effect of in- addition and structural transformation …effect of in- addition and structural...
TRANSCRIPT
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 5
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
Effect of In- Addition and Structural Transformation
on the Physical Behavior of Bi- 44.5 wt% Pb Rapidly
Quenched Ribbons from Melt Mustafa Kamal, Abu-Bakr El-Bediwi, and JAMAL KHALIL MAJEED*
Metal Physics Lab. Physics Department, Faculty of Science –Mansoura University, Egypt.
*On leave, M.Sc. student, Iraq
[email protected], [email protected], [email protected]
Abstract-- This paper presents experimental results and
theoretical considerations to evaluate the effect of indium
additions on the solidification behavior of Bismuth-Lead eutectic
alloys used as coolant in some nuclear reactors. Structural
modifications, electrical, thermal and mechanical properties
improvements on chill-block melt spinning of melt-quenched
ribbons of the bismuth-lead eutectic containing indium are
described and discussed.
Index Term-- Melt-spin technique, X-ray diffraction, Lattice
distortions, Resistivity, Elastic moduli, specific heat, Melting
temperature and internal friction.
1- INTRODUCTION AND BACKGROUND INFORMATION
The Bi-Pb eutectic system has attracted the attention of many
investigators because it provides a good model for studying the
structure and properties of metallic behavior using chill-Block
melt spinning technique [1]. The most important component of
fusible alloys is Bismuth. Bismuth alloys were known to have
very low- melting temperatures and low physical strength.
Bismuth expands on freezing namely 3.3% of volume when
changing from molten to solid form. When bismuth is alloyed
with other metals such as lead and indium, this expansion is
modified according to the relative percentage of Bismuth and
other components present. Lead-bismuth eutectic is eutectic
alloy of bismuth (55.5wt %) and lead (44.5wt %) [2], as
indicated in figure (1) used as a coolant in some nuclear
reactors as spallation target in a future accelerator driven
system, and is a proposed coolant for lead –cooled fast reactors
[3, 4]. It has a melting point of 123.5C˚.Lead-bismuth alloys
with between 30% and 75% bismuth all have melting points
below 200C˚. Alloy with between 48% and 63% bismuth have
melting points below 150 C˚, while lead expands slightly on
melting and bismuth contracts slightly on melting. Lead-
bismuth eutectic has negligible change in volume on melting.
Glasbrenner et al [5] studied the expansion of solidified lead
bismuth eutectic. Experiments on the volumetric expansion of
lead bismuth eutectic were performed by variation of cooling
rates, holding times and different starting temperature of the
melt. Claude Borromee-Gautier et al assumed that new phase
found include a complex phase Pb-Bi phase. The terminal
Fig. 1.
solubilities, especially those of Pb in Bi were strongly an
appreciable decrease of the rhombohedral angle [6].Singh al [7]
reported that is the Bi-Pb binary system, two metastable phase
that are called X and Y were reported to form by the very rapid
quenching method such as splat cooling of sample on a metal
surface kept at -190C˚ by liquid nitrogen .Seung wook Yoon and
H. Yuck Mo Lee [8] studied the Bi-Pb system and assumed
thermodynamic parameters of all the stable phase in Bi-Pb binary
system. Mustafa Kamal and Abu-Baker-El-Bediwi [9] showed
that the metastable X (Pb-Bi) phase in melt spun Pb50Sn10Bi40 or
Pb50Bi50 ribbons have a lower strength and lower conductivity
than any other composition having either a Pb-rich solid solution
of a Bi-rich solid solution, and Mustafa Kamal et al ., revealed
from x-ray diffraction patterns[10] that Bi-50%Pb metal
irradiated or non-irradiated rapidly solidified from melt using
melt-spinning technique is composed of Pb7Bi3 and Bi-phase,
each of both has the same orientation of growth. In this work, the
Pb-Bi-In system has chosen essentially due to its technological
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 6
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
importance. Therefore, the present study focused on structural
characterization of rapidly Pb-Bi using the rapid quenching of
metallic melts (melt-spinning technique). So the procedure
studied in this paper, namely, the solidification process of
melted metal. Its advantages are as follows: For the synthesis of
lead-bismuth eutectic base alloys nanowires [11, 12].-
Decreased in grain size, - Extension of solid solubility limit, -
Creation of metastable crystalline phases, and -Increased in
chemical homogeneity. A critical assessment of the lead-
bismuth eutectic technology for Hyperion reactor design is well
reported by Zhang et al [13] based on and analyzed on currently
available knowledge.
