Journal of Surface Engineered Materials and Advanced Technology, 2011, 1, 62-72
doi:10.4236/jsemat.2011.12010 Published Online July 2011 (http://www.SciRP.org/journal/jsemat)
AZ91 Magnesium Alloys: Anodizing of Using
Environmental Friendly Electrolyt es
N. A. El Mahallawy1, M. A. Shoeib2, M. H. Abouelenain3
1The Design and Production Engineering Department, Faculty of Engineering, Ain Shams Un iversity, Cairo, Egypt; 2Surface Coating
Department, Central Metallurgical Research & Development Institute, Helwan, Cairo, Egypt; 3Petroleum Marine Service, Cairo,
Egypt.
Received March 14th, 2011; revised May 30th, 2011; accepted Jun e 8th, 2011.
ABSTRACT
An anodizing process, based on environmental friendly electrolyte solutions has been studied on AZ 91 magnesium al-
loys by using three types of electrolytes: the first is based on sodium silicate, the second on sodium hydroxide-boric
acid-borax and the third on sodium silicate-potassium hydroxide-sodium carbonate-sodium tetra borate. A pretreat-
ment including fluoride activation was applied before the anodizing process. It was found that the anodic film thickness
increases as current density or anodizing voltage increases. It is also increased with deposition time until the deposition
stops due to the formation of a thick anodic film. Optimization of the anodizing conditions - current density and deposi-
tion time - was ma de for each electrolyte. Characterization of anodizing layer was achieved by determination of surface
morphology, microstructure, phase analysis, coat thickness, adhesion and corrosion resistance. In all cases, excellent
adhesion and corrosion resistance was obtained. A corrosion efficiency ranging from 94% to 97% was reached; the
highest value corresponding to the third electrolyte.
Keywords: Anodizing, Magnesium AZ91, Corrosion, Characterization, Environmental Friendly Electrolytes
1. Introduction
Magnesium and its alloys have received great attention
because of their superior properties, such as low density,
high specific strength/stiffness, excellent dimensional
stability and elec tromagnetic shielding property, superior
damping capacity, high creep strength, good machinabil-
ity, weldability, high impact resistance, high recyclabili-
ty, as well as thermal and electrical conductivities [1,2].
They are used in fields where weight reduction is critical
or where particular technical requirements are required
such as automotive, aeronautic and aerospace including
space station, artificial satellite, space shuttle, nuclear
energy, electronic and military industries, together with
AVCC (Audio video-Comp uter -Communication) equip-
ment, portable tools, supporting goods, etc. [3,4]. How-
ever, magnesium and its alloys are highly susceptible to
corrosi on esp ecial ly in harsh environmental conditions.
Several techniques have been applied in order to im-
prove the surface properties of magnesium alloys. Ano-
dizing is among the promising techniques for surface
protection of Mg alloys; however, most existing anodiz-
ing processes use toxic chromate, harmful phosphate
or/and fluorides. Therefore, it is still worthy to develop
new environmental friendly anodizing processes [5].
In this paper, the anodizing process, based on envi-
ronmental friendly electro lyte solutio ns using DC c urrent
have been developed to enhance the corrosion resistance
of magnesium AZ91alloy. The electrolytes contain none
of the chromates, phosphates or fluorides solutions. Op-
timization of the process parameters was achieved and
the anodizing layer was characterized by its adhesion
strength, thicknes s, phase analysis, microstructure, a s well
as its corrosion resistance on AZ91 magnesium alloys .
2. Experimental Technique
The die-cast Mg alloy AZ91, whose chemical composi-
tion is shown in Table 1, was prepared as circular discs
of 50 mm diameter and 10 mm thickness. The chemical
composition was analyzed by Atomic Emission Spec-
troscopy (AES).
Anodizing experiments were done by using two
group s of c hemic als: che micals for pretreatment and che-
micals for anodizing processes. The pretreatment proce-
dure used commonly in electroless processes [7], shown
in Table 2, was applied.

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
63
Table 1. Chemical composition of AZ91 Mg alloy (wt%)
Al Zn Mn Si Cu Fe K Mg
8.77 0.74 0.18 0.01 0.001 0.001 0.01 BAL
Table 2. Pret reatment procedure applied before anodizing process.
