improved corrosion performance of Al – CeO2 composites, but it was not in proportion to the amount of CeO2 incorporated.

Although, the metal matrix composites are well suited for mechanical, tribological and high temperature applications, it is to be clearly noted that their corrosion aspects could be considerably different, as well as complex, compared to the monolithic metallic systems. Corrosion of metal matrix composites could arise due to different reasons, such as electrochemical and chemical interaction between the constituent phases, microstructural effects, and possibly from processing related issues too (Cramer & Covino, 2005). Usually, composites have higher tendency to corrode because of the multiphase structure with metal matrix. If the second phase structure is conductive a galvanic cell can be formed within the system. For example, metallic composites reinforced with graphite or semi-conducting silicon carbide could undergo severe corrosion compared to the pure metals. Galvanic corrosion is not a problem if the second phase dispersoids are insulating, for example, oxide

It is also very important that the second phase particles be uniformly distributed in the metal matrix. The effect of oxide particle size, volume fraction and their pretreatment can also influence the corrosion phenomenon. The other important factors that can contribute to the corrosion are surface morphology, porosity, stresses, bonding, defects at the matrix and dispersoid interfaces, crystallographic structure, and the type of oxide phase dispersed. For example, bonding between Al and Al2O3 (alumina) plays a crucial role in the corrosion of Al - Al2O3 composites. Usually the corrosion rate of the composites is measured by weight loss and the corrosion studies conducted on Al - Al2O3 composites in NaCl solution for prolonged periods showed considerable weight loss due to pits or microcrevice formation in the matrix near the particle-matrix interfaces, as well as from the particle dropout. The corrosion via pit initiation and propagation was determined to be due to the weak spots in the air-formed Al2O3 film because of the discontinuities and the second phase particles (Nunes & Ramanathan, 1995). In the case of 6061-T6 alloy mixed with 10 vol% Al2O3, poor corrosion resistance was reported to be due to poor bonding at the matrix and oxide particle interfaces (Bertolini et al., 1999). The Al alloys AA 6061 and AA 2014 embedded with Al2O3 particles exhibited stress-corrosion cracking when subjected to three-point beam bending along with alternate or continuous exposure to NaCl solution (Monticelli et al., 1997). Although addition of Al2O3 may seem to be detrimental in terms of corrosion resistance of Al alloys, with the combination of wear and corrosive conditions, the corrosion resistance of 6061 and 7075 Al alloys was observed to improve with the Al2O3 second phase dispersion (Fang et al., 1999; Varma & Vasquez, 2003) along with the enhancement of wear resistance. In marine biological applications, the microbial corrosion was also reported to occur in the Al - Al2O3 composites due to biofilm formation at the interfaces of Al and Al2O3 particles (Vaidya et al., 1997). In environmental and marine biological applications, the protective chromium oxides are not very benign because of their toxicity and as a result usage of chromia coatings is restricted. However, different rare earth oxides were proposed as alternatives for protection of Al alloys because of their cathodic inhibition properties (Aramaki, 2001; Hamdy et al., 2006; Hinton et al., 1986, 1987; Lin et al., 1992). Usually rare earth oxides are very useful for aerospace applications because of their high temperature oxidation resistance. According to Hamdy et al., (2006) CeO2 (ceria) treated Al alloys exhibited improved corrosion resistance due to oxide layer thickening. Muhamed & Shibli (2007) also showed improved corrosion performance of Al – CeO2 composites, but it was not

**4. Overview of corrosion phenomena of metal – Oxide systems** 

in proportion to the amount of CeO2 incorporated.

particles.

Presence of rare earth oxides was proved to enhance the corrosion resistance of Ni composites also. It was reported that the Ni matrix reinforced with micron CeO2 particles possessed good corrosion resistance compared to Ni – ZrO2, Ni – partially stabilized ZrO2 (PSZ), and pure Ni coatings (Qu et al., 2006). Although the corrosion process usually proceeds along the grain boundaries, in the case of Ni – CeO2 composites the corrosion path was observed to be preferentially along the Ni/CeO2 interfaces, instead of Ni grain boundaries. Along with that, higher corrosion resistance of CeO2 was also observed to enhance the corrosion resistance of Ni/CeO2 interface. Also, codeposition of CeO2 particles induced the formation of small equiaxed Ni grains, which resulted in the corrosion along less straight paths and thus lowering the corrosion rates in Ni - CeO2 composites (Aruna et al., 2006). It is also considered that when CeO2 nanosized particles are embedded in the nickel matrix, the corrosion path is more seriously distorted as compared to micro-sized particles, which is favorable for corrosion resistance. In fact, the fine grain structure arising from the co-electrodeposition of CeO2 nanoparticles also promotes good corrosion resistance as compared to coarse grain structure (Qu et al., 2006).