2- EXPERIMENTAL PROCEDURE
The apparatus used to prepare the quenched ribbons from melt
is based on the design by Kamal et al. [14]. The alloys under
investigation were prepared by a single-roller type melt-
spinning as listed in a Table (І).
Table І
quenched ribbons Density (g/cm3)
Bi55.5-Pb44.5 9.4
Bi55-Pb44.5-In0.5 10.42
Bi54.5-Pb44.5-In1 10.16
Bi52.5- Pb44.5- In3 9.42
Bi50.5-Pb44.5-In5 9.22
The surface speed of aluminum wheel was about 30.4 m.s-1
to
obtain well shaped ribbons. Melt-spun ribbons (thickness 50-
120 μm, width about 3-5 mm, cooling rate 106 K/sec) were
prepared from pure bismuth, lead, and indium. Extrusion was
performed at about 772 Kelvin. The procedure in the
preparation of the melt spun ribbons was reported previously
[15]. The structure of the quenched ribbons was investigated by
X-ray diffraction using Cu kα radiation at room temperature. In
situ electrical resistivity measurements have been carried out
using the double-bridge method. The heating rate of furnace
used maintained at about 3.13K.min-1
. The temperature
measurements were performed using a Beckman industrial TP
850 digital thermometer. The elastic moduli, the internal
friction, and the thermal diffusivity of melt-spun ribbons were
examined in air atmosphere with a modified dynamic resonance
method. The hardness of the quenched ribbons was measured
using a digital Vickers micro hardness tester (model FM-7).
Applying a load of 10 gf for 5sec via a Vickers diamond
pyramid. More than fifteen indents were made on each sample to
bring out any hardness variation due to presence of more phases,
with one phase soft and ductile and another phase considerably
harder, so that the average value Hv would be obtained [16].
3- RESULT AND DISCUSSIONS
A. Structure analysis
In the binary phase diagram, the eutectic phase of Pb-Bi
quenched ribbons from melt is consisted of the Bi-phase rich
rhomobohedral solid solution, Pb-phase rich cubic solid solution
and the hexagonal close packed Pb7Bi3 phase. In figure (2) the X-
ray diffraction pattern proves that the crystal phase structure of
the melt-spun ribbon and the X-ray diffraction spectrum
identified of the melt-spun ribbons in agreement with the
theoretical value [12]. Because there were three phases in the
present quenched ribbons (bismuth, lead, and Pb7Bi3 phases),
some peaks were very close to each other.
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 7
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
Fig. (2, a, b, c, d, e)
The crystal structure of the melt-spun Pb7Bi3 phase has been
identified by Claude Borromee-Gautier et al [6], and M. Kamal
et al [17]; it was suggested to be hexagonal close-packed
structure cell. From the structural data, it may be shown that the
ratio of c to a in a hexagonal closed packed structure for Pb7Bi3
formed of sphere in contact is less than √3 figure (3).
Fig. 3.
Figure (3) the hexagonal close-packed structure of Pb7Bi3 so the
direction of motion of individual atoms during shear in the
direction. The effect of indium additions slightly raising the
valence electron concentration was investigated. Table (II)
summarizes the data of the observed axial ratios c/a and the
average valence electron concentration e/a of the Bi-phase in
quenched ribbons Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5, Bi 54.5-Pb44.5-In1,
Bi52.5-Pb44.5-In3, and Bi50.5-Pb44.5-In5. Thus, indium addition
produced the highest c/a ratio measured; this leads to a valence
electron concentration of 4.22 e/a, but the c/a value are slightly
higher. This may be due to a large coefficient of thermal
expansion for c than for a, as the equilibrium axial ratios were
determined at 27C˚.
