effect of in- addition and structural transformation …effect of in- addition and structural...

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

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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.



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



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)



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



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



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



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.



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.

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