enhanced corrosion resistance of mild steel in molar hydrochloric acid solution by...
TRANSCRIPT
Enhanced corrosion resistance of mild steel in molar
hydrochloric acid solution by
1,4-bis(2-pyridyl)-5H-pyridazino[4,5-b]indole: Electrochemical,
theoretical and XPS studies
F. Bentiss a,c, F. Gassama b, D. Barbry b, L. Gengembre d,H. Vezin e, M. Lagrenee a, M. Traisnel f,*
aLaboratoire de Cristallochimie et Physicochimie du Solide, CNRS UMR 8012 ENSCL,
BP 90108, F-59652 Villeneuve d’Ascq Cedex, Franceb Laboratoire de Chimie Organique EA 2692, Bat. C4, USTL, F-59652 Villeneuve d’Ascq Cedex, France
c Laboratoire de Chimie de Coordination et d’Analytique, Universite Chouaib Doukkali,,
Faculte des Sciences, B.P. 20, El Jadida, Moroccod Laboratoire de Catalyse, CNRS UMR 80100, Bat. C3, USTL, F-59652 Villeneuve dAscq Cedex, France
eLaboratoire de Chimie Organique et Macromoleculaire, CNRS UMR 8009, USTL Bat C3,
F-59655 Villeneuve d’Ascq Cedex, Francef Laboratoire des Procedes d’Elaboration des Revetements Fonctionnels, UPRES EA 1040 ENSCL,
BP 90108, F-59652 Villeneuve d’Ascq Cedex, France
Received 9 January 2005; accepted 30 March 2005
Available online 6 June 2005
www.elsevier.com/locate/apsusc
Applied Surface Science 252 (2006) 2684–2691
Abstract
The inhibition effect of the new pyridazine derivative, namely 1,4-bis(2-pyridyl)-5H-pyridazino[4,5-b]indole (PPI) against
mild steel corrosion in 1 M HCl solutions was evaluated using weigh loss and electrochemical techniques (potentiodynamic
polarisation curves and impedance spectroscopy). The experimental results suggest that PPI is a good corrosion inhibitor and the
inhibition efficiency increased with the increase of PPI concentration, while the adsorption followed the Langmuir isotherm. X-
ray photoelectron spectroscopy (XPS) and theoretical calculation of electronic density were carried out to establish the
mechanism of corrosion inhibition of mild steel with PPI in 1 M HCl medium. The inhibition action of this compound was,
assumed to occur via adsorption on the steel surface through the active centres contained of the molecule. The corrosion
inhibition is due to the formation of a chemisorbed film on the steel surface.
# 2005 Elsevier B.V. All rights reserved.
Keywords: Corrosion inhibition; Mild steel; Pyridazine; HCl solution; Adsorption
* Corresponding author. Tel.: +33 320 436 658; fax: +33 320 436 658.
E-mail address: [email protected] (M. Traisnel).
0169-4332/$ – see front matter # 2005 Elsevier B.V. All rights reserved.
doi:10.1016/j.apsusc.2005.03.231
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–2691 2685
Fig. 1. Molecular structure of PPI.
1. Introduction
Acid solutions are generally used for removal of
undesirable scale and rust in several industrial
processes. The use of inhibitors is one of the most
practical methods for protection against corrosion in
acid solutions because they prevent metal dissolution
and acid consumption [1] and, during the past decade,
many inhibitors have been studied in different media
[2–8]. The mechanism of their action can be different,
depending on the metal, the medium and the structure
of the inhibitor. One possible mechanism is the
adsorption of the inhibitor, which blocks the metal
surface and thus do not permit the corrosion process to
take place. The existing data show that most organic
inhibitors get adsorbed on the metal surface by
displacing water molecules and form a compact
barrier film. Availability of lone pairs and p electrons
in inhibitors molecules facilitate electron transfer
from the inhibitor to the metal, the strength of the
resulting chemisorption bond depends on electronic
density on the donor atom of the functional group and
also on the polarisability of the group. It is well known
that heterocyclic compounds containing nitrogen
atoms are good corrosion inhibitors for many metals
and alloys in various aggressive media. The inhibiting
effect of some derivatives of indole on the corrosion of
mild steel or copper in acidic media has been reported
[9,10] as well as these of some pyridazine derivatives
[11].