Table II
quenched ribbons Bi-phase
c / a e/a
Bi55.5-pb44.5 2.61 4.55
Bi55-pb44.5-In0.5 2.61 4.51
Bi54.5-pb44.5-In1 2.62 4.48
Bi52.5- pb44.5- In3 2.66 4.35
Bi50.5-pb44.5-In5 2.65 4.22
B. Determination of number of atoms in unit cell
To find the number of atoms in unit cell, we use the fact that the
volume of the unit cell of Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5, Bi
54.5-Pb44.5-In1, Bi52.5- Pb44.5- In3, and Bi50.5-Pb44.5-In5 rapidly
quenched ribbons form melt, calculated from the lattice
parameters [18], multiplied by the measured density of the
substance equals the weight of all the atoms in the cell. When
determined in this way, the number of atoms of per cell is always
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 8
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
an integer, within experimental error, except for a very
substance which has defect structures. So in our melt-spun
ribbons of Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5, Bi 54.5-Pb44.5-In1,
Bi52.5-Pb44.5-In3, and Bi50.5-Pb44.5-In5 as indicated in Table (III).
Table III
quenched ribbons
Number of atom per
unit cell
Bi55.5-Pb44.5 1.13
Bi55-Pb44.5-In0.5 1.92
Bi54.5-Pb44.5-In1 1.89
Bi52.5- Pb44.5- In3 1.76
Bi50.5-Pb44.5-In5 1.73
Atoms are simply missing from a certain fraction of those
lattice sites which they would be expected to occupy, and the
result is a non-integral number of atoms per Bi-, Pb-, and the
Pb7 Bi3 phases in the Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5, Bi 54.5-Pb44.5-
In1, Bi52.5-Pb44.5-In3, and Bi50.5-Pb44.5-In5 melt spun ribbons are
well known example, in our studies [10]. As a result of this
restraint by its neighbors, a plastically deformed grain in a solid
aggregate usually has regions of its lattice left
in a state of uniform tension or compression. The rapidly
quenched ribbons from melt is then said to contain residual
stress or internal stress. Stresses of this kind also called micro-
stress since they vary from one grain to another or from one
part of a grain to another part, on a microscopic scale. The line
breadths or the interpretation of line broadening may be
attributed to simultaneous small particle size and strain
broadening, the later predominating particularly at higher Bragg
angles. Hence it is shown that the observed effects are produced
by structural fault. Change is integral intensity have been
discussed by Hall and Williamson [19], and it is the object of
this section to interpret and discuss the lattice disorder in the
quenched ribbons. Line width B, both at half maximum
(FWHM) intensity and integral, were used in Williamson-Hall
plot [20] as illustrated in figure (4), To drive information about
the crystallite size Deff and local lattice distortion < Σ2
> in all
phases.
B = (1/Deff) +5 < Σ2 >
½ sinθ /λ …….. (1)
The 1/Deff and 5 < Σ2 >
½ parameters are given in Tables (IV).
Fig. (4, a, b, c, d, e)
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 9
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 10
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
Tables IV
structural data for phases present in Bi-Pb-In as quenched ribbons.
