Journal of Minerals & Materials Characterization & Engineering, Vol. 11, No.3, pp.285-302, 2012
jmmce.org Printed in the USA. All rights reserved
High Temperature Oxidation and Hot Cor ro sion Be ha viour of Yttria-
Stabilised Zirc onia as Plasma Sprayed Coating in Air and Salt
at 900°C under C yclic Condition
Dinesh Gonda*, R.S. Lalbondreb, D. Puric, S. Prakashc
aHEEP, Bharat Heavy Electricals Ltd. (Government of India Undertaking) Haridwar, India.
b Mechanical Engineering Department, National Institute of Technology, Suratkal, India
cMetallurgical & Materials Engineering Department, Indian Institute of Technology
*Corresponding author: firstname.lastname@example.org, email@example.com.
Yttria-Stabilised Zirconia (YSZ) coatings were deposited on a T-91 boiler steel. NiCrAlY was
used as bond coat and YSZ as top coat. Hot corrosion studies were conducted on uncoated as
well as plasma spray coated specimens in air as well as salt (75wt. % Na2SO4 + 25wt. %
NaCl) at 900°C under cyclic conditions. The thermogravimetric technique was used to
establish kinetics of corrosion. X-ray diffraction (XRD) and scanning electron
micros co p y/energ y-dispersive x-ray analysis (SEM/EDAX) techniques were used to analyse
the corrosion products. This YSZ overlay coatings enhance resistance to corrosion
significantly which can be attributed to formation of zirconium oxides (ZrO2) and yttrium
oxide (Y2O3). This coating was more effective in salt environment and there is an extra phase
Keywor d s: Hot corrosion; T-91; Plasma spray coating.
286 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
In a wide variety of applications, mechanical components have to operate under severe
conditions, such as high load, speed or temperature and hostile chemical environment. Thus,
their surface modiﬁcation is necessary in order to protect them against various types of
degradation. Ceramic coatings produced by thermal spray techniques are widely used for a
range of industrial applications, to confer wear and erosion resistance, corrosion protection
and thermal insulation [1–4].
Thermal barrier coatin g (TBC) s ystems are used in thermal insulating components in the hot
sections of gas turbines in order to increase operational temperature with better efficiency [5–
11]. Yttria stabilized zirconia (YSZ) has been usually chosen for the top insulating coat
material because of its high thermal expansion coefficient, which closely matches that of the
substrate. [6,7]. Apart from this application TBC is also useful in aerospace, aircraft and
The different functions of the coating, such as wear and corrosion resistance, thermal or
electric al i nsulat ion can be ach iev ed usi ng diff ere nt coat ing t echniqu es an d co ating material s.
The purpose of a hot corrosion resistant coating is to serve as an effective solid-state
diffusion barrier between oxygen (or other gases) and base metal .
Mostly metals and alloys experience accelerated oxidation when their surfaces are covered
with a thin film of fused salt in an oxidising gas atmosphere at elevated temperatures. This is
known as hot corrosion where a porous non-protective oxide scale is formed at the surfaces
and sulphides in the substrate .
The research work deals with development of NiCrAlY as bond coat and YSZ as top coat on
T-91 boiler steels and their characterisation. X-ray diffraction (XRD) and scanning electron
micros co py/ener gy-dispersive analysis (SEM/EDAX) techniques have been used to
characterise coating and respective corrosion products after hot corrosion at 900 °C.
2. EXPERIMENTAL PROCEDURE
Vol.11, No .3 High temperature oxidation and hot corrosion 287
2.1. Development of Coatings
2.1.1. Substrate material
The experimental work was performed by using samples of T-91 boiler steel. The T-91 steel
samples were obtained from Gurunank Dev Power plant, Bhatinda, Punjab, India. The
spectroscopic analysis of candidate material is given below in Table 1.
Table 1: Spectroscopic analysis of T-91 boiler steel.
