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Electrochimica Acta 52 (2007) 70687074
Evaluation of corrosion and erosioncorrosion resistances of mildsteel in sulfide-containing NaCl aerated solutions
Abdel Salam Hamdy a,b,, A.G. Saeh c,M.A. Shoeib b, Y. Barakat d
a Department of Materials Science and Engineering, Boise State University, Boise, ID, USAbDepartment of Surface Technology and C orrosion Protection, Central Metallurgical Research and Development Institute,
CMRDI, P.O. Box 87, Helwan, Cairo, Egyptc Faculty of Engineering, University of Tripoli, Libya
d Tabbin Institute for Metallurgical Studies, Helwan, Cairo, Egypt
Received 8 March 2007; received in revised form 14 May 2007; accepted 16 May 2007
Available online 21 May 2007
Abstract
This paper reports results of potentiodynamic polarization, electrochemical impedance measurements and erosioncorrosion of mild steel in
aerated sulfide containing 3.5% NaCl solutions at room temperature. The pitting corrosion behavior was studied in NaCl solution containing 0.001,
0.005 and 0.010M Na2S, using potentiodynamic polarization and electrochemical impedance spectroscopy. The erosioncorrosion resistance
was evaluated after rotating the samples in sulfide polluted NaCl solution for 24 h at a velocity of 300, 600 and 900 ppm using a rotating disc
electrode. Results showed that the presence of sulfide ions in NaCl solution resulted in a significant increase in the corrosion attack due to the
local acidification caused by iron sulfide formation. The localized replacement of the protective Fe-oxide film by a non-protective iron sulfide film
is responsible for the pitting and erosioncorrosion attack. The study concluded that the higher the concentration of sulfide in NaCl solution, the
lower the resistance to pitting and erosioncorrosion. Moreover, increasing the solution rotating velocity affects negatively the erosioncorrosion
resistance.
2007 Elsevier Ltd. All rights reserved.
Keywords: Pitting corrosion; Sulfide; Erosioncorrosion; Mild steel; NaCl solution; EIS; Polarization
1. Introduction
The corrosion of steel in sulfide-containing solutions has
received considerable attention for many years due to its
importance in several industrial processes such as oil and gas
production and transport. The evaluation of steel corrosion in
sulfide environments is important in the petrochemical indus-
try, as this phenomenon is responsible for costly economic and
human loss [1].
Mild steel is used to manufacture essential parts and com-
ponents used in the petroleum industry. Because these oil
environments contain sulfides, numerous studies have been
Corresponding author at: Department of Surface Technology and Corrosion
Protection, Central Metallurgical Research and Development Institute, CMRDI,
P.O. Box 87, Helwan, Cairo, Egypt. Tel.: +20 2 501 0640; fax: +20 2 510 0639.
E-mail address: [email protected] (A.S. Hamdy).
made concerning iron sulfide corrosion products formed on
steels under a variety of reaction conditions [13].
In addition, sulfide pollution of seawater at the coastal
areas can occur from industrial waste discharge, biologi-
cal and bacteriological process in seawater (seaweed, marine
organisms or microorganisms, sulfide reducing bacteria) which
promotes aqueous corrosion of different materials includ-
ing steels. It has been reported that the corrosion rates of
materials, such as copper alloys, increases by a factor of
1030 when seawater contains sulfur compounds as impuri-
ties [4]. Corrosion problems can occur when an oil processing
plant is left idle for long periods, with stagnant seawater
(after testing or during downtime). In this case, corrosion
can be particularly aggressive as a result of sulfide pollution
[2].
Therefore, the objective of this work is to evaluate the cor-
rosion and erosioncorrosion resistance of mild steel in 3.5%
NaCl as a function of sulfide content.