The present work reports the use of a new
heterocyclic derivative, the 1,4-bis(2-pyridyl)-5H-
pyridazino[4,5-b]indole (PPI) which have the parti-
cularity to possess both indole and pyridazine parts,
as corrosion inhibitor in 1 M HCl medium. The
presence of several nitrogen atoms in PPI is an
opportunity to understand and explain the mechan-
ism of the inhibition and the type of adsorption on
the metal surface. The influence of PPI on the
corrosion inhibition in 1 M HCl solution was
investigated by weight loss measurements, electro-
chemical techniques: potentiodynamic polarisation
method and electrochemical impedance spectro-
scopy (EIS) and by X-ray photoelectron spectro-
scopy (XPS). Molecular modelling has been
conducted in attempt to correlate the corrosion
inhibition properties with the calculated quantum
chemical parameters [12,13].
2. Experimental details
2.1. Materials
The synthesis of the inhibitor, namely 1,4-bis(2-
pyridyl)-5H-pyridazino[4,5-b]indole (PPI) has been
described elsewhere [14–17]. PPI was prepared
through an inverse electron-demand Diels-Alder
reaction between 3,6-bis(2-pyridyl)-1,2,4,5-tetrazine
and indole. Its molecular formula is shown in Fig. 1.
Mild steel strips composed of (wt%): 0.09% P, 0.38%
Si, 0.01% Al, 0.05% Mn, 0.21% C, 0.05% S, and
balance Fe were pre-treated prior to the experiments
by grinding with emery paper SiC (grades 600 and
1200), then cleaned in ultrasonic bath with ethanol,
rinsed with doubly distilled water and finally dried at
room temperature. The solutions (1 M HCl) were
prepared by dilution of an analytical reagent grade
37% HCl with doubly distilled water. The concentra-
tion range of PPI employed was 1 � 10�5 M to
1 � 10�4 M.
2.2. Weight loss measurements
Gravimetric experiments were carried out in a
double glass cell equipped with a thermostated cooling
condenser. The solution volume was 100 ml. The steel
specimens used have a rectangular form (length =
2 cm, width = 1 cm, thickness = 0.06 cm). The max-
imum duration of tests was 24 h at 30 8C � 1 8C in non-
de-aerated solutions. At the end of the tests, the
specimens were carefully washed in ethanol under
ultrasound and then weighed. Duplicate experiments
were performed in each case and the mean value of the
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–26912686
weight loss is reported. Weight loss allowed calculation
of the mean corrosion rate in mg cm�2 h�1.
2.3. Electrochemical techniques
Electrochemical experiments were carried out by
means of impedance equipment (Tacussel-Radiometer
PGZ 3O1) and controlled with Tacussel corrosion
analysis software (Voltamaster 4). Electrochemical
experiments were carried out in a standard glass three-
electrode cell with a capacity of 500 ml for polarisa-
tion curves and a polymethyl methacrylate (PMMA)
cell with a capacity of 1000 ml for electrochemical
spectroscopy measurements.
2.3.1. Polarisation curves
The electrochemical tests were performed as
follows: the disc formed working electrode exposing
surface of 1 cm2, the platinum counter-electrode and
the reference saturated calomel electrode (SCE) filled
in a Luggin’s capillary bridge were placed in a
conventional three-electrode glass cell. The solutions
under continuous agitation were deaerated by bub-
bling with a nitrogen stream at 30 8C. The potential
applied to the working electrode ranges from �800 to
0 mV at a rate of 500 mV s�1. The procedure adopted
for the polarisation measurements was the same as
described elsewhere [18]. Inhibition efficiencies were
determined from corrosion currents calculated by the
Tafel extrapolation method and fitting the curve to the
polarisation equation.
2.3.2. Electrochemical impedance spectroscopy
(EIS)
Impedance spectra were obtained using TACUS-
SEL RADIOMETER PGZ 3O1 Frequency Response
Analyser in a frequency range in the frequency range
100 kHz to 10 mHz with 10 points per decade at the
corrosion potential after 24 h of immersion. Tests were
performed in a PMMA cell with a capacity of 1000 ml.