Type of steel C Mn Si Cr Mo Cu Fe
T-91 0.0607 0.3874 0.2297 8.078 0.8029 0.1168 Balance
The specimens each measuring approximately 20 x 15 x 3.5 mm was obtained from T-91
boiler pipe. The specimens were polished and grit blasted with alumina powders (grit 60)
before being plasma sprayed.
2.1.2. Coating powders
Yttria stabilised zirconia (YSZ; ZrO2 – 8wt. % Y2O3) and NiCrAlY (Ni–22Cr–10Al–1Y) is
been used for TBC coating which were applied on samples by plasma spray process. The
chemical composition and particle size for these powders are given in Table 2.
Table 2: Composition, mean particle size and manufacturing of coating powders.
powder Composition (wt. %)
Mean parti cl e
size (µm) Manufacturer
Cr (21-23), Al (7-9), Y (0.8-1.2), Ni
(Balan ce) 38-106 METCO, Corp. USA
YSZ Y2O3 (8), ZrO2(Balance) 0.024 Tosho, Corp., Japan
2.1.3. Coating formulation
Samples were grit blasted before plasma spraying. 40 kW Miller thermal plasma spray
apparatus available with Anod Pl asma Spray Ltd., Kanpur (India) has been used to apply the
288 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
coatings. Argon was used as powder carrying and shielding gas. All the process parameters
including the spray distance were kept constant throughout coating process. Ni–22Cr–10Al–
1Y powder was sprayed as a bond co at of around 150 µm thickness before appl ying the ﬁnal
coatings of YSZ around 200µm and the process parameters were as reported in Table 3.
Table 3: Parameters of argon shrouded plasma spray process used for coating.
Arc current (A)
Arc voltage (V)
Powder ﬂow rate (rev/min)
Spraying distance (mm)
Plasma arc gas (argon) (psi)
Carrier gas (psi)
2.1.4. Porosity measurement
Coated samples were subjected to porosity measurements with the help of Image Analyser
having software of Dewinter Material Plus 1.01 based on ASTM B487. The images were
obtained through the attached PMP3 Inverted Metallurgical Microscope made in Japan. The
porosity values were then determined.
2.2. High Temperature Oxidation Study in Air and Salt
Hot corrosion studies were conducted at 900°C in laboratory using silicon carbide tube
furnace having PID temperature controller (make Digitech, India). The bare samples were
subjected to mirror polishing including cloth polish. Dimensions were accurately measured
by digital vernier (make Mototoyo, Japan) to calculate area of sample. Finally specimens
were cleaned i.e. degreased b y ethanol and kept in alumina boat. Prior to ex periment alumina
boat was kept in oven for 5hr at 250°C in oven and then kept in furnace at 900°C for
2hr to expel all the moisture. After this samples of T-91 bare steel were kept in alumina boat
and then inserted in the tubular furnace for 1 hr at a temperature of 900°C and then they were
removed and cooled further for 20 minutes to room temperature and their weights were
measured. In case of hot corrosion in the given sal t environment of 75wt. % Na2SO4 + 25wt.
% NaCl fo r as spra yed samples each cycle con sist ed of 1 hr heating at 900°C followed by 20
min. cooling at room temperature.
Vol.11, No .3 High temperature oxidation and hot corrosion 289
The salt coating of uniform thickness with 3–5mg/cm2 of 75wt. % Na2SO4 + 25wt. % NaCl
was applied with camel hairbrush on the preheated samples (250°C). After the salt
application the samples were kept in an oven for 2 ½ hr at 250°C and then cyclic oxidation
test was carried out o n samples . The samples were subj ected to wei ght change me asurements
after visual observation at the end of each cycle. Weight was taken with help of Electronic
Balance Model CB-120 (Contech, Mumbai, India) with a sensitivity of 0.001 gms. Burnt
oxide layer which were spalled out in boat were also taken into consideration i.e. the weight
was taken along wit h the boat . This c ycle was r epeated fo r 50 times i.e. 50 c ycles were mad e
for each sample. Corroded samples from air and salt environment were analysed by
XRD (BRUKER-binary V3) and SEM/EDAX and the oxide scale which fell into the boat
were also anal ysed by XRD. Cu radiation was used in XRD at a step of 2°/min and the range
of angle was 5-100°.