0013-4686/$ see front matter 2007 Elsevier Ltd. All rights reserved.
doi:10.1016/j.electacta.2007.05.034
mailto:[email protected]://localhost/var/www/apps/conversion/tmp/scratch_4/dx.doi.org/10.1016/j.electacta.2007.05.034http://localhost/var/www/apps/conversion/tmp/scratch_4/dx.doi.org/10.1016/j.electacta.2007.05.034mailto:[email protected] -
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A.S. Hamdy et al. / Electrochimica Acta 52 (2007) 70687074 7069
Table 1
Chemical composition of mild steel (wt.%)
Si Mn Ti V Al Cr Ni Mo Nb Cu Co W Pb C Fe
0.087 0.44 0.013 0.026 0.005 0.002 0.0005 0.0009 0.0006 0.003 0.029 0.011 0.011 0.05 Bal.
2. Experimental
2.1. Materials
The electrodes used for these corrosion studies were cut from
a mild steel sheet in the form of 6 cm 3 cm 0.3 cm pieces.
The specimens for erosioncorrosion studies were cut from a
mild steel rod and prepared in cylindrical form with diameter of
0.85 cm and height of 3 cm. The chemical composition of the
mild steel under investigation is shown in Table 1.
2.2. Surface preparation and solutions
Each steel specimen was abraded to a 800 grit finish withSiC paper, degreased in acetone, washed with distilled water,
and dried in dry air. For the erosioncorrosion experiments, the
samples were weighed before immersion in the corrosive solu-
tions. A series of mild steel samples were subjected to corrosion
under the following conditions.
All the experiments were performed at room temperature
under stagnant conditions, except that for erosioncorrosion
tests. Specimens for erosioncorrosion studies were immersed
in the corrosive solutions (listed in Table 2) for 24 h under differ-
ent rotating speeds: 0, 300, 600, and 900 rpm, respectively. After
24 h of rotation, the samples were rinsed with distilled water and
acetone, dried with hotair,and weighed again forweight loss cal-culations. Laboratory grade chemicals and distilled water were
used to prepare all solutions.
3. Methods
3.1. Electrochemical impedance tests
The corrosion behavior of the previous specimens was moni-
tored using electrochemical impedance spectroscopy (EIS) and
DC polarization techniques during immersion in the corrosive
solutions (Table 2). The solutions were open to air and kept at
room temperature for up to one week.
A three-electrode set-up was used with impedance spectrabeing recorded at the corrosion potential ECorr. A saturated
calomel electrode (SCE) was used as the reference electrode.
It was coupled capacitively to a Pt wire to reduce the phase
Table 2
Experimental parameters for corrosion of mild steel
Symbol Electrolyte composition pH Rotating speed (rpm)
Blank Pure 3.5% NaCl 6.5 0, 300, 600, 900
S1 3.5% NaCl + 0.001 M Na2S 8.13 0, 300, 600, 900
S2 3.5% NaCl + 0.005 M Na2S 8.60 0, 300, 600, 900
S3 3.5% NaCl + 0.01 M Na2S 10.88 0, 300, 600, 900
shift at high frequencies. EIS was performed between 0.01 Hz
and 65 kHz frequency range using a frequency response ana-
lyzer (Autolab PGSTAT 30, Eco-Chemie). The amplitude of the
sinusoidal voltage signal was 10 mV.
3.2. Polarization tests
Liner polarization measurements of specimens, previously
immersed for 30 min in the solutions (Table 2), were made
using a scan rate of 0.07 mV/s in the applied potential range
from 0.15 to 0.7 VSCE with respect to ECorr using an Autolab
PGSTAT 30 galvanostat/potentiostat. The corrosion potential
(Ecorr) and corrosion current density (icorr), calculated using the
Tafel extrapolation method [5]. The exposed surface area was25.4 mm2. All curves were normalized to 1 cm2.
3.3. Energy-dispersive spectrometry
After immersing the samples in NaCl solutions for one week,
the samples were washed with deionized water and then dried.
SEM images of the cleaned samples were obtained using a
digital scanning electron microscope (Model JEOL JSM 5410,
Oxford Instruments). Microprobe analysis was performed using
energy dispersive spectrometry (EDS) (Model 6587, Pentafet
Link, Oxford Microanalysis Group).
3.4. X-ray diffraction
After drying the corroded specimen (one week in corrosive
solutions) with methanol, the solid surface corrosion products
were characterized by an X-ray diffractometry (XRD). XRD
analysis was performed using Bruker AXS, Model D8, 40 kV,
40 mA, Cu K ADVANCE.