Square sheets of mild steel of size (5 cm � 5 cm �0.06 cm), which exposed a 7.55 cm2 surface to the
agressive solution, were used as the working electrode.
All tests have been performed at 30 8C in non-de-
aerated solutions under unstirred conditions. After the
determination of steady-state current at a given
potential, sine wave voltages (10 mV) peak to peak
were superimposed on the rest potential. The
impedance data were analysed and fitted using
graphing and analysing impedance software, version
(Voltamaster 4).
2.4. X-ray photoelectron spectroscopy (XPS)
Rectangular mild steel specimens of dimensions
5 cm � 2 cm � 0.6 cm were immersed in 1 M HCl
with 1 � 10�4 M of PPI at 30 8C during 24 h. After
removal from acid solution, the sample was rinsed
with ethanol and then dried at room temperature. A
pure sample of PPI has also been analysed for
comparison. Surface analyses were performed with an
VG ESCALAB 220 XL spectrometer, using a
monochromated Al Ka X-ray source (1486.6 eV).
The experimental details of this analysis have been
previously reported by Bentiss et al. [18].
2.5. Theoretical calculations
Geometry optimisation was performed at the DFT
B3LYP level theory using 6-31G** basis set with
Gassian-98 program. The highest occupied molecular
orbital (HOMO) and the lowest unoccupied molecular
orbital (LUMO) were mapped with the second
function of the total electronic density using full
SCF matrix.
3. Results and discussion
3.1. Weight loss measurements
The weight loss of rectangular steel specimens
sized 5 cm � 2 cm � 0.05 cm in 1 M HCl without and
in the presence of various concentrations of inhibitor
was determined after 24 h of immersion in acid at
30 8C without bubbling. Values of the inhibition
efficiency E (%) obtained and corrosion rate are given
in Table 1. In this method, the inhibition efficiency can
be calculated by the relation:
Eð%Þ ¼�Wcorr �WcorrðinhÞ
Wcorr
�� 100 (1)
where W and Winh are the values of weight loss of steel
after immersion in solutions without and with inhi-
bitor, respectively.
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–2691 2687
Table 1
Corrosion rates of mild steel and inhibition efficiencies for various
concentrations of PPI in 1 M HCl after 24 h of immersion at 30 8C
Concentration
(M)
Corrosion
rate (mg cm�2 h�1)
Inhibition
efficiency E (%)
Blank 5.939 –
1 � 10�5 2.091 64.8
2 � 10�5 1.539 74.1
6 � 10�5 0.456 92.3
8 � 10�5 0.386 93.5
1 � 10�4 0.356 94.0
Table 2
Kinetic parameters for the corrosion of mild steel in 1 M HCl
containing various concentrations of PPI at 30 8C
Concentration
(M)
Ecorr
(mV/SCE)
Icorr
(mA cm�2)
bc
(mV dec�1)
E
(%)
Blank �476 534 157 –
1 � 10�5 �468 252 186 53.0
2 � 10�5 �458 107 182 79.9
6 � 10�5 �453 97 178 81.8
8 � 10�5 �450 77 180 85.5
1 � 10�4 �444 50 184 90.6
It can be clearly noticed that the corrosion rate
values of mild steel decrease when the inhibitor
concentration increases. The inhibition efficiency
increases with the concentration of PPI reaching a
maximum value (94%) at 10�4 M.
3.2. Polarisation curves
Both anodic and cathodic polarisation curves for
mild steel in 1 M HCl at various concentrations of PPI
at 30 8C are shown in Fig. 2. The extrapolation of the
Tafel straight line allows the calculation of the
corrosion current density (Icorr). The values of Icorr,
the corrosion potential (Ecorr) and the cathodic and
anodic Tafel slopes (bc), E (%) as function of PPI
concentrations are given in Table 2. In this case, the
inhibition efficiency is defined as follows:
Eð%Þ ¼ Icorr � IcorrðinhÞIcorr
� 100 (2)
where Icorr and Icorr(inh) are the corrosion current
density values without and with the addition of inhi-
bitor, respectively.