3. EXPERIMENTAL RESULTS
3.1. Behaviour in Air and Salt at Elevated Temperature
The weight gain plots for the substrate without coating and with coatings have been shown in
Fig. 1 in the presence of air and salt layer of 75wt. % Na2SO4 + 25%wt NaC l at 900°C. On x-
axis “number of cycles” and on y-axis “weight gai n/area (mg/cm2)” was ta ken. In case o f air
oxidation, hot corrosion behaviour of T-91 b are steel in air was so mewhat linear becaus e the
oxi de la yer fo rmed on subs trate used to p eel of ver y easily and as compared to this oxidation
rate of T-91 YSZ coated sample was too less i.e. nearly 53.79% less as compared to bare
steel. In case of salt oxidation, T-91 bare steel be haviour was parabolic but T-91 YS Z coated
sample showed more resistance to oxidation than the bare sample i.e. nearly 73.58% less as
compared to bare steel . The grap h rev eals that T -91 YS Z coated steel is bet ter t han T-91 bare
steel in an environment of air and salt for 50 cycles. Fig. 2 shows plot of (weight
gain/ar ea)2 vs. Number of cycles. In this plot every curve is associated with straight line of
same colour. This straight line is trend line and it is used to calculate rate constant (Kp) which
is given in Table 4.
Every line or curve in graph is having its approximate equation which is given below.
For T-91 air oxidised bare sample the approximated curve equation is
290 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
Y= -6.86739 + 2.66488*X -0.00851*X^2
Fig 1. Wei ght gain vs. number of cycles plot for coated Fig 2. (Weight gain/a rea)2 vs. number of cycles plot
and uncoated T-91 steel subjected to cyclic oxida tion for coated and uncoated T-91 steel subjected to
for 50 cycles in air and salt at 900°C. cyclic oxidation for 50 cycles in air and salt at 900°C
For T-91 air oxidised YSZ coated sample the approximated curve equation is
Y= 1.56652 – 0.13746*X -0.0212*X^2
For T-91 salt oxidised bare sample the approximated curve equation is
Y= 30.52124 – 2.19772*X -0.03*X^2
For T-91 salt oxidised YSZ coated sample the approximated curve equation is
Y= 0.56075 – 0.15298*X -0.00408*X^2
(Where X is number of cycle and Y is weight gain/area & these equation are calculated by
using analysis mode of Origin software)
Table 4: Value of the rate constant Kp
(10-6 g2 cm-4 s-1)
T-91 bare air oxidised
T-91 bare salt oxidised
T-91 YSZ coated air oxidised
T-91 YSZ coated salt oxidised
As shown in macrograph Fi g. 3 (a ) ex trusion of mat erial from beneath and cracks in the scal e
were observed during hot corrosion runs for T-91 bare air ox idised sample but T-91 bare salt
oxidised sample did not showed much more crack or extrusion of material from beneath as is
Vol.11, No .3 High temperature oxidation and hot corrosion 291
evident from Fig. 3(b). Some cracks were observed in T-91 YSZ coated air oxidised sample
Fig. 3(c) and due to this, corrosion occurred beneath the coating while in case of T-91 YSZ
coated salt oxidised sample Fig. 3(d) cracks did not occurred in coating so there was no
corrosion which is revealed in Fig. 7 (c and d).
(a) (b) (c) (d)
Fig.3.Macrograph of (a) T-91 bare air oxidised (b) T-91 bare salt oxidised (c) T-91 YSZ
coated air oxidised (d) T-91 YSZ coated salt oxidised.
3.2. X-Ray Diffraction Analysis
The samp les and th eir s c ales after oxidation were removed from boat and t he y were an al ysed
separately by XRD and after that onl y oxidised sample were anal ysed by SEM /EDAX. The
results of XRD analysis contained graph indicating peak values (i.e. d values) which were
used to identify various phases with the help of inorganic X-ray Diffraction data card from
Powder diffraction file of JCPDS. Help of Philips X’ pert High score soft ware was also t aken
for finding out compounds at respective peaks.
