Hindawi Publishing Corporation

International Journal of Corrosion

Volume 2011, Article ID 896845, 7 pages
doi:10.1155/2011/896845

Research Article
Corrosion Behavior of Mg-Al/TiC Composites in
NaCl Solution

L. A. Falcon,1 E. Bedolla B.,1 J. Lemus,1 C. Leon,1 I. Rosales,2

and J. G. Gonzalez-Rodriguez2
1
Instituto de Investigaciones Metalurgicas, Universidad Michoacana de San Nicolás de Hidalgo, 58060 Morelia, MICH, Mexico
2 CIICAp, Universidad Autonoma del Estado de Morelos, Avenue Universidad 1001, 62209 Cuernevaca, MOR, Mexico

Correspondence should be addressed to J. G. Gonzalez-Rodriguez, ggonzalez@uaem.mx

Received 6 October 2010; Revised 14 January 2011; Accepted 17 January 2011

Academic Editor: Sebastian Feliu

Copyright © 2011 L. A. Franco et al. This is an open access article distributed under the Creative Commons Attribution License,
which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

The corrosion behavior of TiC particles reinforced Mg-Al alloy in 3.5% NaCl solution has been evaluated using electrochemical
techniques. Tested alloys included an Mg-9Al (Mg AZ91E) alloy with and without 56 wt. % TiC particles. Electrochemical tech-
niques included potentiodynamic polarization curves, linear polarization resistance, electrochemical noise, and electrochemical
impedance spectroscopy measurements. All techniques showed that the composite exhibited a lower corrosion rate than the
base alloy. Evidence of galvanic effects that increased the composite corrosion rate was found between the matrix and the TiC
particles. Additionally, the tendency to suffer from pitting corrosion was higher for the base alloy than that for the composite.
Electrochemical impedance results showed the importance of adsorption/diffusion phenomena in both materials.

1. Introduction disadvantage has been found for Mg-Al-Zn alloys, being Mg

AZ91, the most significant alloy.
Nowadays, aluminum matrixes are widely used in metallic Researches on metallic-based matrix composites using
matrix composites (MMCs), because they have the highest magnesium are considerable fewer than those done for
priority in applications where a combination of corrosion aluminum [5–10]. Many studies have been carried out to
resistance, low density, and high mechanical performance are determine the Mg-Al-Zn corrosion behavior. Pardo et al.
required, such as in the automotive and aerospace industry. [11] concluded that corrosion damage was mainly caused by
The reinforcement of an aluminum matrix, based on the use formation of a Mg(OH)2 corrosion layer. AZ80 and AZ91D
of TiC particles is interesting because of its good wettability alloys revealed the highest corrosion resistance. The relatively
[1, 2] which results in a clean and strong interface [2– fine β-phase (Mg17 Al12 ) network and the aluminum enrich-
4]. While aluminum alloys are the most commonly used ment produced on the corroded surface were the key factors
matrix in metal-ceramic composites, it has been reported limiting progression of the corrosion attack. Preferential
that the addition of TiC, as reinforcement, improves the attack was located at the matrix/β-phase and matrix/MnAl
mechanical properties at room and high temperatures. intermetallic compounds interfaces. Nunez-Lopez et al. [12]
However, research in new systems is required due to rapid reported the corrosion behavior of Mg ZC71 composites
increase in technological development. Therefore, it could be with 12 vol. % SiC, by electrochemical and saline dew tests.
appreciated as an increasing interest in the use of magnesium MMC composite showed a 10 times difference in corrosion
and its alloys as a metallic matrix for MMC composites. rates than the alloy. Local corrosion was 3 times faster in
The main disadvantage of magnesium is the high chemical the composite than in the monolithic alloy. Furthermore,
reactivity due to its negative electrochemical potential; this Nunez observed that there was no correlation between the
greatly restricts its industrial applications, and the same interface and the local corrosion. Suqiu et al. [13] reported
2 International Journal of Corrosion