Fig. 2. Polarisation curves for mild steel in 1 M HCl containing
different concentration of PPI.
It is clear that the addition of PPI hindered the
acid attack on the steel electrode and a comparison
of curves, showed that, with respect to the blank,
increasing the concentration of the inhibitor gave rise
to a consistent decrease cathodic and anodic current
densities. Its presence caused an ennoblement of the
corrosion potential of mild steel and a change of the
cathodic Tafel slope (bc) (Fig. 2). As it is shown in
Fig. 2, the cathodic current–potential curves give rise
to parallel Tafel lines, which indicate that hydrogen
evolution reaction is activation controlled and that the
addition of the PPI does not modify the mechanism of
this process [19]. The results demonstrate that the
hydrogen reduction is inhibited and that the inhibi-
tion efficiency increases with inhibitor concentration.
In the anodic range, the polarisation curves of mild
steel show that the addition of PPI decreases current
densities in a large domain of potential. This result
suggest that this compound act as a mixed-type
inhibitor of the corrosion of mild steel in hydro-
chloric acid medium. It can be noticed that for
potential higher than �300 mV/SCE, the inhibitor
start to desorb. This potential can be defined as
the desorption potential. Similar behaviour have
been already reported for other organic compounds
[20,21].
E (%) increased with inhibitor concentrations
reaching a maximum (76.2%) for the higher con-
centration of PPI. The polarisation curves study also
confirms the inhibiting character of PPYobtained with
weight loss measurements, however, E (%) values
determined using polarisation curves were smaller
than those obtained by weight loss measurements.
The kinetic parameters for the corrosion of mild
steel in 1 M HCl indicate satisfactory inhibiting
efficiencies even at very low concentration (73.0% at
10�5 M). At higher concentrations (10�4 M) the
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–26912688
Table 3
Impedance parameters for the corrosion of mild steel in 1 M HCl
containing various concentrations of PPI after 24 h of immersion at
30 8C
Concentration
(M)
Rt
(V cm�2)
Cdl
(mF cm�2)
Erest potential
(mV/SCE)
E
(%)
Blank 20.2 785.1 �473 –
1 � 10�5 41.0 489.4 �448 50.5
2 � 10�5 69.5 229.1 �452 70.8
6 � 10�5 137.4 145.9 �457 85.3
8 � 10�5 170.1 125.8 �472 88.1
1 � 10�4 200.0 93.6 �453 90.2
inhibition efficiency is found to be higher when the
weight loss measurements or the EIS methods are
used: 94 (Table 1) and 90.2% (Table 3) respectively
instead of 90.6% (Table 2) obtained by the polariza-
tion curve. This difference was probably caused by the
shorter immersion time in the case of polarisation
curve measurements.
3.3. Electrochemical impedance spectroscopy
(EIS)
The impedance diagrams obtained after 24 h of
exposure of the samples at 30 8C in inhibited and
uninhibited solutions containing various concentration
of PPI are shown in Fig. 3. It is apparent from these
plots that the impedance response of mild steel in
uninhibited HCl solution has significantly changed
after the addition of PPI in the corrosive solution. This
indicates that the impedance of inhibited substrate
increases with increasing inhibitor concentration and
consequently the inhibition efficiency increases.
Fig. 3. Nyquist diagrams for mild steel of PPI after 24 h of
immersion in 1 M HCl containing different concentrations.
When the complex plane impedance contains a
‘‘depressed’’ semicircle with the center under the real
axis, such behaviour characteristic for solid electrodes
and often referred to as frequency dispersion have
been attributed to different physical phenomena such
as roughness and inhomogeneities of the solid surfaces
[22], impurities, dislocations, grain boundaries
[23,24], fractality [23,25], distribution of the active
sites, adsorption of inhibitors [18], formation of
porous layers [26]. Similar diagrams were described
elsewhere [12,13] for steel electrode with and without
organic inhibitors in 1 M HCl. In addition to the high
frequency loop, a low inductive frequency loop was
also observed (Fig. 3), indicating that a Faradaic
process is taking place on the free electrode sites. This
low inductive loop is generally attributed to the
adsorption of species resulting from the iron dissolu-
tion and the adsorption of hydrogen [27–29].