Aruna et al. (2009) showed enhanced performance of wear and corrosion characteristics of Ni based composite coatings by embedding with alumina yttria doped cubic zirconia (AZY, (1−*x*)Al2O3–8 mol% yttria stabilized *x*ZrO2 (*x* = 10 wt%)) particles. The higher Warburg resistance of Ni - AZY and enhanced corrosion resistance was attributed to possible difference in mass transport phenomena in the Ni –AZY composites compared to the pure Ni with increased resistance of Ni grain boundaries in presence of AZY particles and thereby hindered the diffusion of chloride ions (Aruna et al., 2009).

In other examples, Li et al. (2005) demonstrated the effect of the type of oxide particles dispersed on the corrosion behavior of Ni composites. Li et al. (2005) developed nanocomposite coatings consisting of TiO2 in the form of anatase and rutile in Ni matrix via electrochemical deposition technique, and showed improved corrosion properties of Ni – TiO2 composites compared to the pure Ni; however, the improvement in corrosion resistance was predominant in the case of anatase dispersed Ni composites. Improved corrosion resistance of Ni – TiO2 composites was attributed to the inhabitant behavior of TiO2 particles at the grain boundaries and triple junctions, which are the usual sites for corrosion attack. With an increase in the amount of TiO2, a decrease in the corrosion rates was also demonstrated because of the increased number of inhabited sites, which reduce penetration of the corrosive solution into the composite coatings. On the other hand, Ni - Al2O3 composite coatings (Erler et al., 2003) reported to show poor corrosion resistance compared to the monolithic Ni. Szczygieł and Kołodziej (2005) indicated that the lower corrosion resistance of Ni - Al2O3 could be due to poor bonding between the oxide particles and the matrix, which can increase the possibility of dissolution of loosely held Al2O3 (alumina) particles at high potentials and result in more nickel exposure to the electrolyte for corrosion attack. In another study by Aruna et al. (2011) the corrosion properties of Al2O3 embedded Ni composites showed the oxide phase dependent corrosion performance. Their studies indicated that the corrosion resistance of Ni - Al2O3 was better than the corrosion resistance of Ni – Al2O3 as well as the Ni – and Al2O3 mixture; however, the reason for such behavior was not explained.

At high-temperatures the corrosion failure of a material system results from failure of its protective oxide scale. Different researchers have proved that addition of a small amount of

Corrosion of Metal – Oxide Systems 279

As discussed in the earlier sections, high temperature coatings are ubiquitous to industrial power generation, marine applications, and aircraft propulsion systems. Most high temperature coatings operate under extremely harsh conditions with conflicting operational requirements. For instance, coatings used in power plant boilers need to ensure an effective protection against high temperature corrosion under oxidizing, sulfidizing, carburizing environments and erosion from fly ash, as well as having a high thermal conductivity to exchange heat in order to provide an effective and economical maintenance. Further, to avoid premature failure, as discussed in the previously discussed overview section, the high temperature coatings also require good adhesion to the substrate, minimal mismatch in CTE between the coating and the substrate material, good thermal fatigue, and creep resistance

Most commercial coating systems do not meet all the required attributes for a given environment. For example, NiCr (55/45 wt.%) alloy is usually recommended for erosion– corrosion protection for boiler tubes in power generation applications (Higuera, 1997; Martinez-Villafan et al., 1998; Meadowcroft, 1987; Stack et al., 1995). Weld overlay coatings of Alloy 625(Ni-21Cr-9Mo-3.5Nb) have also been used for this application. When nickel is alloyed with chromium (>15wt%), Cr oxidizes to Cr2O3, which could make it suitable for use up to about 1200°C (Goward, 1986), although in practice its use is limited to temperatures below about 800°C. The efficacy of NiCr coatings deteriorates severely when molten ash deposits consisting of sodium-potassium-iron tri-sulfates (Na,K)3Fe(SO4)3 are present. Further, higher Cr content also reduces the creep resistance of NiCr alloys. Particularly, this issue becomes magnified in the case of thermal spray coatings. In addition to the grain boundaries, presence of splat boundaries, an inherent feature in thermal sprayed coatings also contributes to poor corrosion and creep performance at very high temperatures (Soltani et al., 2008; Zhu & Miller, 1997). Thus, from the materials perspective, the corrosion is influenced by several parameters, for example surface and bulk microstructures, thermodynamic stability of the phases, microstructural constituents, electrochemical potentials, protective phases and residual stresses etc. Thereby, it becomes user's responsibility to select an appropriate material system for a given operating condition either