3.5. Surface morphology
Corrosion morphology was examined with a metallographic
microscope (LEICA DMR) with a Quips programming window,
LEICA Imaging Systems Ltd.
4. Results and discussions
4.1. Effect of sulfide concentrations
The effect of sulfide concentrations on the corrosion of mild
steel in 3.5% NaCl solution was studied using electrochemi-
cal impedance spectroscopy (EIS), polarization resistance and
cyclic potentiodynamic techniques. EIS techniques have been
applied to study pitting corrosion and other localized corrosion
and has been shown to have marked advantages in the study of
interfacial reactions and other interfacial phenomena [512]. In
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particular, the information obtained from EIS measurements has
time-resolved and surface-averaged characteristics. Moreover,
EIS is a non-destructive technique.
4.1.1. Electrochemical impedance spectroscopy
EIS has been successfully applied to the study of corrosion
systems for 30 years and been proven to be a powerful andaccurate method for measuring corrosion rates especially for
coatings and thin films. An important advantage of EIS over
other laboratory techniques is the possibility of using very small
amplitude signals without significantly disturbing the proper-
ties being measured. To make an EIS measurement, a small
amplitude signal is applied to a specimen over a range of fre-
quencies.
The expression for impedance is composed of a real and an
imaginary part. If the real part is plotted on the z-axis and the
imaginary part on the y-axis of a chart, we get a Nyquist plot.
However, Nyquist plots have one major shortcoming. When you
look at any data point on the plot, you cannot tell what frequency
was used to record that point. Therefore, other impedance plots
such as Bode plots are importantto make a correct interpretation.
In Bode plots, the impedance is plotted with log frequency on the
x-axis and both the absolute value of the impedance (|Z|=Z0)
and phase-shift on the y-axis. Unlike the Nyquist plot, the Bode
plot explicitly shows frequency information.
The impedance measurement technique has been applied
to the study of pitting corrosion and other localized corro-
sion [69]. The impedance technique has marked advantages in
the study of interfacial reactions and other interfacial phenom-
ena. The impedance information obtained has time-resolved and
surface-averaged characteristics [9]. In this work, the corrosion
behavior of mild steel specimens, immersed in NaCl solutioncontaining different sulfide ratios was investigated. Nyquist
plots (Fig. 1a) show the surface resistances after one week of
immersion in sulfide polluted NaCl solutions. The corrosion
resistances decreased with increasing sulfide concentrations.
The surface resistance of mild steel in pure NaCl solution
(Blank) is 2.8 103 cm2. The resistance sharply decreased
to be 0.1 103, 0.4 103, and 0.7 103 cm2 after addition
of 0.001, 0.005, and 0.010 M Na2S, respectively.
Bode plots (Fig. 1b) showed that the surface resistance of the
mild steels was generally decreased by increasing the sulfide
ratio. The samples that immersed in 3.5% NaCl + 0.001 M Na2S
(S1), 3.5% NaCl + 0.005 M Na2S (S2)and3.5% NaCl+ 0.010 MNa2S (S3) showed dramatic decrease of the impedance in the
capacitive region, which is characteristic for the pitting process
on steel. In addition, the phase angle () tended toward zero at
low frequencies, indicating that theresistance of the barrier layer
Fig. 1. (a) Nyquist plots and (b) Bode plots of mild steel after one week of
immersion in 3.5% NaCl containing varying concentrations of Na2S. (Blank)
0 M Na2S; (S1) 0.001 M Na2S; (S2) 0.005 M Na2S; (S3) 0.010 M Na2S.
was being approached. The changes of the spectra at very low
frequencies indicate the occurrence of pitting and were in agree-
ment with visual and SEM inspection. On the other hand, the
samples tested in pure NaCl solution, without sulfide (blank),
showed very stable impedance behavior, even after one week
of immersion, indicating that the presence of sulfide ions in thesolution negatively affects the protectionperformance of the pas-
sive oxide films. This would indicate that sulfide ions interfere
with the protective iron oxide layer to form less protective layers
of iron oxide plus ion sulfide.