The impedance parameters such as the double layer
capacitance (Cdl), the charge-transfer resistance (Rt),
E (%) and the rest potential (Erestpot) derived from
Nyquist diagrams are given in Table 3. The charge-
transfer resistance Rt, values are calculated from the
difference in impedance at lower and higher frequen-
cies as suggested by Haruyama and Tsuru [30]. To
obtain the double-layer capacitance (Cdl), the fre-
quency at which the imaginary component of the
impedance is maximum (�Z00max) is found and Cdl
values are obtained from the equation.
f ð�Z 00maxÞ ¼
1
2pCdlRt
(3)
The inhibition efficiency is calculated as follows:
E% ¼�R�1 � R�1
R�1
�� 100 (4)
where Rtcorr and Rtcorr(inh) are the charge transfer
resistance values without and with inhibitor, respec-
tively.
The analysis of the electrochemical parameters
shows that the charge-transfer resistance increases with
the concentration of PPI. Seeing that, for a same
immersion time, the values of the double layer
capacitance (Cdl) decrease with increasing concentra-
tion of inhibitor. The double layer between the charged
metal surface and the solution is considered as an
electrical capacitor. The adsorption of the PPI on the
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–2691 2689
Fig. 5. N 1s XPS core-level spectra of steel surface exposed to 1 M
HCl + 10�4 M PPI solution during 24 h at 30 8C.
electrode decreases its electrical capacity because they
displace the water molecule and others ions originally
adsorbed on the surface. The decrease of this capacity
with increasing PPI concentrations may be attributed to
the formation of a protective layer at electrode surface.
Inhibition efficiency is found to increase with PPI
concentration. The inhibition efficiencies calculated
from ac impedance results show the same trend as those
obtained from dc polarisation and weight loss
measurements.
3.4. Theoretical calculations and surface
analysis results
When the frontier molecular orbital are analysed
(Fig. 4), it is observed that the highest occupied
molecular orbital (HOMO), is located for the most part
on the benzene ring of the indole system and on
nitrogen N1 and N2; these atoms are the active sites
for a nucleophilic attack and consequently the
favourable place for the interaction with the metallic
surface as it is observed in the XPS spectrum (Fig. 5)
of the adsorbed PPI.
The protection provided by PPI to mild steel in HCl
solutions was retained when specimens dipped in
acids containing the organic molecules were trans-
ferred into fresh HCl without inhibitor. PPI have a
strong tendency to stick to the steel surface. The PPI
molecules absorbed on the metal surface as it can be
supposed by the EIS studies which show a decreasing
of double layer capacitance values (Cdl).
Fig. 4. HOMO and LUMO map of PPI with respectively alpha (red)
and beta orbitals (green). (For interpretation of the references to
colour in this figure legend, the reader is referred to the web version
of the article.)
The presence of the PPI on the steel surface was
monitored using the characteristic N 1s signals (Fig. 5)
[30]. The XPS spectra were obtained for the steel
exposed to PPI as well as for the steel exposed to PPI
in 1 M hydrochloric acid medium. For comparison
purposes, the XPS spectra were also obtained for pure
PPI (Fig. 6, Table 4). Considering an isolated PPI
molecule, a two component N 1s peak is expected,
the two components being in the ratio 1:4 according
to the two PPI nitrogen species ( NH, N–) at
different bonding energies 399.9 and 399 eV, respec-
tively [31–33].
The XPS spectra show three peaks (Fig. 6, Table 4).
We may attribute the two majors peaks at a BE about
399.03 and 399.16 eV for the nitrogen’s 1–4 and 3–5,
respectively (Fig. 1) and the minor peak at a BE
399.9 eV at the nitrogen 2 (Fig. 1) [31,32]. The XPS
spectrum of the steel surface shows that PPI is present
but the relative proportions of the nitrogen species are
quite different from these observed with pure PPI. The
spectrum exhibits three major components at BE
398.05, 399.25 and 400.06 eV which can be attributed
[33] at the N–H adsorbed of indole part of the
molecule, N– pyridyl substituents and pyridazine
part of the molecule and NH indole respectively
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–26912690
Table 4
Bending energies of redox states of PPI and atomic concentration from surface XPS
Sample Bending energies (eV)
N2ads NHads N– N– NH –N+–H
Pure PPI 399.03 399.16 399.9
Concentration (%) 40 40 20
Steel and PPI 396.97 398.05 399.25 400.06 401.35
Concentration (%) 9 29 23 31 7
References [25] [25] [22–23] [22–23] [24] [24]
(Fig. 5, Table 4). Two small peaks are also observed at
BE 396.97 eV (N2ads), which comes from a partial
degradation of PPI [34] and 401.35 eV characteristic
of apparition of positively charged nitrogen, showing
that there has been oxidation or protonation [33].