Stage no Name Symbo l Con stituent or condition
1 Mechanical Preparation
and Cl eani ng Specimens are first polished by using finer grades of waterproof sili c on ca rbid e ab ra s i ve pa p ers , rin sed in distilled water, supersoni c degrea sing in acetone and finally dried in air.
2
Alka line cleanin g
Sodium hydroxide NaOH 50g/L
Sodium phosphate Na3PO4 10g/L
Temperature Room t emperature
Tim e 8 - 10 min
Spec im ens bec am e brigh ter t han in step on e b ecaus e Mg is pas sive i n alk alin e med ia so th at du st, g rease… etc were removed from
the surface of magnesium alloy.
3 Acid etching
Chromium trioxide CrO3 125 g/L
Nitric Acid HNO3 (70% V/V) 110 ml/L
Temperature Room Temperature
Tim e 30 - 60 s
Gross surfac e scale or o xides a re removed a nd rep laced b y preferr ed oxid es to be removing la ter. Etching treatments also provide
surface pits to act as sites for m echanical int erlocking to improve adh es ion.
4 Fluoride activation
Hydrofluoric acid HF (40%V/V) 385 ml/L
Temperature Room Temperature
Tim e 10 m in
Removing residual oxides, that created in the above step and replacing it with a thin layer of MgF2 .
Three types of electrolytes were used in anodizing
processes. The chemical composition and operating con-
ditions of each type are shown in Table 3. The electro-
lyte cell was built with stai nless steel hoop as catho de 10
cm height and 12 cm diameter wide enough to provide an
even current distribution. The cell was connected to a DC
power supply (MUNK- PSP - VARI-PULS, 10 A, 300 V,
USA).The current density and voltage were measured
using two digita l ammeter s (DT 9205 N, Chi na).
In order to optimize the effect of deposition time and
current de nsity on the deposition layer thickness, the ex-
periments were divided into two groups: in the first
group, the deposition time was varied for the three elec-
trolytes using a constant current density of 20 mA/cm2;
in the se cond gr oup, the curre nt densi ty was varied while
the deposition time was constant. The anodizing process
was made at temperature of (30 - 40)˚C .The observation
of sparks, which indicates the occurrence of deposition
showed that for a time less than 1.5 minutes almost no
deposition occurs. The time was increased from 1.5 mi-
nutes until the deposition stopped-marked by no sparks.
After anodizing processes, the oxide layers obtained
were sealed by immersion in bo iling distilled water for a
time equal to that of the deposition in each case. Sealing
of the anodized film is necessary in order to achieve an
abrasion and corrosion resistant film by precipitation of
hydrated base metal species inside the pores [6,11].
After anodizing, the surface morphology was ex-
amined using a scanning electron microscope (SEM)
model; JEOL JSM 5410. The grain size of the anodic
film was determined by X-ray diffraction (XRD) model;
PANalytical X’Pert. The XRD technique, using
s mall -angle X-ray scattering (SAXS) was used to analyze
the phases in t he a no d ic co a ting. The corrosion resistance
of an odized coat layer on AZ91D alloy was performed in
3.5 wt% NaCl solution to determine the polarization re-
sistance at ambient temperature using AUTOLAB
PGSTAT 30
The anodic film thickness was measured by the coat-
ing thickness meter (posi-tector 6000 FN). Hydraulic
adhesion tester (Elcometer 108) measured the adhesion
of the anodic film. The microhardness measurements

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
64
Table 3. Chemical composition and operating conditions of electrolytes.
Electrolyte (1) [8]
sodium silicate (Na2SiO2) 122 g/l
Temp (30 - 40)˚C
Current density 16 mA/cm2 to 31 mA/cm 2
Deposition time (minute) 1.5 to 11
Ele ctro ly te (2) [9]
Sodium hydroxide (NaOH) 50.0 g/L
Boric acid(H3BO3) 10.0 g/L
Borax or hydrous sodium borate (Na2B4O7.10H2O) 20.0 g/ L
Temp (30 - 40)˚C
Current density 16 mA/c m 2 to 20 mA/cm2
Deposition time (minute) 1.5 to 9
Ele ctro ly te (3) [10]
Sodium silicate (Na2SiO3) 50 g/l
Pota ss ium hydr o xide (KOH ) 50 g/l
Sodium carbonate (Na2CO3) 50g/l
Sodium tetra borate (Borax Na2B4O7 ) 30 g/l
Temp (30 - 40)˚C
Current density 16 mA/cm2 to 31 mA/cm 2
Deposition time (minute) 1.5 to 9
were carried out by the hardness tester model Shimdsu
type M, and the surface roughness by Elcometer 223.