the corrosion resistance in Mg AZ91/TiC composites. They scanning rate of 1 mV s−1 every 60 minutes during 24
observed that the local corrosion rate was higher in the hours. Electrochemical impedance spectroscopy tests were
composite due the formation of a thinner layer of corrosion carried out at Ecorr by using a signal with an amplitude of
products than in the monolithic alloy. Tiwari et al. [14] 10 mV and a frequency interval of 0.1 Hz–10 kHz. An ACM
studied the corrosion behavior of two SiC Mg-based MMC, potentiostat controlled by a desktop computer was used for
namely, Mg-6SiC and Mg-16SiC (vol. %) in aerated 1M NaCl the LPR tests and polarization curves, whereas for the EIS
and compared them with the corrosion rate of pure Mg. The measurements, a model PC4 300 Gamry potentiostat was
presence of SiC particles deteriorated the corrosion resis- used. Finally, electrochemical noise measurements (EN) in
tance of magnesium, and the corrosion resistance decreased both current and potential were recorded using two identical
with increasing SiC volume fraction, finding that galvanic working electrodes and a reference electrode (SCE). The
corrosion between Mg matrix and SiC reinforcement did electrochemical noise measurements were made recording
not significantly contribute to the overall corrosion rate. simultaneously the potential and current fluctuations at a
Salman et al. [15] carried out a comparative electrochemical sampling rate of 1 point per second during a period of
study of AZ31 and AZ91 magnesium alloys in 1 M NaOH 1024 seconds. Removal of the DC trend from the raw noise
and 3.5 wt. % NaCl solutions at room temperature. In 1M data was the first step in the noise analysis when needed.
NaOH solution, AZ31 alloy showed several potential drops To accomplish this, a least square fitting method was used.
throughout the experiment but AZ91 alloy did not. When Finally, the noise resistance, Rn , was then calculated as the
anodized at 3 V for 30 minutes in 1 M NaOH solution, the ratio of the potential noise standard deviation, σv , over the
anticorrosion behavior of anodized specimens was better current noise standard deviation, σi , according to:
than those of specimens which were not anodized. Finally,
σv
Budruk Abhijeet et al. [16] studied the corrosion behavior Rn = , (1)
of pure magnesium, Mg-Cu(0.3, 0.6 and 1 vol. %) and σi
Mg-Mo(0.1, 0.3 and 0.6 vol. %) composites in 3.5% NaCl where Rn can be taken as the linear polarization resistance,
solution, finding that the corrosion rate increased with R p in the Stern-Geary equation
increasing the volume fraction of reinforcement in both
composites. At the same volume fraction of reinforcement, ba · bc · 1
Icorr = (2)
molybdenum reinforced composites corroded faster than 2.23(ba + bc )R p
copper reinforced composites. Microscopic observations of
corroded specimens confirmed microgalvanic activity at the and thus, inversely proportional to the corrosion rate, Icorr .
matrix/reinforcement interfaces, which, together with a poor
quality of corrosion surface films, were responsible for the 3. Results
poor corrosion resistance of composites. Thus, the goal of
this research work is to study the effect of TiC reinforcing The resulting microstructures of both the AZ91E alloy and
particles on the corrosion resistance of an Mg-Al alloy in AZ91E/TiC composite are shown on Figure 1. The surface
3.5% NaCl solution. image obtained by SEM of a polished sample of AZ91E
alloy can be observed in Figure 1(a). It was not possible
2. Experimental Procedure to observe the grain boundaries, however, the primary α-
Mg phase, together with an eutectic phase aluminum rich
Chemical composition of tested Mg-Al alloy is given on surrounding the β phase constituted of Al12 Mg17 could
Table 1, where it can be seen that it contains Mn and Zn also be observed. Additionally, a few AlMn-base precipitates
as main alloying elements, corresponding to an AZ91E alloy. could be observed along the matrix area. Less than 30% in
Composites were fabricated by pressureless melt infiltration fraction area correspond to the eutectic phase, while that
of the AZ91E alloy into 44% TiC porous performs. The approximately a 60% it is occupied by the primary phase.
average TiC particles size was 1.12 μm. These powders were Figure 1(b) shows the composite surface distribution of the
sintered in an argon atmosphere at 1250◦ C during 60 AZ91E/TiC composite, where the particles reinforcement of
minutes, whereas infiltration was carried out at 950◦ C in TiC are visible with approximately 50% area fraction with
an argon atmosphere during 12 minutes. For the corrosion an average size of 1.5 μm. In the image, the dark zones
tests, a 3.5% NaCl solution was used at room temperature correspond to a porosity distributed on the surface and the
(≈25◦ C). Polarization curves were recorded at a constant small particles correspond to the MgAZ91E matrix with an
sweep rate of 1 mV s−1 from −800 to +800 mV interval average size of 1.0 μm. It was observed that the TiC particles
respect to open circuit potential (Ecorr ). A conventional did not present a good enough cohesion with the alloy, which
three electrodes glass cell was used with a graphite rod might produce a depletion of the particles from the matrix.
as auxiliary electrode and a saturated calomel electrode Polarization curves for the AZ91E alloy and AZ91E/TiC
(SCE) as reference. Corrosion current density values, Icorr , composite in the 3.5% NaCl solution is shown on Figure 2.
were calculated by using the Tafel extrapolation method These curves showed an active behavior only, without
and by taking an extrapolation interval of ±250 mV around any passive zone, instead, an anodic limiting current was
the Ecorr value once stable. Linear polarization resistance, observed, with values of 6.11 and 0.16 A/cm2 for AZ91E
LPR, measurements were carried out by polarizing the alloy and AZ91E/TiC composite, respectively. The Ecorr value
specimen from +10 to −10 mV in respect to Ecorr , at a was more active for the base alloy, close to −1390 mV,
International Journal of Corrosion 3