The continued pursuit for increased efficiency in power generation and propulsion systems led to the development of functionally engineered coatings with multiple attributes. For example, an alternative method of combating the effects of coal ash corrosion is to install a material that contains sufficient amount of oxide stabilizing elements such as aluminum or silicon (NiCrAl, NiCrBSi NiCrMoBSi and NiCrBSiFe) to resist the dissolution of the oxide film when the molten ash is deposited. Similarly, functionally gradient materials (FGM) were proposed (Niino & Maeda, 1990) to obtain multifunctional properties with a combination of different metallic and ceramic systems in an engineered fashion. These materials were found to be very promising candidates for high temperature applications because of the reduced thermal stresses between the interfaces, resulting in enhanced thermal fatigue life (Bahr et al., 2003). The high temperature creep strength of metals is also greatly improved by the addition of high temperature stable dispersoid phases, due to grain boundary pinning such as the oxide dispersion strengthened super alloys (Ni-ThO2 and

(Bose, 2007; Patnaik, 1989; Uusitalo et al., 2004; Yoshiba, 1993; Yu et al., 2002).

to avoid or slow down the deterioration during the service period.

NiCr-ThO2) (Clauer & Wilcox, 1972).

reactive elements (such as Y, Ce, La, and Hf), or their oxides, improves the oxidation resistance of some high temperature alloys by decreasing the growth rate of the oxide and increasing the adherence of the oxide scale to the underlying alloys (Peng et al., 1995). Addition of Y2O3, CeO2, ThO2, La2O3 and AI2O3 to Ni - Cr alloys, and Y2O3, HfO2, ZrO2 and TiO2 to Co - Cr alloys may promote the formation of Cr2O3 protective oxide scale as well as increase its adherence to the ODS alloy system very effectively (Michels, 1976; Stringer & Wright 1972; Stringer et al., 1972; Whittle et al., 1977; Wright et al., 1975). In Ni - 20Cr - Y2O3 ODS alloy coatings, presence of Y2O3 was observed to promote the formation of Cr2O3 scale and thereby the improvement in scale spallation (Lianga et al., 2004). Stringer et al. (1972) proposed that the dispersed oxide particles act as heterogeneous nucleation sites for Cr2O3 grains and reduce the internuclear distance for the Cr2O3 scale formation, which will allow rapid formation of a continuous Cr oxide film with a finer grain size. The oxide layer with fine grain size can then easily release the thermal stress and therefore prevent crack propagation. Extensive experimental results and detailed mechanistic studies have indicated that the effects of dispersed oxides seem to be independent of the choice of the oxides, as long as they are not less stable than Cr2O3 (Lang et al., 1991). According to this mechanism, dispersion of above mentioned oxides expected to be most effective in enhancing Cr2O3 scale formation and thus lead to improved resistance to hot corrosion most effectively. According to He and Stott (1996) a short-circuited diffusion of Cr reduced the concentration of Cr in the alloy and thereby facilitated formation of Cr2O3 in Ni - 10Cr alloy with presence of Al2O3 and Y2O3 particles. Quadakkers et al. (1989) reported that Y2O3 incorporation in ODS alloys retarded the diffusion of Cr because of prevailing anionic diffusion over cationic diffusion. This mechanism was also supported by Ikeda et al. (1993), who also confirmed that the adhesion of Al2O3 could be promoted by the dispersed Y2O3 phase in ODS alloys.

According to Carl Lowell et al. (1982), the oxidation and corrosion resistance of ODS alloys was superior compared to the superalloys. However, different corrosion behavior among different ODS alloys, for example Ni based (NiCrAl) and Fe based (FeCrAl) ODS alloys, was attributed to the CTE mismatch and therefore the spallation resistance. Usually lower CTE mismatch between the ferritic ODS alloys and protective alumina film helps reduce the amount of stresses in the oxide during thermal cycling and thereby considerably less, or no, spalling. In contrast, the high CTE of Ni - based ODS alloys directly leads to spalling during cycling from 1100 0C to room temperature. Similarly, better oxidation and hot salt corrosion behavior is expected for Fe - based ODS alloys compared to the Ni - based ODS alloys. Therefore, it is apparent that the corrosion behavior of ODS alloys is highly dependent on the protective oxide layers formed during the high temperatures compared to the oxide particles embedded within the alloys, unlike the metal – oxide composites; however, formation of a uniform protective oxide scale could be dependent on the embedded oxide particles in the metal matrix. Thus, presence of oxide particles in a metal matrix can directly, as well as indirectly, help enhance the corrosion properties of different alloys and composite systems.