The microhardness measurements of coat layers were
performed on specimens cross-sections using 50-gram
load for 15 seconds.
3. Results and Discussion
3.1. Effect of Pretreatment on Surface
Morphology
Study of the surface morphology after the pretreatment
procedure, shown Fig ure 1, indicates the formation of
pits, which is expected to improve the adherence of coat
layer to the substrate. The use of fluoride activation in
the pretreatment is also expected to add a layer of MgF2
which minimizes the effect of local corrosion cells by
cre ating an equipotentialized surface [7].
3.2. Effect o f the Deposition Time on the Coating
Thickne ss
Figure 2 shows that the coat thickness for the three elec-
trolytes incre ases with the depo sition time, rapidly in the
first 3 minutes then with a slow rate after 3 to 9 minutes
until it levels o ff after 9 minutes. T his behavior is due to
the increase in the thickness of the coat layer acting as a
barrier to the flow of current, which decreases the rate of
oxidation of magnesium. From the results, the optimum
deposition time used to obtain maximum coat thickness
was 9 minutes for the three electrolytes at the same oper-
ating conditions with 20 mA/cm2 current d ensit y. In ge n-
eral, the coat thickness was the highest for electrolyte (1)
- 42 µm, followed by electrolyte (2) - 32 µm, then elec-
trolyte (3)-28 µm.
Comparison between the maximum coating thickness
obtained in the present work and previous work [8-10]
indicates a general agreement, however, difference in
values are obtained due to the difference in base metal
composition, current density and temperature. For exam-
ple, for electrolyte 1, maximum coating layer thickness
was 42 µm while in previous work [8] on AZ91, the
anodic film was 25 µm at 60 C, 20mA/Cm2 and 9 mi-
nutes coating time. The large thickness in the present
work is due to the lower anodizing temperature. This
explanation is based on previous work [12,13], which

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
65
indicates that
(a) (b)
Figure 1. Surface morpholog y of the AZ91 magnesium alloy (a) before pre-treatment (b) after pre-treatment.
Figure 2. Effect of deposition time on coat thickness by using three electrolytes and pre-treatment procedure at te mp.
(30 - 40)˚C and constant c urrent dens ity –DC-2 0 mA/cm2.
the temperature and coat thickness are inversely propor-
tional.
3.3. Effect of Current Density on Coating
Thickness
The current density is a main electric parameter in ano-
dizing. Figure 3 shows the effect of current density on
coat thickness for the three types of electrolytes, using a
deposition time of 9 minutes (optimum) at a temperature
(30 - 40)˚C. With increasing current density, the driving

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
66
force for anodizing increases, which enhances the coat
development and formation. The thickness increased first
Figure 3. Effect of current density on coating thickness by
using three electrolytes and constant deposition time at 9
minutes.
rapidly up to 20 mA/cm2 then t he rate slowed d own unt il
almost no increase in thickness of the deposited oxide
layer was obtained. This threshold current density was
25mA/cm2 for electrolyte (1) and (3) and 20 mA/cm2
for electrolyte (2), resulting in coat thickness of 50 µm
for electro lyte (1) and 30 µm for electrolytes (2) and(3).
For coat development, there are three ways by which
anions move to the anode, mainly diffusion, convection
and electric migration [14]. The latter being the main one
during anodizing. It can be said that as the anodizing
layer thickness increases beyond a certain value, the
electric migration is suppressed due to the higher resistivi-
ty of the formed oxide layer marked by stop of sparking.