(a) (b)
β

α-Mg
Eutectic
AlMn

Sig Spot HV Mag WD Scan Del 50 μm

SE 5 30.0 kV 1500x 9.6 mm 37.04 s ETD MgAZ91 MgAZ91E/TiC 5000x 1 μm

Figure 1: SEM micrograph of AZ91E alloy and AZ91E/TiC composite.

Table 1: Chemical composition of tested AZ91E alloy.

Element Al Mn Zn Si Fe Cu Ni Mg
wt. % 8.7 0.24 0.7 0.20 0.005 0.015 0.001 Bal.

0.5
−600
0.25
0
Potential, E (V versus SCE)

Ecorr (mV versus SCE)

−800
−0.25 AZ91E/TiC
−0.5
−1000
−0.75 AZ91E/TiC
−1 AZ91E
−1200
−1.25

−1.5
AZ91E
−1400
−1.75

−2 0 5 10 15 20 25
10−6 10−5 10−4 10−3 10−2 10−1 100 101
Time (h)
Current density, I (A cm−2 )
Figure 3: Change in the Ecorr value with time for AZ91E alloy and
Figure 2: Polarization curves for AZ91E alloy and AZ91E/TiC AZ91E/TiC composite in 3.5% NaCl solution.
composite in 3.5% NaCl solution.