#### **5. Case study on high temperature coatings developed by spray deposition**

This case study presents synthesis and characterization of oxide particle embedded high temperature coatings developed by thermal spray technique, which is one of the processing routes discussed in the Section - 3, for boiler coating applications.

reactive elements (such as Y, Ce, La, and Hf), or their oxides, improves the oxidation resistance of some high temperature alloys by decreasing the growth rate of the oxide and increasing the adherence of the oxide scale to the underlying alloys (Peng et al., 1995). Addition of Y2O3, CeO2, ThO2, La2O3 and AI2O3 to Ni - Cr alloys, and Y2O3, HfO2, ZrO2 and TiO2 to Co - Cr alloys may promote the formation of Cr2O3 protective oxide scale as well as increase its adherence to the ODS alloy system very effectively (Michels, 1976; Stringer & Wright 1972; Stringer et al., 1972; Whittle et al., 1977; Wright et al., 1975). In Ni - 20Cr - Y2O3 ODS alloy coatings, presence of Y2O3 was observed to promote the formation of Cr2O3 scale and thereby the improvement in scale spallation (Lianga et al., 2004). Stringer et al. (1972) proposed that the dispersed oxide particles act as heterogeneous nucleation sites for Cr2O3 grains and reduce the internuclear distance for the Cr2O3 scale formation, which will allow rapid formation of a continuous Cr oxide film with a finer grain size. The oxide layer with fine grain size can then easily release the thermal stress and therefore prevent crack propagation. Extensive experimental results and detailed mechanistic studies have indicated that the effects of dispersed oxides seem to be independent of the choice of the oxides, as long as they are not less stable than Cr2O3 (Lang et al., 1991). According to this mechanism, dispersion of above mentioned oxides expected to be most effective in enhancing Cr2O3 scale formation and thus lead to improved resistance to hot corrosion most effectively. According to He and Stott (1996) a short-circuited diffusion of Cr reduced the concentration of Cr in the alloy and thereby facilitated formation of Cr2O3 in Ni - 10Cr alloy with presence of Al2O3 and Y2O3 particles. Quadakkers et al. (1989) reported that Y2O3 incorporation in ODS alloys retarded the diffusion of Cr because of prevailing anionic diffusion over cationic diffusion. This mechanism was also supported by Ikeda et al. (1993), who also confirmed that the adhesion of Al2O3 could be promoted by the dispersed Y2O3 phase in ODS alloys. According to Carl Lowell et al. (1982), the oxidation and corrosion resistance of ODS alloys was superior compared to the superalloys. However, different corrosion behavior among different ODS alloys, for example Ni based (NiCrAl) and Fe based (FeCrAl) ODS alloys, was attributed to the CTE mismatch and therefore the spallation resistance. Usually lower CTE mismatch between the ferritic ODS alloys and protective alumina film helps reduce the amount of stresses in the oxide during thermal cycling and thereby considerably less, or no, spalling. In contrast, the high CTE of Ni - based ODS alloys directly leads to spalling during cycling from 1100 0C to room temperature. Similarly, better oxidation and hot salt corrosion behavior is expected for Fe - based ODS alloys compared to the Ni - based ODS alloys. Therefore, it is apparent that the corrosion behavior of ODS alloys is highly dependent on the protective oxide layers formed during the high temperatures compared to the oxide particles embedded within the alloys, unlike the metal – oxide composites; however, formation of a uniform protective oxide scale could be dependent on the embedded oxide particles in the metal matrix. Thus, presence of oxide particles in a metal matrix can directly, as well as indirectly, help enhance the corrosion properties of different alloys and composite

**5. Case study on high temperature coatings developed by spray deposition**  This case study presents synthesis and characterization of oxide particle embedded high temperature coatings developed by thermal spray technique, which is one of the processing

routes discussed in the Section - 3, for boiler coating applications.

systems.

As discussed in the earlier sections, high temperature coatings are ubiquitous to industrial power generation, marine applications, and aircraft propulsion systems. Most high temperature coatings operate under extremely harsh conditions with conflicting operational requirements. For instance, coatings used in power plant boilers need to ensure an effective protection against high temperature corrosion under oxidizing, sulfidizing, carburizing environments and erosion from fly ash, as well as having a high thermal conductivity to exchange heat in order to provide an effective and economical maintenance. Further, to avoid premature failure, as discussed in the previously discussed overview section, the high temperature coatings also require good adhesion to the substrate, minimal mismatch in CTE between the coating and the substrate material, good thermal fatigue, and creep resistance (Bose, 2007; Patnaik, 1989; Uusitalo et al., 2004; Yoshiba, 1993; Yu et al., 2002).