quenched ribbons Bi Pb Pb7Bi3 5 < Σ
2 >
½
a ( ) C ( ) c / a a ( ) a ( ) C ( ) c / a Bi Pb Pb7Bi3
Bi55.5+Pb44.5 4.545 11.91 2.61 4.9842 3.507 5.776 1.65 0.0015 0.0009 0.001
Bi55-Pb44.5-In0.5 4.54 11.7 2.613 4.9569 3.51 5.755 1.64 0.0013 0.001 0.0011
Bi54.5-Pb44.5-In1 4.533 11.91 2.626 4.9697 3.506 5.804 1.655 0.0014 0.0011 0.0019
Bi52.5- Pb44.5-In3 4.522 12.03 2.661 5.0188 3.497 5.793 1.656 0.0014 0.0013 0.0013
Bi50.5-Pb44.5-In5 4.524 12 2.655 5.2314 3.494 5.796 1.659 0.0011 0.002 0.002
For Bi-phase as well as for Pb-phase and Pb7Bi3-phase 1/Deff
is not fit to be measured, concluding to a good crystallization
state. Lattice distortion for Bi-phase, Pb-phase, and Pb7Bi3-
phase are slightly the same. This supports the disordered
formation for all composition supporting the stacking faults
segregation origin of the Pb-phase Lattice, when it is also
known in the lesser amounts.
C. Resistivity and Thermal conductivity
The influence of the indium content on the room temperature
resistivity of the quenched ribbons from melt Bi55.5-x Pb44.5 Inx
(0≤ x ≤ 5) is demonstrated in figure (5). The resistivity
decreases significantly with increasing Indium content up
to1wt% In then increased and attains the highest value of about
115.8x10-8 Ω.m. The resistivities here are measured around
room temperature so that the total resistivity pronounced
minima at composition of 0.5%In.This correspond to the
formation of ordered alloys. Moreover, by addition of In to Bi-
Pb eutectic causes a pronounced increase of the electrical
resistivity [21].
Fig. 5.
The value of electrical conductivity σ according to the quantum
theory is σ = ……. (2).
The value of the collision time of an electron at Fermi surface, τʄ
may be computed directly from equation (2) provided the
conductivity is known [9]. Table (V) gives a list of the electrical
conductivities and other transport parameters of Bi55.5-x Pb44.5 Inx
rapidly quenched ribbons from the melt. Values of the equivalent
Fermi temperature, Fermi velocities Fv and Fermi wave vector,
KF, are also given. Another important aspect of the electrical
conduction process in general is that it enables us to compute the
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 11
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
density of states at the Fermi surface FS, g (EF) within the
framework of band theory [22], which leads finally to the
following expression for the electrical conductivity:
σ = e2 vF
2 ƬF g(EF) ……… (3).
It is observed that the electrical conductivity depends on the
density of states at the Fermi surface FS, g (EF). Figure (6) and
Table (VI) shows the density of states for rapidly quenched
ribbons of Bi55.5-x Pb44.5 Inx, indicating the position of the Fermi
level for rapidly quenched ribbons.
Table VI
quenched ribbons
Fermi energy
(EF)
(ev)
g(EF)
1016
Bi55.5-Pb44.5 0.6751 3.200
Bi55-Pb44.5-In0.5 0.9255 1.240
Bi54.5-Pb44.5-In1 0.9135 3.700
Bi52.5- Pb44.5- In3 0.8143 3.500
Bi50.5-Pb44.5-In5 0.7689 3.400
Tables V
electrical conductivity (σ), electron density (n), Fermi wave vector (KF), Femi energy (EF), Femi velocity (VF),
electron mobility (μ), electron mean free path (l) and collision time ( τʄ ).