for the AZ91E base alloy showed a tendency to increase

than that for composite, which had a value of −980 mV. and, after that, to decrease as time elapsed, and, thus, the
The corrosion current density value was also lower for the corrosion rate decreases first and after that it increases,
composite, 8.8 × 10−5 A cm−2 , than that for the base alloy, indicating the cracking or detachment of any protective
2.9 × 10−3 A cm−2 .The change in the Ecorr value with time, corrosion products layer, showing the nonprotective nature
Figure 3, shows that at all times, the base alloy kept more of this layer. It could be also due to the fact that the Al12Mg17
active values than those for the composite, although the later particles enhance the dissolution of the α-Mg phase since it
had a tendency towards nobler values. The change in the is cathode as compared to the matrix.
R p value with time for both the base metal and composite Nyquist diagrams for the base alloy, Figure 5, showed
is given on Figure 4, where it can be seen that the AZ91E a capacitive semicircle at high frequencies, but at lower
base alloy showed lower R p values, and thus, higher corrosion or intermediate frequencies, the data described a straight
rates, than the AZ91E/TiC composite. However, the R p value line, indicating that the corrosion process is under a mixed
4 International Journal of Corrosion

Table 2: Electrochemical parameters obtained from polarization curves.

Alloy Ecorr (mV) Icorr (A cm−2 ) βa (mV/dec) βc /(mV/dec) Anodic limit current (A cm−2 )
AZ91E/TiC −980 8.8 × 10−5 170 187 0.16
AZ91E −1390 2.9 × 10−3 155 177 6.11

600 −800
AZ91E/TiC

500 −600

Zim (Ohms cm−2 )

400
R p (Ohms cm−2 )

−400
0h
300 4h
−200 8h
AZ91E/TiC 20 h
200
0 24 h
100
AZ91E
200
0
0 5 10 15 20 25 −200 0 200 400 600 800 1000 1200 1400 1600 1800 2000
Time (h) Zre (Ohms cm−2 )

Figure 4: Change in the R p value with time for AZ91E alloy and Figure 6: Change in the Nyquist diagrams with time for AZ91E/TiC
AZ91E/TiC composite in 3.5% NaCl solution. composite in 3.5% NaCl solution.

−200 0.105 −1395

− 10 AZ91E
0.1 −1396
Zim (Ohms cm−2 )

−8 24 h

−6 0.095 −1397
−150

E (mV versus SCE)

−4
I (mA cm−2 )

−1398
Zim (Ohms cm−2 )

0.09
−2
0.085 −1399
−100 12 15 18 21
Zre (Ohms cm−2 ) 0.08 −1400

0.075 −1401
0h
−50 0.07 −1402
8h 4h
0.065 −1403
20 h 0 200 400 600 800 1000
0 24 h Time (s)
0 100 200 300
Zre (Ohms cm−2 ) Figure 7: Noise in current and potential for AZ91E alloy in 3.5%
NaCl solution.
Figure 5: Change in the Nyquist diagrams with time for AZ91E
alloy in 3.5% NaCl solution.
other hand, Nyquist diagrams for AZ91E/TiC composite,
Figure 6, showed a capacitive-like, depressed semicircle at
mechanism: charge transfer from the metal to the interface high frequencies, followed by an inductive loop at low
through the double electrochemical layer, and by the diffu- and intermediate frequencies, indicating that the corrosion
sion of aggressive ions through the corrosion products layer, process is under control of adsorption of chloride ions at
such as evidenced by polarization curves shown on Figure 2. the metal/solution interface. The diameter of the semicircles
This diffusion phenomena are the responsible of the anodic decreased as time elapsed, indicating an increase in the
limit current observed on the polarization curve, Figure 2. corrosion rate with time and the nonprotective nature of the
The diameter of the high frequency capacitive semicircle, corrosion products.
described as the charge transfer resistance, Rct , equivalent The time series in both potential and in current for the
to the polarization resistance, R p , in (2) decreased as time AZ91E base alloy is shown on Figure 7, where it can be
elapsed, with an increase in the corrosion rate with time. seen that in both cases, the time series showed transients in
This decrease in the Rct value as time increases is similar high intensity or amplitude, with a sudden decrease in their
to the decrease in the R p value shown in Figure 4. On the values. Each transient represents the rupture of the corrosion
International Journal of Corrosion 5