4.1.2. Linear polarization measurements
Linear polarization measurements of mild steel in 3.5% NaCl
solution containing 0, 0.001, 0.005, and 0.010 M Na2S, respec-
tively, is shown in Table 3. The corrosion potential (Ecorr)
and corrosion current density (icorr), calculated using the Tafel
extrapolation method [5] are also given in Table 3. It is evident
from Table 3 that the addition of sulfide increases the icorr andcorrosion rates and decreases the polarization resistances (Rp).
The extent of increase in icorr and corrosion rates is found to be
a function of the concentration of Na2S, higher the concentra-
tion of Na2S, higher the values of corrosion rate and larger the
Table 3
Effect of sulfide concentrations on the corrosion behavior of mild steel in 3.5% NaCl solution
Sample Ecorr (mV) vs. SCE icorr (A/cm2) Rp () Corrosion rate (MPY) ba (mV/de) bc (mV/de)
Blank 690 1.144 9.811 8.56103 26 25
S1 724 2.019 5.788 15.11103 28 24
S2 709 2.065 5.127 15.45103 22 28
S3 699 3.790 3.801 28.36103 29 29
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increase in icorr values. The corrosion rate increases more than
three times the value of blank samples when the sulfide con-
centration is increased from 0 to 0.010 M. These results are in
agreement with the previous work of Gudas andHack[13]. They
suggested that soluble sulfide concentrations as low as 7 g/l
could cause significant adverse effects to brass. Soluble sulfides
could increase the overall corrosion rates through acceleration
of anodic, cathodic, or both reactions. The observed negative
shift in Ecorr and the increase in icorr in the presence of sulfide
ions (Table 3) are considered to be due to the change in nature
of surface films on steel and suggest that the corrosion is under
anodic control. It is suggested that the iron oxide layer becomes
defective in the presence of sulfide ions in the medium. This
defective surface layer consists of iron oxide and iron sulfide
that permit rapid ionic and electronic transport through it and
causes an increase in the corrosion rate. The iron sulfide seems
to be non-protective compared with the iron oxide. The presence
of sulfide ions in the electrolyte solution catalyzes the corro-
sion reaction by preventing formation of protective iron oxide
[1420]. Hence, increasing the corrosion rate of mild steel in3.5% NaCl solution containing sulfide (Fig. 2) is due to the for-
mation of non-protective iron sulfide film at the steel surface.
Moreover, the presence of iron sulfide promotes the anodic dis-
solution and accelerates local corrosion under the precipitate
film [19,20].
4.1.3. Potentiodynamic polarization measurements
Localized corrosion is one of the most dangerous corrosion
species for degradation of pipes or containers intended for long-
term use in industry. Pitting is of particular concern because
it may lead to premature breaching of the container materials
through electrochemical dissolution processes that can acceler-ate with time [1520].
The effect of sulfide ion concentrations on the corrosion
behavior of mild steel was studied in NaCl solution. Potentio-
dynamic polarization technique (Fig. 3) was used to evaluate
the pitting corrosion resistance for different samples in NaCl
solution containing sulfide. In this technique, the potential was
recorded starting from a cathodic potential(about1.75 V/SCE)
and be allowed to sweep to the anodic potential direction till it
reaches the pitting potential. At that potential, a sudden shift in
Fig. 2. Effect of sulfide concentrations on the corrosion rate of mild steel after
one week in 3.5% NaCl solution.
Fig. 3. Potentiodynamic polarization curves of mild steel after one week of
immersion in different corrosive solutions.
the current to the active direction will be observed. The pitting
tendency of the mild steel can be estimated by the determi-
nation of pitting potential, Epit. The Epit is always defined as
the potential below which the metal surface remains passive
and above which pits can nucleate and propagate. The differ-
ence between Epit and the corrosion potential ECorr representsthe passive domain for any materials or alloys. In this work,
the difference between (Epit ECorr) was taken as a relative
measure of the passivation ability. The greater the difference
between Epit ECorr is, the greater the passive range and hence,
the materials will be safe from corrosion (Fig. 3).