quenched ribbons
Electrical
conductivity
(σ)
(W-1
.m-1
)
108
electron
density(n)
1028
Fermi
wave
vector
( m-1
)
109
Fermi
energy
(EF)
(T)ev
Fermi
velocity(Vf)
( m.s-1
)
105
Electron
mobility
µ
m2.V
-1.S
-1
10-3
collision
time Ƭ
(sec )
10-14
mean free
path l
m
10-9
Bi55.5-Pb44.5 0.007 0.25 4.21 0.675 4.87 1.760 1.001 4.9
Bi55-Pb44.5-In0.5 0.011 0.40 4.9 0.925 5.70 1.760 1.001 5.7
Bi54.5-Pb44.5-In1 0.011 0.39 4.89 0.913 5.67 1.760 1.001 5.7
Bi52.5-Pb44.5-In3 0.009 0.33 4.62 0.814 5.35 1.760 1.001 5.4
Bi50.5-Pb44.5-In5 0.0086 0.31 4.49 0.768 5.20 1.760 1.001 5.2
Fig. 6. position of the Fermi energy level in Bi55.5-x Pb44.5 Inx rapidly
quenched ribbons
The thermal conductivity changes in approximately the same
way as was developed for the electrical conductivity. There is a
definite relationship between the electrical and thermal
conductivities of the alloy; although the Weidman-Franz ratio
does not hold [23].It is found that the values of the thermal
conductivity of the quenched ribbons from melt of Bi55.5-x Pb44.5
Inx is summarized in Table (VII).
Table VII
It is indicated that the thermal conductivity slightly increased by
addition of Indium content up to 8 W/m.K and then decreased as
shown in Table (VII).
D. Thermodynamic functions from DSC
Zu et al [24] suggested that structural changes take place to
some extent in molten alloys as a function of temperature, which
have been confirmed by the corresponding calorific peak in a
differential scanning calorimeter. So in this section, It is noted
that further work is needed to probe the concrete change of
quenched ribbons
Thermal
conductivity (K)
(W.m-1.k-1)
Bi55.5-Pb44.5 5.243
Bi55-Pb44.5-In0.5 8.415
Bi54.5-Pb44.5-In1 8.254
Bi52.5- Pb44.5- In3 6.946
Bi50.5-Pb44.5-In5 6.372
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 12
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
structures with the help of a differential scanning calorimeter.
Specimens approximately 7 mg in mass were cut from the melt-
spun ribbons and were submitted to heating from 323.15 K to
1073.2 K at rates of 10 K.min-1
in a SDTQ600 differential
scanning calorimeter DSC. A typical output is depicted in
Figure (7). The results of the melting temperature, enthalpy,
entropy change and the average specific heat as a function of
indium content are tabulated in Table (VIII).On the basis of
thermodynamic functions from DSC results Bi55.5-Pb44.5, Bi55-
Pb44.5-In0.5, Bi 54.5-Pb44.5-In1, Bi52.5-Pb44.5-In3, and Bi50.5-Pb44.5-In5
quenched ribbons from melt exhibit notably different behaviors.
On the basis of these results we claim that, by increasing the
indium from 0.5 to 5wt% the melting temperature decreases as
indicated in Table (VIII). But also the average specific heat was
increased.
Table VIII
quenched ribbons
melting
Temp1
melting
Temp2 T1 T2 Enthalpy Specific heat
entropy
change
K K K K
j / kg
104
j / Kg.K j / Kg.K
Bi55.5-pb44.5 398.37 400.73 398.2 423.2 1.435 574.00 104.7
Bi55-pb44.5-In0.5 394.77 396.59 413.2 441.2 1.316 470.00 85.7
Bi54.5-pb44.5-In1 364.79 367.28 333.2 364.2 12.59 519.66 423.2
Bi52.5- pb44.5- In3 359.175 363.46 338.2 361.2 8.775 1051.50 538.7
Bi50.5-pb44.5-In5 352.185 358.725 337.2 361.2 1.015 744.73 404.11
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 13
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
Fig. (7, a, b, c, d, e)
E. Elastic Moduli of Quenched Ribbons from Melt
In this section will be concerned with the problem of
determining the elastic moduli of Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5,
Bi 54.5-Pb44.5-In1, Bi52.5- Pb44.5- In3, and Bi50.5-Pb44.5-In5, melt-
spun ribbons from their mechanical resonance frequencies. The
dynamic resonance method has a definite advantage over static
method of measuring elastic moduli because the low-level
alternating stress does not inflate anelastic processes such as
creep or elastic hysteresis [25]. The elastic moduli obtained with
the resonance method give information about elastic
compliances along the long axis of the melt-spun ribbons. In an
elastically isotropic body such as a well prepared polycrystalline
quenched ribbons, the elastic moduli are identical in any
direction. And finally the young modulus for Bi55.5-Pb44.5, Bi55-
Pb44.5-In0.5, Bi 54.5-Pb44.5-In1, Bi52.5- Pb44.5- In3, and Bi50.5-Pb44.5-
In5 quenched ribbons can be calculated using Equation (4)
Measured values are listed in Table (IX) for young modulus E,
shear modulus G, bulk modulus B, and Poisson’s ratio √. The
data indicate that are nearly the same up to the 1wt% In. Thus,
the Young’s modulus is not sensitive to composition in this
limit. But is relatively sensitive to composition by increasing
indium content. The effect of increasing indium content on
elastic stiffness is further indicated in Table (IX) which shows
that the fractional change averages 57% for elastic stiffness.