0.04 towards localized type of corrosion, being the base alloy more
AZ91E/TiC susceptible to this type of degradation. By using the potential
−1100
0.03
noise standard deviation, σv , and dividing it over the current
noise standard deviation, σi , we can obtain a noise resistance,

E (mV versus SCE)

0.02 −1105
Rn and its change with time for the different steels is shown
I (mA cm−2 )

0.01 in Figure 9. This figure shows that Rn decreased as time

−1110 elapsed, in a similar way as that described by the polarization
0 resistance value, R p , shown on Figure 4, and the charge
transfer resistance on Figures 5 and 6. The AZ91E base
−0.01 −1115
alloy exhibited lower Rn values than those exhibited by the
−0.02 composite. Thus, if Rn replaces R p in (2) we can see that the
−1120 base alloy showed corrosion rates than the composite. Thus,
0 200 400 600 800 1000
by using any analysis tool, the composite showed a lower
Time (s)
corrosion rate than the AZ91E base alloy.
Figure 8: Noise in current and potential for AZ91E/TiC composite SEM micrographs of corroded specimens are shown
in 3.5% NaCl solution. on Figure 10 together with X-ray analysis of corrosion
products found on the composite. It can be seen that, on
600 the AZ91E/TiC composite, some corroded particles can be
found, detached from the matrix, which give as a result the
transients in current as shown on Figure 7. Preferential attack
500
along the matrix and the TiC particles interfaces can be seen
due to a different electrochemical potential between the α-
R n (Ohms cm−2 )

400
Mg, β-Mg, AlMn inclusions, and TiC particles, that is, a
AZ91E/TiC galvanic effect. As evidenced by Tiwari et al. [14] who studied
300 the corrosion behavior of two SiC Mg-based MMC, Mg-
6SiC, and Mg-16SiC (vol. %) in aerated 1M NaCl and found
200 that the presence of SiC particles deteriorated the corrosion
AZ91E
resistance of Mg, and the corrosion resistance decreased with
100 increasing SiC volume fraction. Thus, it is not expected that
the corrosion rate of pure Mg decreases with the addition
0 of 56 wt. % of particles just because the contents of Mg
0 5 10 15 20 25 is lower for the composite. The presence of TiC particles
Time (h) together with the presence of different phases with different
Figure 9: Change in the noise resistance value, Rn , with time for electrochemical potential values, induce the presence of
AZ91E alloy and AZ91E/TiC composite in 3.5% NaCl solution. microgalvanic cells where the TiC and Al12Mg17 particles
act as cathodes, whereas α-Mg acts as anode, accelerating,
thus, the corrosion rate of the later.
products layer, and, thus, an increase in the localized current On the other hand, the corroded surface of the AZ91E
density; once the corrosion products layer is rebuilt, the base alloy showed porous, cracked layer of corrosion prod-
current density decreases. Thus, the base alloy exhibited ucts, which do not allow the electrolyte to have access
a high susceptibility towards a localized type of corrosion to the metal and give rise to the transients shown on
such as pitting. On the other hand, the time series for the Figure 8. On the other hand, X-ray data shows that the main
AZ91E/TiC composite, Figure 8, showed transients of much corrosion products were Mg(OH)2 together with some TiC
lower intensity than those shown by the base alloy, indicating particles. This can be due to the fact that the presence of
a lower susceptibility towards pitting corrosion. There is a cathodic phases, such as the Al12Mg17 particles shown on
factor called “Localization Index, LI,” defined as Figure 1, during the alloy/composite formation enhances the
σi susceptibility of hydrolysis reaction. Once hydrolysis reaction
LI = , (3) starts, corrosion reaction can proceed by oxidation of Mg as
irms
Mg2+ resulting in the formation of Mg(OH)2 as follows:
where σi is the current noise standard deviation and irms,  
the current root mean square value [17] which establishes Mg2+ + 2 OH− −→ 2Mg(OH). (4)
that for LI values between 1 and 0.1, the type of corrosion
The Mg2+ ions generate after oxidation of Mg (Mg → Mg2+ ),
that the material suffers is localized; when the LI value lies
while OH− releases after oxygen reduction:
between 0.1 and 0.01, there is a mixture of both uniform and
localized types of corrosion; finally, for LI values between 2H2 O + O2 + 4e− −→ 4OH− . (5)
0.01 and 0.001, there is a tendency towards a uniform type
of corrosion. LI values for AZ91E base alloy and AZ91E/TiC This reaction explains the reason why Mg is not detected on
composite were 0.78 and 0.2, respectively. In view of these the corrosion products because it is as Mg(OH)2 . Because
results, we can establish that both alloys have a tendency of insolubility of Mg(OH)2 in the solution it accumulates
6 International Journal of Corrosion