3.2.1. XRD result for T-91 bare and YSZ coated air and salt oxidised sample
From the X-Ray Diffraction analysis it is found that ferrous oxide (Fe 2O3), chromium ferrous
oxide (Cr, Fe) 2O3 are mainly formed along with Cr2O3 in T-91 bare air oxidised sample Fig.
4 (p and q) and T-91 bare salt oxidised sample Fig. 5 (x and y) . Fe2O3, Cr2O3 form a
protective oxide layer at surface due to which further oxidation is prevented as it acts as
barrier for further corroding media to interact with substrate but at initial stage as the
substrate material was in direct contact of corroding media so th er e was acc el erated cor ros io n
at initial stage.
292 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
Fig 4. XRD patterns for T-91 steel subjected to cyclic oxidation in air at 900°C after 50
cycles. (p) T-91 bare sample (q) T-91 bare sputtered scales (r) T-91 YSZ coated sample (s)
T-91 YSZ coated sputtered scales.
Fig 5. XRD patterns for T-91 steel subjected to cyclic oxidation in Na2SO4+25 wt.% NaCl
salt at 900°C after 50 cycles. (x) T-91 bare sample (y) T-91 bare sputtered scales (z) T-91
YSZ coated sample.
Vol.11, No .3 High temperature oxidation and hot corrosion 293
In case of coated samples the case of accelerated corrosion was absent due to the overlay
coating of Yttria stabilised zirconia (YSZ). In T-91 YSZ coated air oxidised sample Fig. 4(r
and s) and T-91 YS Z coat ed salt oxidised sample Fig. 5 ( z ) there is formation of mainly ZrO2,
Y2ZrO3 and in case of YSZ coated salt oxidised sample apart from this ZrS was also formed.
3.3. Energy Dispersive X-Ray (EDAX) Studies
3.3.1. Surface scale
The SEM/EDAX analysis for T-91 bare sample after oxidation in air for 50 cycles at 900°C
is shown in Fig. 6 (a). The oxide scale reveals the dominance of Fe 2O3 and along with this
compounds of Mo2O3 and Cr2O3 are also formed. The obtained morphology indicates that
the oxide formed is layer-wise i.e. one below the other and the weight wise composition is
approximately same but it greatly differs in case of Cr content. The upper layer contains
nearly no Cr but the lower layer is rich in Cr content. T-91 bare salt oxidised sample Fig 6(b)
reveals that the oxide formed is layer wise and it contains granules. Analysis of these
granules revealed that they were formed when the amount of chromium oxide was less in it
i.e. at about 1-2%.and it showed some cracking in oxide layer.
(a) T-91 bare air oxidised sample at scale of 100µm
294 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
(b) T-91 bare salt oxidised sample at scale of 100µm
(c) T-91 YSZ coated air oxidised sample at scale of 50µm
(d) T-91 YSZ coated salt oxidised sample at scale of 50µm
Fig. 6.Surface scale morphology and EDAX analysis (wt. %) for T-91 bare and YSZ coated
sample subjected to the cyclic oxidation at 900°C for 50 cycles in air and 75 wt. %
Na2SO4+25 wt. % NaCl salt environment.
EDAX analysis of T-91 YSZ coated air oxidised sample Fig. 6(c) reveals the formation of
ZrO2 and Y2O3 which prevented the oxidising media to interact directly with substrate but in
this cracki n g of coat i n g o ccured henc e co rr osi on o ccu red b ene at h t he co at i ng. In case of T-91
YSZ coat ed salt ox idised s ample Fi g. 6(d) along with formation of ZrO 2 and Y 2O3, there is
an extra phase of ZrS as analysed from XRD pattern.