Note that the incremental decrease upon indium additions is
about the same for all elastic modulus.
Table IX
quenched ribbons
Young
modulus
GPa
Shear
modulus
GPa
Bulk
modulus
GPa
Poisson
ratio
Bi55.5+Pb44.5 24.3 8.80 33.42 0.3789
Bi55-Pb44.5-In0.5 27.5 9.98 38.10 0.37952
Bi54.5-Pb44.5-In1 24.3 8.82 33.84 0.3801
Bi52.5- Pb44.5- In3 16.2 5.87 22.99 0.3824
Bi50.5-Pb44.5-In5 18.5 6.68 26.75 0.3847
F. Internal friction Q-1
Internal friction measurements have been quite fruitful for
learning the behavior of rapidly quenched ribbons from melt. It
is one of the important characteristics which are indirectly
related to their elastic properties. The free vibration is based on
the measurement of the decay in amplitude of vibrations during
free vibration. The internal friction is obtained by [26].
Q-1
= 0.5773 ……… (5)
Where f is a critical frequency of quenched ribbons. From the
measurement of the internal friction, Q-1
it is found that the
quenched ribbons of Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5, Bi 54.5-Pb44.5-
In1, Bi52.5- Pb44.5- In3, and Bi50.5-Pb44.5-In5 have slightly large
acoustic loss, as listed in Table(X).
Table X
internal friction of the quenched ribbons
quenched ribbons internal friction
Bi55.5-Pb44.5 0.065
Bi55-Pb44.5-In0.5 0.174
Bi54.5-Pb44.5-In1 0.401
Bi52.5- Pb44.5- In3 0.397
Bi50.5-Pb44.5-In5 0.386
From Table (IX) it can be seen the internal friction Q-1
is more
sensitive than the elastic moduli to the phase changes occurring
in the quenched ribbons [27]. At first increases and shows a
maximum at 1wt% In. From zero to 1wt% In it shows an
increase. This sudden change in internal friction can be
attributed to the phase changes. It is also confirmed that internal
friction measurement has been quite for learning about the small
change in the mechanical state of a material.
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 14
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
G. Thermal diffusivity
Using dynamic resonance method for measuring the thermal
diffusivity of quenched ribbons of Bi55.5-Pb44.5, Bi55-Pb44.5-In0.5,
Bi 54.5-Pb44.5-In1, Bi52.5- Pb44.5- In3, and Bi50.5-Pb44.5-In5. From the
frequency f, at which the peak damping occurs, the thermal
diffusivity D can be obtained directly from the relation
……… (6)
Where t is the thickness of quenched ribbons. For Bi-44.5%Pb-
0.5%In and Bi-44.5%Pb-1%In ,as indicated in Table(XI), the
thermal diffusivity are smaller than for the others compositions
of the quenched ribbons by approximately a factor 16 or 8. It is
seen that quenched ribbons of Bi-44.5%Pb-0.5%In and Bi-
44.5%Pb-1%In have smaller thermal diffusivity than the other
compositions, we assume that this fact is caused by slightly
lower aggregation of Pb7Bi3 particles. But in the case of Bi-
44.5%Pb-0.5%In and Bi-44.5%Pb-5%In, the aggregates of
Pb7Bi3 and Bi could improve a heat transport in the quenched
ribbons and improve thermal diffusivity.