3.5. Adsorption isotherm
Adsorption isotherms are very important in under-
standing the mechanism of organo electrochemical
reactions [35]. In order to obtain the isotherm, the
fractional coverage values Q, as a function of inhibitor
concentration, must be obtained. It is preferable to
Fig. 6. N 1s XPS core-level spectra of pure PPI.
evaluate the adsorption isotherm with AC impedance
study because the imposed sine wave voltages, at
10 mV peak to peak, does not disturb the surface,
therefore not desorption occurs in this case. Q can be
obtained from the impedance measurements as
described elsewhere [35]. A simple model connects
Cdl to Q: impedance measurements
Cdl;Qð1 �QÞCdlðQ¼0Þ þQCdlðQ¼1Þ (5)
where Cdl,Q is the Cdl with inhibitor, Cdl(Q=0) is the Cdl
without inhibitor, and Cdl(Q=1) is the Cdl of an entirely
covered surface. After rearrangement, the Q for differ-
ent concentrations of the inhibition in acidic media is:
u ¼Cdlðu¼0Þ � Cdl;u
Cdlðu¼0Þ � Cdlðu¼1Þ(6)
Q can also be evaluated from corrosion rate using the
equation:
u ¼ W �Winh
W(7)
In this study, attempts were made to fit these Q
values to various isotherms (Langmuir, Temkin,
Fig. 7. Langmuir adsorption plots for mild steel in 1 M HCl
containing different concentrations of PPI from capacitance values.
F. Bentiss et al. / Applied Surface Science 252 (2006) 2684–2691 2691
Frumkin,. . .). These models have been used for other
inhibitor systems [36]. By far the best fit was obtained
with the Langmuir isotherm (Fig. 7).
The plot of Cinh/Q versus Cinh yielded a straight
line, where Cinh is the inhibitor concentration (Fig. 7).
This was observed, clearly proving that the adsorption
of the PPI from 1 M HCl solutions on the steel surface
corresponds to the Langmuir isotherm model where,
Q ¼ bCinh
1 þ bCinh
ðLangmuir isothermÞ (8)
and where ‘‘b’’ designates the adsorption coefficient.
The strong correlation (r = 0.99) for the Langmuir
adsorption isotherm plot confirmed the validity of this
approach.
4. Conclusions
PPI inhibits the corrosion of mild steel in 1 M HCl
medium. The additions of inhibitor modified slightly
the cathodic Tafel slope and the Ecorr potential
increase with increasing concentrations. This shows
that PPI is more anodic than cathodic inhibitor. The
XPS spectrum shows that PPI is present on the steel
surface. The relative proportion of nitrogen species is
quite different from those observed with pure PPI; a
part of nitrogen is oxidised and other part is reduced.
Inhibition of corrosion by PPI is due to the formation
of chemisorbed film on the steel surface. Adsorption
of this inhibitor on the steel surface from HCl solution
follows the Langmuir isotherm.
Acknowledgements
The authors would like to thank the FEDER, the
CRNS, the ‘‘Region Nord-Pas de Calais’’ and the
‘‘Ministere de l’Enseignement Superieur et de la
Recherche Scientifique’’ for the their financial support
for the acquisition of the XPS spectrometer.
References
[1] J.M. Sykes, Br. Corros. J. 25 (1990) 175.
[2] G. Schmitt, Br. Corros. J. 19 (1984) 165.
[3] J.O’M. Bockcis, B.O. Yang, J. Electrochem. Soc. 138 (1991)
2237.
[4] C. Pillali, R. Narayan, Corros. Sci. 23 (1983) 151.