3.3.2. Cross-sectional scale
The cross sectional analysis of T-91 bare air oxidised sample Fig. 7 (a) shows a thin oxide
layer formed on surface which shows that till point 5 all elements are constant in weight
percent and after that ferrous starts to deplete and oxygen rises slightly. At point 8 all the
elemental wt . % goes down. In T -91 bare salt oxidised sample Fig. 7 (b) three distinct layers
Vol.11, No .3 High temperature oxidation and hot corrosion 295
can be seen and first two layers have same composition without any variation in wt. % of
elements which shows that second layer is also parent material but it has parted of from
subst r at e. Cross sectional analysis of T-91 YSZ coated air oxidised sample Fig. 7 (c) shows
that corrosion occurred between the substrate and coating layer i.e. between point 2 and 7. It
can be seen that at point 2 there is start of corrosi on which is separated clearly from substrate
and from point 3 to 6 wt. % of f errou s and oxygen is high as compared to ot her. From point 7
to 8 bond coat layer is present which is revealed by presence of nickel and at point 9 small
proportion of yttrium and zirconium layer along with ferrous and oxygen is present . Th is case
of intermediate corrosion occurred due to cracking of coating and penetration of corroding
media through it. In case of T-91 YSZ coated salt oxidised sample Fig. 7 (d) there was no
corrosion at substrate as the wt. % of ferrous wen t on depleting. From point 2-4 it shows th e
presence of bond coat and from point 5-7 it shows the high wt. % of zirconium and yttrium
which shows the presence of YSZ top coat.
Elemental x-ray mapping analysis of T-91 bare air oxidised sample is shown in Fig.8. The
micrograph indicates a thin oxide scale which mainly contains chromium and oxygen with
some amount of manganese.
In case of T-91 bare salt oxidised sample more protection is achieved than T-91 bare air
oxidised sample. From Fig.9 three layers are observed and in this first two layers are of
substrate, the only thing is that second layer is cracked and parted off from parent substrate
material where little accumulation of oxygen is revealed and chromium is fairly distributed
all over, but as compared to ferrous, chromium has very dense layer in oxide scale along with
oxygen as revealed from Fig.9. In the initial region of third layer a dense layer of
molybdenum is also present. Hence here also we can sa y that Cr and O is playing major role
for achieved protection.
According to cross-sectional study of T-91 YSZ coated air oxidised sample and macroscopic
view Fig. 3(c) and Fig.10 it is observed that protective coating is cracked and the oxidising
media has entered through these discontinuities and corrosion has occurred beneath the
coating. According to elemental mapping it is observed that Al is diffused towards substrate
material from bond coat.
296 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
(a) T-91 bare air oxidised sample (b) T-91 bare salt oxidised sample
(c) T-91 YSZ coated air oxidised sample (d) T-91 YSZ coated salt oxidised sample
Fig.7. Oxide scale morpholo gy and elementa l c omposition v a riation across the cross section of T-91 bare and
YSZ coated sample exposed to air and salt environment at 900°C for 50 cycles.
Substrate Oxide Substrate Oxide
Substrate Oxide Coating Substrate Coating
Vol.11, No .3 High temperature oxidation and hot corrosion 297
In this layer wise corrosion occurred and the comprising layers are of Fe, Cr and O. From Fig
10 it is also revealed that due to cracking of coating layer the corrosion product is also
formed at surface of sample. Fe is diffused at surface from the crack and presence of O is also
reveal ed i n t hat region an d along with this aluminium from bond coat is also diffused towards
Fig. 8. BS EI and elemen tal X-ray mapping of the cross-section of T-91 bare sample exposed
to cyclic hot corrosion in air at 900°C for 50 cycles.
According to cross-sectional study of T-91 YSZ coated salt oxidised sample Fig.10 it is
observed that very high rate of corrosion protection is achieved and bond coat as well as top
coat both are in well intact of substrate material. From Fig. 10 it is also observed that some
Fe and Al are diffused towards surface and reveals the presence in pockets of top coat. In this
mainly yttrium is dispersed all over the area uniformly and a dense layer of zirconium is
present in the region of YSZ top coat.