Table XI
quenched ribbons
Thermal
diffusivity
m2 /s
10-8
Bi55.5-Pb44.5 1.23
Bi55-Pb44.5-In0.5 0.37
Bi54.5-Pb44.5-In1 0.83
Bi52.5- Pb44.5- In3 3.03
Bi50.5-Pb44.5-In5 6.09
H. Micro-hardness investigations:
The present part is concerned with micro-hardness measurement
carried on rapidly quenched ribbons of Bi55.5- x Pb44.5Inx (0≤ x
≤5wt %) from the melt are summarized in Table (XII).
Table XII
quenched ribbons HV ( M P)
Bi55.5-Pb44.5 44.13
Bi55-Pb44.5-In0.5 54.92
Bi54.5-Pb44.5-In1 70.12
Bi52.5- Pb44.5- In3 124.05
Bi50.5-Pb44.5-In5 104.44
The Vickers hardness value reported is an average value of ten
indentions made on each melt-spun ribbons using a10 gf. Load
for 5 sec. The micro-hardness value of BiPbIn ribbons material
increased with increasing indium content as a result of both
dispersion strengthening and solid solution strengthening.
Variations in properties with indium content are due to the
presence of Bi3 Pb7 and Bi- precipitates as well as to variations
in cell and grain sizes. It is indicated that as the indium content
increases there is a trend of gradual increases in hardness for
each quenched ribbon composition. It is also observed that pure
eutectic Bi-Pb quenched ribbon exhibits the lowest hardness. In
the concentration range of 0.5wt% to 3wt% In the hardness
values have shown a linear increase. The sudden change in
hardness value can be suggested to the phase changes occurring
in the system.
4- CONCLUSIONS
The following conclusions can be made from our results as
follows. –Effect of In-addition and structural transformation on
the physical behavior of Bi-44.5%Pb rapidly quenched ribbons
from melt showed desirable properties.- The Bi-Pb-In quenched
ribbons showed a high potential as coolant in nuclear systems
only with further modification of compositions for improvement
of thermal behavior to enhance the safety measures.-we except
that the present set of material property such as structural,
electrical, mechanical and thermal properties of the melt
quenched ribbons of Bi-Pb-In could utilized as standard data
basis for use in safety analysis. –The quantitative conformance
of the experimental and with the calculated results is sensitive to
the material properties. Also, the near future studies in main
areas of the technology are recommended for meeting the design
requirements. The present work shows that rapid quenching
from melt leads to the formation of Pb7Bi3 intermediate phases
and to enhancement the material properties of the quenched
ribbons from melt. Finally all the investigated melt-spun ribbons
show three phases appearance, the Bi-phases, Pb- phases, and
the intermediate phases (Pb7 Bi3), as evidenced by X-ray
diffraction analysis.
REFERENCES
[1] Mustafa Kamal and Usama S. Mohammad, A Review: Chill-Block
Melt-spin Technique, Theories & Applications. eISBN: 978-1-
60805-151-9(2012), Bentham e Books, Bentham science Publishers.
[2] V.S. Chirkin. The thermophysical properties for nuclear Engineering
Moscow Atomizdat 484 (1968).
[3] C. Rubbia, J. A. Rubio, S. Buono, F. Carmianti, N. Fietier , J. Galvez
,C. Geles, Y. Kadi, R. Klapish, Mandrillioni, J.P. Revol, C. Roche,
International Journal of Engineering & Technology IJET-IJENS Vol:14 No:02 15
141702-6565-IJET-IJENS © April 2014 IJENS I J E N S
European Organization for Nuclear Research, CERN report AT/ 95-
44(ET). (1995).