[5] F.B. Growcock, V.R. Lopp, Corros. Sci. 28 (1998) 397.
[6] M. Bartos, N. Hackeman, J. Electrochem. Soc. 139 (1992)
3429.
[7] F. Zucchi, G. Trabanelli, G. Brunoro, Corros. Sci. 33 (1992)
1135.
[8] S.L. Granesse, Corrosion 44 (1998) 322.
[9] G. Moretti, G. Quartarone, A. Tassan, A. Zingales, Werkst.
Korros. 45 (1994) 5.
[10] G. Moretti, G. Quartarone, A. Tassan, A. Zingales, Electro-
chim. Acta 41 (1996) 1971.
[11] A. Chetouani, A. Aouniti, B. Hammouti, N. Benchat, T.
Benhadda, S. Kertit, Corros. Sci. 45 (2003) 1675.
[12] F. Bentiss, M. Traisnel, H. Vezin, M. Lagrenee, Ind. Eng.
Chem. Res. 39 (2000) 3732.
[13] M. Lagrenee, B. Mernari, N. Chaibi, M. Traisnel, H. Vezin, F.
Bentiss, Corros. Sci. 43 (2001) 951.
[14] M. Takahashi, H. Ishida, M. Kohmoto, Bull. Chem. Soc. Jpn.
49 (1976) 1725.
[15] S.C. Benson, C.A. Palabria, J.K. Snyder, J. Org. Chem. 52
(1987) 4610.
[16] N. Haider, R. Wanko, Heterocycles 38 (1994) 1805.
[17] F. D. Gassama, Thesis UST Lille (2001).
[18] F. Bentiss, M. Traisnel, L. Gengembre, M. Lagrenee, Appl.
Surf. Sci. 152 (1999) 237.
[19] S. Kertit, B. Hammouti, Appl. Surf. Sci. 93 (1996) 59.
[20] W.J. Lorenz, F. Mansfeld, Corros. Sci. 21 (1981) 647.
[21] L. Elkadi, B. Mernari, M. Traisnel, F. Bentiss, M. Lagrenee,
Corros. Sci. 42 (2000) 194.
[22] K. Juttner, Electrochem. Acta 35 (1990) 1501.
[23] Z.B. Stoynov, B.M. Grafov, B. Savova-Stoynove, V.V. Elkin,
Electrochemical Impedance, Nauka, Moscow, 1991.
[24] F.B. Growcock, J.H. Jasinski, J. Electrochem. Soc. 136 (1989)
2310.
[25] A.H. Mehaute, G. Grepy, Solid State Ionics 910 (1989) 17.
[26] S. Veleva, A. Popova, S. Raicheva, in: Proceedings of the 7th
European Corrosion Inhibitors, Ferrara, 1990, p. 149.
[27] K.F. Khaled, N. Hackerman, Electrochim. Acta 48 (2003) 2715.
[28] J. Bessone, C. Mayer, K. Juttner, W.J. Lorenz, Electrochim.
Acta 28 (1983) 171.
[29] I. Epelboin, M. Keddam, H. Takenouti, J. Appl. Electrochem. 2
(1972) 71.
[30] T. Tsuru, S. Haruyama, Boshoku Gijutsu, J. Jpn. Soc., Corros.
Eng. 27 (1978) 573.
[31] F. Bentiss, M. Traisnel, L. Gengembre, M. Lagrenee, Appl.
Surf. Sci. 161 (1999) 237.
[32] C. D. Wagner, W. M. Riggs, L. E. Davis, J. F. Moulder,
Perking-Elmer Corporation, Physical Electronics Division.
[33] E.T. Kang, K.G. Neoh, K.L. Tan, Surf. Interf. Anal. 19 (1992) 33.
[34] K.L. Tan, B.T.G. Tan, E.T. Kang, K.G. Neoh, J. Mater. Sci. 27
(1992) 4056.
[35] N. Hackerman, E. McCafferty, In: Proceedings of the 5th
International Congress on Metallic Corrosion, Houston,
1974, p. 542.
[36] S. Bilgic, N. Caliskan, Appl. Surf. Sci. 152 (1999) 107.