(a) (b)

10 μm EHT = 20.00 kV Mag = 2.00 kX

CIICAp File name = M2-05.jpg
Capa Pas 3000x 10 µm WD = 34 mm Signal A = SE1

1200

1000

800
Intensity (a.u.)

600

400

200

0
0 10 20 30 40 50 60 70 80
2Θ (degrees)

TiC
Mg(OH)2
(c)

Figure 10: SEM micrograph of corroded (a) AZ91E/TiC composite and (b) AZ91E base alloy, and (c) X-ray diffractogram of corrosion
products in the composite.

at the metal/solution interfaces of the electrode resulting in oxide surface, (ii) formation of a soluble hydroxychloride
the formation of corrosion products layer, leaving inside it aluminium salts, and (iii) dissolution of the oxide where
the uncorroded TiC particles found in the X-ray pattern. the film is thinner. Since adsorption of chloride ions is the
Formation of Mg(OH)2 with the increase of potential in first step of localized attack, it may therefore be inferred
the anodic region and their subsequent accumulation at the that susceptibility to pitting corrosion is likely to be more
electrode interfaces seems to be the main reason for the pronounced for a composite than for a base alloy. It has
occurrence of the diffusion limiting behaviour in the anodic been reported [18–20] that the corrosion resistance of
region of the base alloy and composite polarization curves composites is less than their Mg alloys because the reinforce-
observed on Figure 2. ment/interface acts as potential sites for pitting corrosion.
Electrochemical noise measurements have shown that On the contrary, the corrosion resistance of composites
both the base alloy and composite were susceptible to pitting has been reported to be higher than that for their alloys
corrosion, due to chloride ions adsorption, although the [21–23]. It was explained that as though pits were formed,
diffusion phenomena is less pronounced in the base alloy. their growth was restricted by the presence of particles and
The mechanism of pitting initiation involves three steps: effective area offered by the matrix for corrosion to take place
(i) adsorption and penetration of chloride ions on the with reduced rate. We could observe this behaviour on this
International Journal of Corrosion 7