According to the potentiodynamic data in Table 4 and Fig. 3,
the pitting corrosion resistances decreased with increasing sul-
fide concentrations. The passivity domain of mild steel in pure
NaCl solution (blank) is 221 mV. The passivity domain grad-
ually decreased to be 117, 24, and 4 mV after one week
of immersion in NaCl solution containing 0.001, 0.005, and
0.010 M Na2S, respectively. These results are in agreement withthe EIS results, visual inspection and microscopic examinations.
4.1.4. Surface examinations
SEM micrographs (Fig. 4), optical microscope and visual
inspection of S1, S2 and S3 samples showed severe pitting as
well as crevice corrosion after one week of immersion. The
number of pits exceeded 15 pit/cm2 for S3. Pitting corrosion
was also observed in S1 and S2 samples with limited areas
of crevice corrosion. However, the number of pits was less
than 15 pit/cm2. The best localized corrosion resistance was
observed from the blank samples (without sulfide). Few zones of
crevice corrosion were observed in addition to general corrosion
Fig. 5.
The chemical composition of corrosion products was inves-
tigated by XRD. Generally, iron sulfide and iron oxide (Fe 2O3)
Table 4
Potentiodynamic polarization data for mild steel after one week of immersion
in different corrosive solutions
Sample Epit (mV) ECorr (mV) Epit ECorr (mV)
Blank 523 744 221
S1 696 813 117
S2 745 769 24
S3 776 780 4
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Fig. 4. SEM micrograph of mild steel after one week of immersion in 0, 0.001, 0.005, and 0.010 M sulfide containing NaCl solutions, respectively.
were detected in the surface layers of samples S1, S2 and S3.
The blank samples revealed formation of both ferric and ferrous
oxides. Microprobe analysis using EDS (Table 5), revealed pres-
ence of sulfur for S1 and S3 samples. However, the amount of
sulfur detected in S3 samples is three times higher than S1. The
lowest sulfur content was detected from S2 samples. However,
about 1% of chlorine with the highest oxygen content (66.8)
was also observed in S2. These results may indicate formation
of Fe2O3 and iron oxychloride compound. Although such com-
pounds have an inhibitive action on the corrosion of iron, the
presence of sulfide mixed with such compound increases the
Fig. 5. EDX analysis for mild steel surface layer after one week in 3.5% NaCl
solution + 0.001 M Na2S (S1).
competitive action between the different forms of oxide and
sulfide and hence, decreases the localized corrosion resistances
after one week of immersion. It seems that the presence of sul-
fur inside the outer iron oxide layer decreases the protective
power of such layer to corrosion attack due to the local acidifica-
tion caused by iron sulfide formation. The localized replacement
of the protective Fe-oxide film by a non-protective iron sulfide
(FeS1x) film is responsible for the pitting corrosion. Therefore,
blank samples showed the highest resistance to pitting corro-
sion. Further details about the chemical composition of the outer
surface layers will be discussed in a futurepaper for better under-standing the nature of oxide and sulfide formed due to corrosion
attack especially for S2.
4.2. Effect of solution speed (erosioncorrosion)
In sulfide free 3.5% NaCl solution, the weight loss of mild
steel slowly increases with increasing the rotation speed from 0
to 600 rpm due to the corrosion reaction between the protective
iron oxide layers with chloride ions from the NaCl solution.
Increasing the speed up to 900 rpm will increase the possibility
to remove such protective layer and hence the corrosion rate will
increase dramatically.On the other hand, the corrosion rates increased dramatically
with the increase of rotation speed from 0 to 300 rpm in pres-
ence of Na2S in NaCl solution. The presence of sulfide ions in
NaCl solution resulted in a significant increase in the corrosion
attack due to the local acidification caused by iron sulfide forma-
tion. The localized replacement of the protective Fe-oxide film
by a non-protective iron sulfide film is responsible for increas-
ing the pitting and erosioncorrosion attack. The higher the
concentration of sulfide in NaCl solution is, the lower the resis-
tance to erosioncorrosion. Increasing the rotation speed more
than 300 rpm increases the corrosion rate slowly. This can be
attributed to the removal of sulfide ions from the surface at high
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Table 5
EDS of mild steel after one week of corrosion
Sample Fe, atomic ratio (%) S, atomic ratio (%) O, atomic ratio (%) Cl, atomic ratio (%)
Blank 31.49 68.46
S1 41.13 1.93 55.24
2S 30.62 0.66 66.80 0.92
3S 34.27 5.13 60.43
speed preventing the local acidification which is the main source
of corrosion.