Most commercial coating systems do not meet all the required attributes for a given environment. For example, NiCr (55/45 wt.%) alloy is usually recommended for erosion– corrosion protection for boiler tubes in power generation applications (Higuera, 1997; Martinez-Villafan et al., 1998; Meadowcroft, 1987; Stack et al., 1995). Weld overlay coatings of Alloy 625(Ni-21Cr-9Mo-3.5Nb) have also been used for this application. When nickel is alloyed with chromium (>15wt%), Cr oxidizes to Cr2O3, which could make it suitable for use up to about 1200°C (Goward, 1986), although in practice its use is limited to temperatures below about 800°C. The efficacy of NiCr coatings deteriorates severely when molten ash deposits consisting of sodium-potassium-iron tri-sulfates (Na,K)3Fe(SO4)3 are present. Further, higher Cr content also reduces the creep resistance of NiCr alloys. Particularly, this issue becomes magnified in the case of thermal spray coatings. In addition to the grain boundaries, presence of splat boundaries, an inherent feature in thermal sprayed coatings also contributes to poor corrosion and creep performance at very high temperatures (Soltani et al., 2008; Zhu & Miller, 1997). Thus, from the materials perspective, the corrosion is influenced by several parameters, for example surface and bulk microstructures, thermodynamic stability of the phases, microstructural constituents, electrochemical potentials, protective phases and residual stresses etc. Thereby, it becomes user's responsibility to select an appropriate material system for a given operating condition either to avoid or slow down the deterioration during the service period.

The continued pursuit for increased efficiency in power generation and propulsion systems led to the development of functionally engineered coatings with multiple attributes. For example, an alternative method of combating the effects of coal ash corrosion is to install a material that contains sufficient amount of oxide stabilizing elements such as aluminum or silicon (NiCrAl, NiCrBSi NiCrMoBSi and NiCrBSiFe) to resist the dissolution of the oxide film when the molten ash is deposited. Similarly, functionally gradient materials (FGM) were proposed (Niino & Maeda, 1990) to obtain multifunctional properties with a combination of different metallic and ceramic systems in an engineered fashion. These materials were found to be very promising candidates for high temperature applications because of the reduced thermal stresses between the interfaces, resulting in enhanced thermal fatigue life (Bahr et al., 2003). The high temperature creep strength of metals is also greatly improved by the addition of high temperature stable dispersoid phases, due to grain boundary pinning such as the oxide dispersion strengthened super alloys (Ni-ThO2 and NiCr-ThO2) (Clauer & Wilcox, 1972).

Corrosion of Metal – Oxide Systems 281

The hybrid process offers all benefits of wire stock and productivity of electric arc spraying combined with noticeably improved coating density of HVOF. In addition to introducing material through arcing mechanism, if desired, powder/liquid/gas precursors can also be fed through the HVOF coaxial feed line (Fig. 5a). This enables us to tailor the composition inflight by introducing particles into the HVOF jet, to cater to specific property requirements of a composite coating. This unique capability completely eliminates the necessity of processing and handling of the ultrafine particulates prior to feeding them into the hybrid gun. Synthesizing and introducing ultrafine and nano dispersoids inflight in a functional manner to produce composite coatings by the hybrid technique is quite unique in terms of simplicity compared to any other processes. A comparative picture of the steps involved in processing of particulate reinforced composites by conventional routes versus our approach

NiCr-Matrix NiCr wire (55/45 wt. %)

Following the above mentioned approach of inflight synthesis, different oxide ceramic particles were introduced into the NiCr (55/45 wt.%) alloy coating. The following coatings were deposited onto mild steel coupons for characterization: (a) NiCr only, (b) NiCr + Cr2O3, (c) NiCr + Al2O3, and (d) NiCr + SiO2. Along with these coatings, NiCr coatings using a twin wire arc spray process (TAFA 3830, Praxair Surface Technologies, Indianapolis, IN) were also deposited for comparison purposes. The arc current and voltage for both the processes were kept at 100 amps and 36 volts, respectively. The HVOF gas pressures were

**Precursor Materials Percentage** 

Aluminum nitrate -Al(NO3)3·9H2O 1:1 by weight in isopropyl

Chromium nitrate -Cr(NO3)3·9H2O Up to 50% by weight of

Tetraethoxysilane 100 %

alcohol (70%)

aluminum nitrate

Fig. 5. (a) Schematic of hybrid gun and (b) hybrid gun in operation.

(a) (b)

is presented in Table 1.

**Target Material** 

Al2O3 particulate

Cr2O3 Stabilizer

SiO2 particulate

Table 1. List of precursors used.