work; the pitting corrosion susceptibility of the composite double cycle polarization technique,” Corrosion Science, vol.
was lower than that for the base alloy. In other works [24, 25] 41, no. 6, pp. 1185–1203, 1999.
it has been reported that the corrosion resistance of the [11] A. Pardo, M. C. Merino, A. E. Coy, R. Arrabal, F. Viejo, and
base alloys remains unchanged by the reinforcement of the E. Matykina, “Corrosion behaviour of magnesium/aluminium
particles. However, a galvanic effect between the TiC particles alloys in 3.5 wt.% NaCl,” Corrosion Science, vol. 50, no. 3, pp.
and matrix that enhanced the composite corrosion rate was 823–834, 2008.
[12] C. A. Nunez-Lopez, P. Skeldon, G. E. Thompson, P. Lyon, H.
evident. In the present work, occurrence of inductive loops
Karimzadeh, and T. E. Wilks, “The corrosion behaviour of Mg
shown by Nyquist diagrams for the base alloy suggest the alloy ZC71/SiCp metal matrix composite,” Corrosion Science,
adsorption of corrosive chloride ions at their metal/solution vol. 37, no. 5, pp. 689–708, 1995.
interface, whereas for the composite the most important [13] J. Suqiu, J. Shusheng, S. Guangping, and Y. Jun, “The
process is diffusion of aggressive ions through the corrosion corrosion behaviour of Mg alloy AZ91D/TiCp metal matrix
products layer. composite,” Materials Science Forum, vol. 488-489, pp. 705–
708, 2005.
[14] S. Tiwari, R. Balasubramaniam, and M. Gupta, “Corrosion
4. Conclusions behavior of SiC reinforced magnesium composites,” Corrosion
Science, vol. 49, no. 2, pp. 711–725, 2007.
A research on the addition of 56 wt. % TiC particles on
[15] S. A. Salman, R. Ichino, and M. Okido, “A Comparative
the corrosion resistance of the EZ91E Mg-base alloy in 3.5% electrochemical study of AZ31 and AZ91 magnesium alloys,”
NaCl solution has been carried out using different electro- International Journal of Corrosion. In press.
chemical techniques. All different techniques have shown [16] S. Budruk Abhijeet, R. Balasubramaniam, and M. Gupta,
that the addition of TiC particles decreased both the uniform “Corrosion behaviour of Mg-Cu and Mg-Mo composites in
corrosion rate of the base alloy and the resistance towards 3.5% NaCl,” Corrosion Science, vol. 50, no. 9, pp. 2423–2428,
pitting type of corrosion. Some evidence of a galvanic effect 2008.
between the matrix and the TiC particles was found. Both [17] H. H. Huang, W. T. Tsai, and J. T. Lee, “Electrochemical behav-
the base alloy and the composite showed a tendency towards ior of A516 carbon steel in solutions containing hydrogen
pitting corrosion, although on the base alloy the adsorption sulfide,” Corrosion, vol. 52, no. 9, pp. 708–716, 1996.
of chloride ions seemed to the corrosion-controlling factor, [18] O. P. Modi, M. Saxena, B. K. Prasad, A. H. Yegneswaran,
and M. L. Vaidya, “Corrosion behaviour of squeeze-cast alu-
whereas in the composite the diffusion of the aggressive ions
minium alloy-silicon carbide composites,” Journal of Materials
was the rate controlling factor. Science, vol. 27, no. 14, pp. 3897–3902, 1992.
[19] H. Y. Yao and R. Z. Zhu, “Interfacial preferential dissolution on
References silicon carbide particulate/aluminum composites,” Corrosion,
vol. 54, no. 7, pp. 499–507, 1998.
[1] C. A. Leon, V. H. Lopez, E. Bedolla, and R. A. L. Drew, [20] M. S. N. Bhat, M. K. Surappa, and H. V. S. Nayak, “Corrosion
“Wettability of TiC by commercial aluminum alloys,” Journal behaviour of silicon carbide particle reinforced 6061/Al alloy
of Materials Science, vol. 37, no. 16, pp. 3509–3514, 2002. composites,” Journal of Materials Science, vol. 26, no. 18, pp.
[2] A. Contreras, C. A. León, R. A. L. Drew, and E. Bedolla, 4991–4996, 1991.
“Wettability and spreading kinetics of Al and Mg on TiC,” [21] S. J. Harris, B. Noble, and A. J. Trowsdale, “Corrosion
Scripta Materialia, vol. 48, no. 12, pp. 1625–1630, 2003. behaviour of aluminium matrix composites containing silicon