Internal oxidation further led to the cracking of the scale due to the different thermal
expansion coefficients of oxides in the scale from that of coating as suggested by P.
Niranatlumpong . This has further been supported by the findings of R.A. Rapp and
P.S.Liu [15-16], where it has been observed that development of stresses due to difference in
Fe Cr Mn
298 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
thermal expansion coefficients. Through these cracks and irregularities, corrosive gases can
penetrat e to the base material and will thus allow significant grain boundary corrosion attack
[17–19]. Inspite of cracking, in some cases like T-91 air oxidised sample, little weight gain
has been recorded. Zirconia-based TBCs require alloying oxides such as Y2O3, CaO, CeO,
MgO, etc., in order to stabilize a single-phase material, usually in the tetragonal form . At
room temperature the equilibrium phases of yttria partially stabilized zirconia are expected to
be a low yttria content monoclinic phase and a high yttria content cubic phase. However, due
to rapid cooling .During the plasma-spraying process, a non-equilibrium tetragonal phase
takes place [20-22].
Fig.9. BSEI and elemental X-ray mapping of the cross-section of T-91 bare sample exposed
to cyclic hot corrosion at 900°C for 50 cycles in 75 wt. % Na2SO4 + 25 wt. % NaCl salt.
A possible hot corrosion mechanism in zirconia-based TBCs can be divided into three steps.
The first step is salt & other corroding media penetration into the entire thickness of the
zirconia top coating layer through splat boundaries and other coating defects such as
microcracks and open pores. This step is accomplished very fast. The second step is the
reaction of penetrated salts & other corroding media with tetragonal stabilizers in zirconia.
Because each zirconia splat is surrounded by the corroding media in the entire area of the
zirconia coating layer, the depletion of stabilizers in zirconia and consequent phase
transformation to monoclinic can occur in a very rapid and effective manner. Because of the
Substrate Oxi de
Cr Mo Mn
Vol.11, No .3 High temperature oxidation and hot corrosion 299
volume expansion effect, accompanied with monoclinic phase transformation, results in
unexpected failure under thermal shock conditions with a corrosive environment, this step is
crucial and should be carefully considered, especially in the case of YSZ TBC systems. The
final step is macroscale damage by diffusion controlled salt attacks. The failure of YSZ is due
to transformation of zirconia to fully monoclinic, which can be retarded or prevented by
using more acidic stabilizers . The result which were seen till now shows that YSZ
coating is very much effective in providing protection from high temperature corrosion in
case of both air and 75wt. % Na2SO4 + 25wt. % NaCl salt environment. In case of YSZ
coated salt oxidised sample there occurred no cracking till the end of 50 cycles which
occurred in YSZ coated air oxidised sample.
Fig.10. BSEI and elemental X-ray mapping of the cross-section of T-91 YSZ coated air
oxidised sample exposed to cyclic hot corrosion at 900°C for 50 cycles.
300 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
The measured porosity value of plasma sprayed coating was 0.58% and this YSZ coated layer
has provided very high resistance to corrosion and thereby increasing their workable life as
compared to bare sample subjected to corrosion in both condition i.e. air and 75wt. %
Na2SO4 + 25wt. % NaC l salt environment. The cyclic oxidation of T-91 bare steel in air
follow linear rate of weight gain and it has formed mainly hematite (Fe 2O3) at top surf ace. In
case of T-91 bare steel in salt oxidised sample weight gain follows parabolic law and it has
formed chromium iron oxide (Cr, Fe) 2 O3 , chromium oxide Cr 2O3 and hematite (Fe 2O3) at
top su rface. Cyclic oxidation of T-91 YSZ coat ed air oxi dised sampl e resulted in cracking of
coating due to volume expansion effect which resulted in unexpected failure under thermal
shock conditions with corrosive environment but then to also the corrosion rate was too less
as compared to bare sample as shown in Fig.1 and in case of T-91 YSZ coated salt oxidised
sample cracking did not occurred and an extra phase of ZrS was revealed from XRD analysis.