Various approaches have been adopted to disperse the second phase particles into bulk matrix phase, such as mechanical alloying/powder metallurgy (Kang & Chan, 2004), in situ formation of dispersoids via a chemical reaction within the matrix phase (Cui et al., 2000), spray synthesis (Chawla, 1998), casting techniques (Rohatgi et al., 1986) and elecrodeposition (Clark et al., 1997). Processing methods, such as powder metallurgy (Heian et al., 2004; Kawasaki & Watanabe, 1997, 2002) and thermal spraying (Hamatani et al., 2003; Khor et al., 2001, 2003; Polat et al., 2002; Prchlik et al., 2001), cannot easily tailor the composition in a functional manner. Typically, thermal sprayed composite coatings are made using premixed powders with a given ratio of the constituent phases. This limits the production as well as the design flexibility. Further, a spray deposition approach involving direct spraying of nano-sized powders, has a number of limitations (Rao et al., 1997; Skandan et al., 2001). The primary issue is the introduction of nano-sized powders into the high velocity thermal spray jet and their impingement on the substrate. Nano-sized powders tend to agglomerate, resulting in plugged particle feed line, and the extremely small particles do not readily penetrate the jet. Also, impingement on to the substrate is difficult as the small powders follow the gas streamlines. An alternative methodology is to introduce a liquid or gaseous precursor, which reacts in flight to form nanosized particles (Rao et al., 1997; Xie et al., 2004). This approach is very promising, and has worked well for several material systems. Combustion synthesis using liquid precursors has been used to deposit a number of different high temperature oxide coatings, including Al2O3, Cr2O3, SiO2, CeO2, some spinel oxides (MgAl2O4, NiAl2O4), and yttria stabilized zirconia (YSZ) (Hampikian & Carter 1999). For example, using a solution of aluminum acetylacetonate in ethanol, alumina was deposited at temperatures of approximately 850, 1050, and 1250°C (Hendrick et al., 1998). Similarly, SiO2 has been deposited by combustion synthesis of ethanol containing tetrathyloxysilicate precursor.

As for the production of nanoparticle dispersed microcrystalline coating by thermal spray technique, different approaches have been adopted, such as agglomeration of nano-sized particles with a binder used in the Co-WC cermet (Skandan et al., 2001) or premixing of dispersoid phase with the matrix powder (Laha et al., 2004, 2007; Bakshi et al., 2008). However, these approaches also suffer from the same design inflexibility mentioned above. This case study presents an innovative approach to synthesize ultrafine/nano particulate dispersed (Al2O3, SiO2) NiCr alloy coatings. A novel process called "Hybrid Spray Technique" (Kosikowski et al., 2005) has been employed to fabricate these functionally engineered coatings in a single step. The rationale behind the selection of the dispersoid phases, their liquid precursors and the particulate distribution layout is presented. The influence of these dispersoid phases on the functional characteristics of the resulting coatings is discussed.

#### **5.1 Processing and testing of high temperature coatings**

The "hybrid spray" process utilized in this study was conceptualized in our laboratory at the University of Michigan (Kosikowski et al., 2005). This process combines the arc and high velocity oxy fuel (HVOF) spray techniques; molten metal at the arcing tip is atomized and rapidly propelled to the substrate by a HVOF jet. This so called "hybrid" concept shown in Fig. 5 offers many advantages.

Various approaches have been adopted to disperse the second phase particles into bulk matrix phase, such as mechanical alloying/powder metallurgy (Kang & Chan, 2004), in situ formation of dispersoids via a chemical reaction within the matrix phase (Cui et al., 2000), spray synthesis (Chawla, 1998), casting techniques (Rohatgi et al., 1986) and elecrodeposition (Clark et al., 1997). Processing methods, such as powder metallurgy (Heian et al., 2004; Kawasaki & Watanabe, 1997, 2002) and thermal spraying (Hamatani et al., 2003; Khor et al., 2001, 2003; Polat et al., 2002; Prchlik et al., 2001), cannot easily tailor the composition in a functional manner. Typically, thermal sprayed composite coatings are made using premixed powders with a given ratio of the constituent phases. This limits the production as well as the design flexibility. Further, a spray deposition approach involving direct spraying of nano-sized powders, has a number of limitations (Rao et al., 1997; Skandan et al., 2001). The primary issue is the introduction of nano-sized powders into the high velocity thermal spray jet and their impingement on the substrate. Nano-sized powders tend to agglomerate, resulting in plugged particle feed line, and the extremely small particles do not readily penetrate the jet. Also, impingement on to the substrate is difficult as the small powders follow the gas streamlines. An alternative methodology is to introduce a liquid or gaseous precursor, which reacts in flight to form nanosized particles (Rao et al., 1997; Xie et al., 2004). This approach is very promising, and has worked well for several material systems. Combustion synthesis using liquid precursors has been used to deposit a number of different high temperature oxide coatings, including Al2O3, Cr2O3, SiO2, CeO2, some spinel oxides (MgAl2O4, NiAl2O4), and yttria stabilized zirconia (YSZ) (Hampikian & Carter 1999). For example, using a solution of aluminum acetylacetonate in ethanol, alumina was deposited at temperatures of approximately 850, 1050, and 1250°C (Hendrick et al., 1998). Similarly, SiO2 has been deposited by combustion synthesis of