3.4. Oxide Formation Mechanism
The anodizing process is a dynamic equilibrium of par-
tial processes of oxide formation, the others. The me-
chanism of anodizing process could be explained disso-
lutio n, and oxygen e voluti on. T he d ominance of one p ar-
tial process will suppress according to the growth of
anodic film, in which the pre-existing film was streng-
thened, modified or substituted repeatedly by spark-
ing/break- down events. The sparking occurs by the ac-
tion of the strong electric field created during anodiza-
tion. Anions in the electrolyte first need to arrive at the
anode/elec- trolyte interface and then enter into anodic
coatings [15].
The general reactions, occurring in the anodizing
process for Mg, are as follow:
2
Mg Mg2e
+−
→+
(1)
22
4OHO2H O4e
−−
→ ↑++
(2)
( )
2
2
Mg2OHMg OH
+−
+→
(3)
( )
2
2
MgOHMgOH O→+
(4)
( )
2 24
2
MgOHSiOMgSiO+→ (5)
During the oxidation process, the Mg ions, produced
by reaction (1), combine with the OH− in the electrolyte
solution to form Mg(OH)2 and Mg2SiO4 (reactions (3)
and (5), respectively). Due to the thermal energy from
the sparks in the PEO process, the hydroxides change to
oxide compounds by the dehydration process, reaction
(4). The coating formation processes, reactions (3), (4)
and (5) may be promoted by a high concentration of the
electrolyte, containing more SiO2 and OH− ions.
Based on previous observations during anodizing of
AZ 91 magnesium alloy [5], formation and dissolution of
oxide/hydroxide films occur simultaneously. The present
results indicate that the anodic film growth is dominant
up to 20 - 25 mA/cm2, b eyo nd which t he thi ck ness o f th e
oxide layer remains almost constant due to the break-
down and/or dissolution of this thin film as previously
noticed.
3.5. Surface Morphology of Anodic Coat
The surface morphology of anodic coat, Figures 4-6,
revealed the presence of pores with different shapes and
sizes distributed all over the surface. However, the pores
are very small and do not have full penetration to the
substrate surface. Different pore size and density were
observed depending on the electrolyte. Electrolyte (1)
created many pores of approximately 7 µm diameter,
Figure 4, while electrolyte (2) created a few pores of
approximately 1 µm diameter, Figure 5, and electrolyte
(3) created a few pores of (2 - 3) µm diameter, Figure 6.
These differences in pore diameters result from the dif-
ferences of spark behavior and evolution of gases, as in
electrolyte (1) the spark was stronger and accompanied
with higher evolution of gases compared to electrolytes
(2) and (3).
Micro cracks are also visible on the coat surface. They
are formed due to thermal stresses resulting from rapid
cooling of the oxides by the electrolyte acting as a coo-
lant.
Difference crack sizes are also observed in the coat
layer due to the presence of different oxides, with differ-
ent shrinkage rates [16,17] depending on the type of
electrolyte (see next paragraph), Figures 4-6 .
The cracks are probably formed in week regions,
where the localized film layers were destroyed prior to
other regions. However, new anodizing products formed
in/around the broken regions rapidly and intensively so
that the existing microdefects were filled up or mended
by the fresh products. This is clear from the occurrence
of cracks on the surface but not reaching the depth.

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
67
3.6. Phase Analys is in Coat Layer Using XRD
and EDX X-ray diffraction patterns of the specimen anodized by
Figure 4. SEM morphology show ing the coat surface using electro lyte (1).

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
68
Figure 5. SEM morphology showing the coat thickness using electrolyte (2).
Figure 6. SEM morphology showing the coat surface using electrolyte (3).

Current Distortion Evaluation in Traction 4Q Constant Switching Frequency Converters
69
using electrolyte (1), Figure 7, indicate that the domi-
nating phase is MgO, followed by smaller amounts of
SiO2 and M g as s hown i n Table 4 , while in case o f elec-
trolyte(2), the dominating phase is MgO, Mg and B2O3.
For electrolyte (3), the dominating phase is MgO, fol-
lowed by SiO2, Mg and Mg2SiO4. The occurrences of
these phases indicate that the substrate and the electro lyte
both contrib ute in forming the coat layer.
The EDX analysis across the anodic coat layer, Table
5, indicates that the percentage of oxygen and silicon
decreases from the surface towards the substrate (zone III
> zone II > zone I). This indicates that the coat layer acts
as a barrier to decrease the rate of oxidation of magne-
sium. It was found previo usly [18 ] that when a r elatively
thick coating was established, an excessive oxygen evo-
lution is observed. This could explain the increase in
oxygen at the exp ense of the Mg on the outer l ayer.