Fig.11. BSEI and elemental X-ray mapping of the cross-section of T-91 YSZ coated sample
exposed to c yclic hot corrosion at 900°C for 50 cycles in salt of 75wt. % Na 2SO4 + 25wt. %
BSEI Fe O
Vol.11, No .3 High temperature oxidation and hot corrosion 301
The oxidation rate of T-91 YSZ coated air oxidised sample was too less i.e. nearly 53.79%
less as compared to bare steel and in case of T-91 YSZ coated salt oxidised sample more
resistance to oxidation than the bare sample was achieved i.e. nearly 73.58% less at 900° C
for 50 cycles.
 K.G. Bundinski, Surface Engineering for Wear Resistance, Prentice-Hall, New Jersey,
 M.K. Hobbs, H. Reiter, Residual stresses in ZrO2–8%Y2O3 plasma sprayed thermal
barrier coatings, in: D.L. Houck (Ed.), Thermal Spray: Advances in Coatings
Technology, ASM International, 1989, 285–290.
 H. Herman, C.C. Berndt, H. Wang, Plasma sprayed ceramic coatings, in: J.B.
Wachtman, R.A. Haber (Eds.), Ceramic Films and Coatings, Noyes Publications, New
 L. Pawlowski, The Science and Engineering of Thermal Spray Coatings, Wiley, New
 A.G. Evans, D.R. Mumm, J.W. Hutchinson, G.H. Meier, F.S. Pettit, Prog. Mater. Sci.
46 (2001) 505.
 J.R. Brandon, R. Taylor, Surf. Coat. Techol. 69 (10) (1992) 75.
 I. Gurrappa, J. Mater. Sci. Lett. 17 (1998) 1267.
 R.L. Jones, J. Therm. Spray Technol. 6 (1) (1997 (March)) 77.
 B.A. Nagaraj, D.J. Wortman, Trans. ASME 112 (1990) 536.
 R. Srinivasan, J.M. Merrilea, Surf. Coat. Technol. 160 (2002) 187.
 R.L. Jones, J. Am. Ceram. Soc. 75 (7) (1992) 1818.
 K. Yamada, Y. Tomono, J. Morimoto, Y. Sasaki, A. Ohmori, Vacuum 65 (2002) 533–
 R.A. Rapp, Y.S. Zhang, JOM, (1994 Dec) 47– 55.
 P. Niranatlumpong, C.B. Ponton, H.E. Evans, Oxid. Met. 53 (3–4) (2000) 241.
 R.A. Rapp, J.H. Devan, D.L. Douglass, P.C. Nordine, F.S. Pettit, D.P.Whittle, Mater.
Sci.Eng.50 (1981) 1.
 P.S. Liu, K.M. Liang, H.Y. Zhou, S.R. Gu, X.F. Sun, H.R. Guan, T. Jin, K.N. Yang,
Surf. Coat. Technol. 145 (2001) 75.
302 Dinesh Gond, R.S.Lalbondre Vol.11, No.3
 S. Danyluk, J.Y. Park, Corrosion 35 (12) (1979) 575.
 D. Wang, Surf. Coat. Technol. 36 (1988) 49.
 S.E. Sadique, A.H. Mollah, M.S. Islam, M.M. Ali, M.H.H. Megat, S.Basri, Oxid. Met.
54 (5–6) (2000) 385.
 R.A.Miller, R.G. Garlick, J.L. Smialek, Ceram. Bull. 62 (12) (1983) 1355.
 A.N. Khan, J. Lu, H. Liao, Mater. Sci. Eng., A Struct. Mater.: Prop.Microstruct.
Process . 359 (2003) 129.
 C. Batista, A. Portinha, R.M. Ribeiro, V. Teixeira, C.R. Oliveira, Surf. Coat. Technol.
200 (2006) 6783–6791.
 S.Y. Park, J.H. Kim, M.C. Kim, H.S. Song, C.G. Park, Surf. Coat. Technol.190 (2005)