As for the production of nanoparticle dispersed microcrystalline coating by thermal spray technique, different approaches have been adopted, such as agglomeration of nano-sized particles with a binder used in the Co-WC cermet (Skandan et al., 2001) or premixing of dispersoid phase with the matrix powder (Laha et al., 2004, 2007; Bakshi et al., 2008). However, these approaches also suffer from the same design inflexibility mentioned above. This case study presents an innovative approach to synthesize ultrafine/nano particulate dispersed (Al2O3, SiO2) NiCr alloy coatings. A novel process called "Hybrid Spray Technique" (Kosikowski et al., 2005) has been employed to fabricate these functionally engineered coatings in a single step. The rationale behind the selection of the dispersoid phases, their liquid precursors and the particulate distribution layout is presented. The influence of these dispersoid phases on the functional characteristics of the resulting

The "hybrid spray" process utilized in this study was conceptualized in our laboratory at the University of Michigan (Kosikowski et al., 2005). This process combines the arc and high velocity oxy fuel (HVOF) spray techniques; molten metal at the arcing tip is atomized and rapidly propelled to the substrate by a HVOF jet. This so called "hybrid" concept shown in

ethanol containing tetrathyloxysilicate precursor.

**5.1 Processing and testing of high temperature coatings** 

coatings is discussed.

Fig. 5 offers many advantages.

Fig. 5. (a) Schematic of hybrid gun and (b) hybrid gun in operation.

The hybrid process offers all benefits of wire stock and productivity of electric arc spraying combined with noticeably improved coating density of HVOF. In addition to introducing material through arcing mechanism, if desired, powder/liquid/gas precursors can also be fed through the HVOF coaxial feed line (Fig. 5a). This enables us to tailor the composition inflight by introducing particles into the HVOF jet, to cater to specific property requirements of a composite coating. This unique capability completely eliminates the necessity of processing and handling of the ultrafine particulates prior to feeding them into the hybrid gun. Synthesizing and introducing ultrafine and nano dispersoids inflight in a functional manner to produce composite coatings by the hybrid technique is quite unique in terms of simplicity compared to any other processes. A comparative picture of the steps involved in processing of particulate reinforced composites by conventional routes versus our approach is presented in Table 1.


Table 1. List of precursors used.

Following the above mentioned approach of inflight synthesis, different oxide ceramic particles were introduced into the NiCr (55/45 wt.%) alloy coating. The following coatings were deposited onto mild steel coupons for characterization: (a) NiCr only, (b) NiCr + Cr2O3, (c) NiCr + Al2O3, and (d) NiCr + SiO2. Along with these coatings, NiCr coatings using a twin wire arc spray process (TAFA 3830, Praxair Surface Technologies, Indianapolis, IN) were also deposited for comparison purposes. The arc current and voltage for both the processes were kept at 100 amps and 36 volts, respectively. The HVOF gas pressures were

Corrosion of Metal – Oxide Systems 283

Fig. 6. (a) Hot erosion test set up, (b) corrosion cell, and (c) sample for hot corrosion test.

Fig. 7. (a) SEM picture of NiCr coating with dispersed Al2O3 particulates and (b) higher

magnification SEM picture of NiCr coating with dispersed Al2O3 particulates.

Fig. 7a, presents the general cross section microstructure of a NiCr coatings with embedded alumina particles produced by the hybrid spray process. The coating is very dense and exhibits the characteristics of an HVOF coating rather than of an arc sprayed coating. The hybrid spray process is unique in the sense that while it yields comparable density to that of the HVOF process, the deposition rate is closer to that of an arc spray process. The observed density is advantageous for high temperature corrosion and erosion performance of the coatings. Details on the corrosion and erosion performance of the coatings are discussed in the forthcoming sections. The dispersion of the alumina particles (dark phase) in the NiCr

**5.2 Microstructural analysis of high temperature coatings** 

(a) (b)

matrix is shown in Fig. 7b.

maintained at 50/65/80 psi of propylene/oxygen/air, respectively. The Aluminum nitrate and Tetraethoxysilane precursors were fed from separate reservoirs, however, they were mixed together prior to the injection into the combustion jet. The atomization of the liquid was achieved by a two fluid injector. Liquid precursors up to 100 cc/min were fed to the HVOF jet coaxially.

Table 1 lists the liquid precursors employed for the synthesis of the dispersoid phase particles. The rationale behind the selection of the dispersoids (SiO2, and Al2O3,) and their influence on the properties is as follows.