3.7. Microstructure of the Coat Layers and
Crystal Size
The cross-section view of the coat layers for all three
electrolytes, Figure 8, s hows that anod ized coating films
are relatively uniform in thic kness and that the pores are
present but do not completely extend to the base metal.
Pores result from the generation of sparks and evolution
of gases from the hydrolysis of water [16]. These pores
are relatively uniform in distri bution.
The crystal size of the anodic coat determined by
X-ray diffraction (XRD), indicate that all crystal phases
are in the nano scale with sizes 4 to 5 nm, Table 6. This
means that the three electrolytes result in almost similar
crystal size, as the MgO is the dominating phase in all
coats.
3.8. Coat Adhesion
An excellent adhesion exceeding 18 MPa between the
anodic film and the substrate was found for all speci-
mens. This value is larger than for electroless nickel
plating on anodized magnesium alloy (about 11 MPa)
[19]. This adhesion is enhanced by the formation of pits
formed by the pretreatment procedure, which increased
the surface roughness and contributed to increased adhe-
sion of the coat layer as reported by Adachi et al. [20]. In
additions, the analysis of the obtained anodic film layers
showed that they contain (Mg - MgO- Mg2SiO4). This
indicates that the metallic substrate has diffused into
coating layer, resulting in further enhancement of the
adhesion.
3.9. Surface Roughness
Ten surface roughness measurements were taken on the
surface of the specimens and the results in Figure 9 in-
dicate that the surface roughness ranges from 13 µm to
Figure 7. XRD spectra of the anodic coatings by using electrolyte (1), [temp . (30 - 40)oC, deposition time 9 min and current
density 31 mA/cm2].
Table 4 Phases present in coating layer using the different electrolytes.
Compound name Chem ical formu la Score Percentage (wt%)
Electrolyte (1)

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
70
Magnesium Mg 31 0.25
Periclase MgO 68 0.55
Sili con Oxide SiO2 25 0.20
Electrolyte (2)
Magnesium Mg 53 0.3
Periclase MgO 75 0.42
Ceramic Ox ide Or (Boric oxide) B2O3 51 0.28
Electrolyte (3)
Magnesium Mg 52 0.28
Sili con Oxide SiO2 47 0.25
Periclase MgO 69 0.37
Forsterite Mg2SiO4 16 0.10
Table 5. EDX analys is of anodic c oat layer (w t%).
Zone No. O% Mg% Al% Si%
Zone I (close to the Mg) 27.7 33.4 0.9 37.8
Zone I I (central region ) 29.2 27.6 0.8 42.2
Zone III (close to surface) 31.1 24.3 0.7 43.7
*The EDX analysis of the anodic coat layer by using electrolyte ()3 after th e pretreatment, deposition time 9 min and current density 31 mA/cm2 at temp. (30 -
40)˚C.
(a)
(b)
Figure 8. (a) Cross section morphology (b) sketch of a typical
cross section, for anodic coating of anodic coating film on
magnesium alloy AZ91D at 31 mA/cm2 current density, 9
minutes depo sition time and temperature (30 - 40)˚C.
Table 6. Crystalline size for the coat layers for the three
electrolyt es.
Type of bath Crystal size (nm)
Electrolyte (1) 5.1
Electrolyte (2) 3.95
Electrolyte (3) 4.12
24 µm. It increases by increasing the current density and
is lower for electro lyte (2). I n addition, Figure 10 shows
that the surface roughness increases by increasing the
coating thickness. For electrolyte (2), the surface rough-
ness was found to be constant for curr ent d ens ity r angi n g
fr o m 2 4 mA/cm2 to 31 mA/cm2, which corresponds to an
almost constant coat thickness, as indicated in Fig ure 3.
The surface roughness is partly related to the non-
homogeneity of coat layer and the formation of pores and
cracks on the anodic film layers. These surface defects

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
71
were greater in case of electrolyte (1) followed by (3)
and (2).
Figure 9. Effect of change of current density on surface
roughness of coating layers by using three electrolytes at
temperature (30 - 40)˚C and constant time 9 minutes.