[3] D. Muscat, K. Shanker, and R. A. L. Drew, “Al/TiC composites carbide particles,” Materials Science Forum, vol. 217–222, no.
produced by melt infiltration,” Materials Science and Technol- 3, pp. 1571–1579, 1996.
ogy, vol. 8, no. 11, pp. 971–976, 1992. [22] S. Y. Yu, H. Ishii, and T. H. Chuang, “Corrosive wear of
[4] A. Contreras, A. Albiter, and R. Pérez, “Microstructural prop- SiC whisker- and particulate-reinforced 6061 aluminum alloy
erties of the Al-Mg/TiC composites obtained by infiltration composites,” Metallurgical and Materials Transactions A, vol.
techniques,” Journal of Physics Condensed Matter, vol. 16, no. 27A, no. 9, pp. 2653–2662, 1996.
22, pp. S2241–S2249, 2004. [23] E. P. Raju, K. Balakrishnan, and P. B. Shrinivasan, “Picolines
[5] S. Candan, “An investigation on corrosion behaviour of as corrosion inhibitors for aluminium alloy in hydrochloric
pressure infiltrated Al-Mg alloy/SiC composites,” Corrosion acid,” Bulletin of Electrochemistry, vol. 13, pp. 107–113, 1970.
Science, vol. 51, no. 6, pp. 1392–1398, 2009. [24] L. Pinto and E. Zschech, “Mechanical properties and corrosion
[6] S. Candan and E. Bilgic, “Corrosion behavior of Al-60 vol.% behavior of extrusions for aircraft applications made by
SiC composites in NaCl solution,” Materials Letters, vol. 58, no. discontinously silicon-carbide-reinforced aluminum matrix
22-23, pp. 2787–2790, 2004. composites,” Materials Science Forum, vol. 217–222, no. 3, pp.
[7] S. Candan, “Effect of SiC particle size on corrosion behavior of 1593–1598, 1996.
pressure infiltrated Al matrix composites in a NaCl solution,” [25] H. Sun, E. Y. Koo, and H. G. Wheat, “Interfacial preferential
Materials Letters, vol. 58, no. 27-28, pp. 3601–3605, 2004. dissolution on silicon carbide particulate/aluminum compos-
[8] Z. Ahmad and B. J. Abdul Aleem, “Degradation of aluminum ites,” Corrosion, vol. 47, no. 9, pp. 741–749, 1991.
metal matrix composites in salt water and its control,”
Materials and Design, vol. 23, no. 2, pp. 173–180, 2002.
[9] C. Chen and F. Mansfeld, “Corrosion protection of an Al
6092/SiC metal matrix composite,” Corrosion Science, vol. 39,
no. 6, pp. 1075–1082, 1997.
[10] G. E. Kiourtsidis, S. M. Skolianos, and E. G. Pavlidou, “A study
on pitting behaviour of AA2024/SiC(p) composites using the
Journal of International Journal of International Journal of Smart Materials Journal of
Nanotechnology
Hindawi Publishing Corporation
Corrosion
Hindawi Publishing Corporation
Polymer Science
Hindawi Publishing Corporation
Research
Hindawi Publishing Corporation
Composites
Hindawi Publishing Corporation
http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014

Journal of
Metallurgy

BioMed
Research International
Hindawi Publishing Corporation Hindawi Publishing Corporation
http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014

Nanomaterials
Submit your manuscripts at
http://www.hindawi.com

Journal of Journal of
Materials
Hindawi Publishing Corporation
Nanoparticles
Hindawi Publishing Corporation
http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014

Nanomaterials
Journal of

Advances in The Scientific International Journal of

Materials Science and Engineering
Hindawi Publishing Corporation
Scientifica
Hindawi Publishing Corporation Hindawi Publishing Corporation
World Journal
Hindawi Publishing Corporation
Biomaterials
Hindawi Publishing Corporation
http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014

Journal of Journal of Journal of Journal of Journal of

Nanoscience
Hindawi Publishing Corporation
Coatings
Hindawi Publishing Corporation
Crystallography
Hindawi Publishing Corporation
Ceramics
Hindawi Publishing Corporation
Textiles
Hindawi Publishing Corporation
http://www.hindawi.com
http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 http://www.hindawi.com Volume 2014 Volume 2014