Microstructural analysis of the coatings was done using electron microscopy (SEM/TEM). The oxidation characteristics of the coatings were characterized on a TA instruments SDT Q600 model for thermogravimetric analysis (TGA). For functional property characterization, coatings were tested for hot erosion, wet corrosion and hot corrosion; and compared with 304 stainless steel, as well as alloy 625 overlay cladding. The hot erosion test setup consisted of a grip for holding and rotating (80 rpm) the coated samples while heating with a heat source (HVOF flame), and an alumina grit (250 mesh) delivering system at a fixed angle (450) as shown in Fig. 6a. The flow rate of the grit was 60 gm/min and the applied grit carrier air pressure was 15 psi at a rate of 42 SCFM. Testing was done at 750 0C for 3 minutes on spray-coated cylinders. Wet corrosion tests were done at room temperature in a dilute 0.1% NaCl solution. NiCr coatings sprayed by the hybrid and arc techniques were tested using an electrochemical cell shown in Fig 6b. Electrochemical experiments were performed using a Solartron (Hampshire, England) SI 1287 potentiostat at the open circuit potential for two different time periods (0hrs and 24 hrs). Hot corrosion tests were carried out by applying film of sulfates and chlorides (potassium, sodium and iron) on to the surface of coated samples (304 stainless steel caps) as shown in Fig. 6c. Samples were initially weighed, and then their surfaces were coated with a solution of sulfate/chloride mixed with water in a weight ratio of 1:1. The samples were carefully masked to ensure salt solution only covered the sprayed coating and the area coated with salt solution was also measured. The solution was dried to leave a film of salt on the surface of the sample. The masking material was removed and the sample was weighed again. Samples were then placed in an oven at 9000 C for 24 hours. This test also included samples of bare 304 stainless steel cap as well as alloy 625 overlay cladding. After the hot corrosion test, weight loss/gain of the samples was measured to evaluate the corrosion resistance.

maintained at 50/65/80 psi of propylene/oxygen/air, respectively. The Aluminum nitrate and Tetraethoxysilane precursors were fed from separate reservoirs, however, they were mixed together prior to the injection into the combustion jet. The atomization of the liquid was achieved by a two fluid injector. Liquid precursors up to 100 cc/min were fed to the

Table 1 lists the liquid precursors employed for the synthesis of the dispersoid phase particles. The rationale behind the selection of the dispersoids (SiO2, and Al2O3,) and their

 The silica particles are expected to provide both creep and crack resistance. It has also been demonstrated that the presence of SiO2 enhances the high temperature resistance

 The presence of alumina is expected to provide enhanced high temperature corrosion resistance. Also, the introduction of SiO2 into alumina based coatings has been found to form mullite and reduce the cracking within the coating (Marple et al., 2001). Mullite is

Microstructural analysis of the coatings was done using electron microscopy (SEM/TEM). The oxidation characteristics of the coatings were characterized on a TA instruments SDT Q600 model for thermogravimetric analysis (TGA). For functional property characterization, coatings were tested for hot erosion, wet corrosion and hot corrosion; and compared with 304 stainless steel, as well as alloy 625 overlay cladding. The hot erosion test setup consisted of a grip for holding and rotating (80 rpm) the coated samples while heating with a heat source (HVOF flame), and an alumina grit (250 mesh) delivering system at a fixed angle (450) as shown in Fig. 6a. The flow rate of the grit was 60 gm/min and the applied grit carrier air pressure was 15 psi at a rate of 42 SCFM. Testing was done at 750 0C for 3 minutes on spray-coated cylinders. Wet corrosion tests were done at room temperature in a dilute 0.1% NaCl solution. NiCr coatings sprayed by the hybrid and arc techniques were tested using an electrochemical cell shown in Fig 6b. Electrochemical experiments were performed using a Solartron (Hampshire, England) SI 1287 potentiostat at the open circuit potential for two different time periods (0hrs and 24 hrs). Hot corrosion tests were carried out by applying film of sulfates and chlorides (potassium, sodium and iron) on to the surface of coated samples (304 stainless steel caps) as shown in Fig. 6c. Samples were initially weighed, and then their surfaces were coated with a solution of sulfate/chloride mixed with water in a weight ratio of 1:1. The samples were carefully masked to ensure salt solution only covered the sprayed coating and the area coated with salt solution was also measured. The solution was dried to leave a film of salt on the surface of the sample. The masking material was removed and the sample was weighed again. Samples were then placed in an oven at 9000 C for 24 hours. This test also included samples of bare 304 stainless steel cap as well as alloy 625 overlay cladding. After the hot corrosion test, weight loss/gain of the samples was

known for its excellent creep resistance (Dokko et al., 1977; Lessing et al., 1975). It has also been found that the presence of chromia aids in - alumina formation, as well as limits the phase transformations during heating to temperatures below 1200 0C (Marple et al., 2001; Chraska et al., 1997). Therefore, chromium nitrate was added to the

HVOF jet coaxially.

influence on the properties is as follows.

measured to evaluate the corrosion resistance.

of chromia scale (Carter et al., 1995; Liu et al., 2004).

aluminum nitrate precursor to stabilize the - alumina phase.