Figure 10. Relation between coating thickness and surface
roughness for anodizing process by using three electrolytes,
pre-treatment procedure 9 minute deposition time, and cur-
rent density (16 to 31) Am/cm2.
3.10. Mic rohardness
The results indicate that the microhardness increases with
increasing the current density, Figure 11, and coat
thickness, Fig ure 12 reaching value of 570 VHN for
electrolyte (3) with 28 µm thickness. This is expected as
the coat phases include MgO and SiO2 hard phases. Ta-
ble 5 indicates that the Si increases towards the coat sur-
face which could results in higher concentration of the
SiO2 hard phase. In general, the hardness of the coat
phases is higher than that of the magnesium substrate
(VHN = 360 HV).
3.11. Corrosion Tests
Figure 13 shows potentiodynamic curves obtained for
AZ91 magnesium alloys before and after anodizing pro-
cesses by using the three electrolytes. Potentiodynamic
curves for the anodized specimens are shifted in the
noble direc tion indi cating a higher corrosion resi sta nce.
The electrolytes can be ranked to give the best anti-
corrosion properties as electrolyte (3) followed by (2),
Figure 11. Effect of change current density in microhardness
of coating layers by using three electrolytes at temperature
(30 - 40)˚C and time at 9 minute.
Figure 12. Relation between coating thickness and micro-
hardness of coating layers for anodizing process by using
three electrolytes.
then by (1). The results of linear polarization experiments
summarized in Table 7 shows that the corrosion resis-
tance of AZ91 magnesium alloys is enhanced signifi-
cantly by using the three electrolytes in anodizing
processes. T his is marked by the increase of Rp, decrease
in Icorr and shift of Ecorr in the noble direction (more
positive values). The corrosion rate drops from 57.48
mpy to 3.39, 2.64 and 1.70 mpy using electrolytes (1),
(2) and (3) reaching excellent efficiency of 94%, 95%
and 97% respectively.

AZ91 Magnesium Alloys: Anodizing of Using Environmental Friendly Electrolytes
72
Figure 13. Potentiodynamic polarization curves for the
anodized specimens by using three-electrolyte to gather
with the AZ91 Mg Substrate (Blank).
4. Conclusions
1) The anodizing process of AZ91 based on environ-
mental friendly electrolytes was successful to form a
smooth anodic film, with high corrosion resistance and
excellent bonding strength to substrate. The solutions
used were sodium silicate for electrolyte (1), sodium hy-
droxide - boric acid - borax for electrolyte (2), sodium
silicate-potassium hydroxide- odium carbonate-sodium
tetra bora te for e le c trolyte (3),
2) The anodized layer included the MgO phase as the
dominating phase followed by smaller amounts of SiO2,
MgO, B2O3 and Mg2SiO4 indicating that the substrate
and the electrolyte both contribute in forming the coat
layer .
3) High i mprove ment in corr osion is due to the forma-
tion of anodic film with layer thickness between 30 mi-
cron (electrolyte (2) and (3)) and 50 micron (electrolyte
(1)) with excellent adhesion to the magnesium substrate.
The higher improvement in corrosion resistance is asso-
ciated with less microcracks and micropores in the coat
which in all cases do not reach the Mg substrate.
4) The best anticorrosion performance was obtained
for electrolyte (3) where the corrosion resistance effi-
cienc y 97% was reached, while it was 94% and 95% for
Table 7. Result s of linear polarization experiments.
Specimen for Ecorr, V Rp, Ω.cm2 Icorr, µA/cm2 Corrosion Rat e, mpy Efficiency
AZ91 Mg substrate (Blank) –1.585 4.168 E+2 5.027×10-5 57.481 -----------
Electrolyte (1) –1.427 1.863E+3 4.171E-6 3.39 94.10%
Electrolyte (2) –1.394 2.71E+3 3.19 3 E-6 2.64 95.40%
Electrolyte (3) –1.371 3.67E+2 2.09 3 E-6 1.70 97.04%
*Efficiency = ( Corrosion Rate for Mg blank - Cor rosion Rate using Electrolyte )/C orrosion Rat e for Mg blank.
electrolyte (1) and (2) respectively.
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