[4] H.H. Knebel, X, chang, C.H. Lefhalm, G.Müller, G. Schumacher, J.
Konys, H. Glasbrenner, Nucl. Eng. Design 202(2000)279.
[5] H. Glasbrenner, F. Gröschel, H.Grimmer,J.potorski, M.Rohde,
Journal of nuclear Materials 343(2005),341-348
[6] Claude Borromee-Gautier, Bill C. Giessen, and Nicholas J. Grant,
The Journal of chemical physics Vol.48,No.5 March (1968),1905-
1911.
[7] H.P. singh,C. suryanarayana, S. Misra and T.R. Anantharaman, Z.
Matalkde, 62,52(1971).
[8] Seung Wook Yoon and H. Yuck Mo Lee, calphad, vol.22, No.2,
PP.167-178, (1998) pergamon.
[9] Mustafa Kamal and Abu-Baker-El-Bediwi, Journal of Materials
science: Material in Electronics 11(2000)519- 523.
[10] Mustafa Kamal and Abu-Baker-El-Bediwi, Tamer Dawod and
Waqlan, International Journal of Engineering and Technology IJET-
IJENS vol: 19, No: 05 October (2012) IJENS, 34-42.
[11] C. G. Kuo, Y.Y. Hsu, M.K.Wu, and C. G. Chao, A ppl. phys, A80,
1501-1504 (2005).
[12] Chin Guo Kuo- Chuen-Guang Chao Int. J. Adv. Manuf Technol,
Vol.32, no-5, pp 468-472,(2005).
[13] J.Zhang, R.J. Kapernick, P.R. Mc.Cluse, T.J. Trapp, Journal of
Nuclear Materials. 441(2013)644-649.
[14] M. Kamal, J. C. Pieri, R. Jouty, Memoires et Etudes scietifiques
Revue de Metallurgie-Mars1983 PP: 143-148.
[15] Rizk Mustafa Shalaby and Mustafa Kamal, International Journal of physics and Research (IJPR), vol.3,Issue, Dec.(2013),51-60.
[16] Mustafa Kamal and Abu-Baker-El-Bediwi, Radiation, Eff. Defect
solids 174(1999)211. [17] Mustafa Kamal and Abu-Baker-El-Bediwi and Mohamed Bashir
Karman, Journal of Materials science: Material in Electronics
9(1998) 425-428. [18] B. D. Cullity, Elements of X-Ray Diffraction, Addison-Wesley
Publication Company, Inc, U.S.A., London, England, (1959) 316.
[19] W. H. Hall and G.K. Williamson, Proc. Phys. Soc 64B (1951) 937, 946.
[20] G.K. Williamson and W. H. Hall, Acta Metall. 1, 22-31(1953).
[21] Mustafa Kamal, shelabia Badr, and Nermin Ali Abdelhakim, International Journal of Engineering and Technology IJENS-IJET-
vol: 14, No: 01 Feb(2014), PP119-129.
[22] M.A. Omar, Elementary solid state physics; principles and Application, Addison-Wesley publishing company, 1975 PP: 235-
238.
[23] G. E. Doan, The principles of physical Metallurgy, McGraw Hill Book Company, INC. (1953) PP: 202-231.
[24] F.Q. Zu, Z. G. Zhu, B. Zhang, Y. Feng and J.P. Shui, J. phys.
Condens. Matter 13 (2001) 11435-11442. [25] E. Schreiber, O. L. Anderson, and N. Soga, Elastic Constants and
their Measurements, McGraw-Hill Book Company (1973) PP: 82-
125. [26] G. Roebbon, B. Bollen, A. Brebels, J. Van Humbeeck and O. Van der
Biest, Rev. Sci. Instrum. 68(12), December (1997), Americam Institute of physics PP: 4511-4515.
[27] P.A. Varkey and A.R.K.L. Padmini, Pramana, Vol. 11, No6,
December 1978, PP 717-724.