4.3. Effect of immersion time
The immersion time in sulfide containing NaCl solution
was found to have a marked effect on the initiation and for-
mation of pitting corrosion. Nyquist plots (Fig. 6a) show the
surface resistances after one day of immersion in sulfide con-
taining NaCl solutions. Taking the surface resistance of theblank sample as a base, the corrosion resistances of sulfide-
containing samples decreased, as expected, by increasing the
sulfide concentrations as shown from the spectra of S1 and
S3 samples. The surface resistance of the blank sample is
3.3103 cm2. The surface resistance of S1 and S3 decreased
to be 1.6 103 and 1.2 103 cm2, respectively. However,
S2 showed a distinct improve in the corrosion resistance to be
4.6103 cm2.
Accordingto Bode plots (Fig. 6b), S1 and S3 samples showed
a dramatic decrease in the impedance in the capacitive region,
Fig. 6. (a) Nyquistplots and (b)Bode plots ofmildsteel after oneday of immer-
sion in 3.5% NaCl containing varying concentrations of Na2S. (Blank) 0 M
Na2S; (S1) 0.001 M Na2S; (S2) 0.005 M Na2S; (S3) 0.010 M Na2S.
which is characteristic for the pitting process on steel. In addi-
tion, the phase angle () tended toward zero at low frequencies,
indicating that the resistance of the barrier layer was being
approached. In addition, maximum of was observed for the
S1 samples, as evident in Fig. 3b. These changes of the spec-
tra at very low frequencies indicated the occurrence of pitting
and were in agreement with visual and SEM inspection. On the
other hand, S2 samples showed very stable impedance behavior
(Fig. 7a and b), indicating that sulfide ions, especially in the first
hours of immersion, may be temporary converted to intermedi-
ate chemical species such as oxychloride or sulfite and sulfate
compounds which have an inhibitive action on steel [19,20].
Therefore, the pitting resistance increased compared with the
blank samples (Fig. 7a and b) after one day of immersion. After
one week of immersion, the corrosion resistances decreased
sharply for all samples. The surface resistance of mild steel
in pure NaCl solution (Blank) is 2.8 103 cm2. The surface
resistance of S1, S2 and S3 sharply decreased to be 0.1 103,
0.4103, and 0.7 103 cm2, respectively.
Fig. 7. (a)Nyquistplots and(b) Bode plotsof mild steelafterdifferentimmersion
times in 3.5% NaCl containing varying concentrations of Na2S. (Blank) 0 M
Na2S; (S1) 0.001 M Na2S; (S2) 0.005 M Na2S; (S3) 0.010 M Na2S.
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5. Conclusion
1. The presence of sulfide ions in 3.5% NaCl solution results in
a significant increase in the corrosion and erosioncorrosion
attack on mild steel.
2. Formation of a non-protective iron sulfide film instead of the
protective oxide film in sulfide containing solution is due
to the catalyzing ability of the sulfide ions to prevent oxide
formation and hence, increase corrosion attack.
3. Increasing the sulfide concentration affects negatively the
corrosion resistance of mild steel.
4. The solution speed was found also to have a marked effect
on the corrosion resistance. In pure NaCl solution, increasing
the speed increases the corrosion rates. In sulfide containing
NaCl, the corrosion rates increase rapidly with increasing
the solution speed. However, at very high speed the corrosion
rates increase gradually. This can be explained by continuous
removal of the local acidic zones caused by sulfide ions at the
mild steel surface. Hence, preventing corrosion to initiate.
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