The study investigates the effect of titanium oxide (TiO2) nanoparticles on the structure and properties of tin-antimony-lead and tin-aluminum alloys, revealing that TiO2 enhances the elastic modulus, Vickers hardness, and thermal diffusivity of these alloys. Results indicate that the addition of TiO2 improves bearing properties, with the sn85.5sb10pb3(tio2)1.5 alloy showing the best characteristics for automotive applications and sn78.5al20(tio2)1.5 for marine uses. The research employs various analytical methods to assess the mechanical and thermal properties impacted by the TiO2 addition.

1. International Journal of Science and Engineering Applications
Volume 4 Issue 2, 2015, ISSN-2319-7560 (Online)
www.ijsea.com 46
Effect of Titanium Oxide on Structure, Bearing Properties of
Tin-Antimony-Lead and Tin-Aluminum Alloys
Abu Bakr El- Bediwi
Metal Physics Lab., Physics
Department, Faculty of Science,
Mansoura University
Mansoura, Egypt
Abbas Al- Bawee
Faculty of engineering, University of
Diayala
Diayala, Iraq
Mustafa Kamal
Metal Physics Lab., Physics
Department, Faculty of Science,
Mansoura University
Mansoura, Egypt
Abstract: Effect of adding titanium oxide nanoparticles (TiO2) on structure, elastic moduli, Vickers hardness, internal friction, electrical
resistivity and thermal properties of tin-antimony-lead and tin-aluminum bearing alloys have been investigated. Elastic modulus, Vickers
hardness and thermal diffusivity of Sn87Sb10Pb3 and Sn80Al20 alloys increased after adding TiO2 nanoparticles. Internal friction, thermal
conductivity and specific heat of Sn87Sb10Pb3 and Sn80Al20 alloys varied after adding TiO2 nanoparticles. Adding titanium oxide nanoparticles
improved bearing properties, such as strengthens and internal friction of Sn87Sb10Pb3 and Sn80Al20 alloys. The Sn85.5Sb10Pb3(TiO2)1.5 alloy has
best properties for automotive industry. Also Sn78.5Al20(TiO2)1.5 alloy has best properties for marine applications.
Key words: titanium oxide, internal friction, thermal properties, structure, hardness, resistivity, bearing alloys
Introduction
Bearings are used to prevent friction between parts during
relative movement. In machinery they fall into two primary
categories: anti-friction or rolling element bearings and
hydrodynamic journal bearings. Today, the term Babbitt covers a
collection of “white metal” alloys consisting generally of a tin or lead
base accompanied by antimony and copper. Babbitt metal is used as
the lining for bearing shells of cast iron, steel and bronze. Fry
manufactures two basic types of babbitt, high-tin alloys and high-lead
alloys. Both are relatively low melting materials consisting of hard
compound in a soft matrix. Al–Sn alloys have a very long history
(Forrester 1960) to be used as bearing materials [1]. These alloys
provide a good combination of strength and surface properties [2].
The fatigue strength of cold worked and heat treated Al–20%Sn–
1%Cu alloy having reticular structure is close to that of Cu–30%Pb
alloy with higher seizure resistance [3]. Aluminium has a low
modulus of elasticity and apart from indium, lead has the lowest
modulus of elasticity of all the soft phases alloying with aluminium
[4]. Al-Sn based alloys are widely used as sliding bearing materials
in automobile and shipbuilding industry [5, 6]. HVOF spray process
has been introduced by McCartney to prepare Al-Sn-Si bearing alloy
coatings. Post heat treatment of the HVOF sprayed coating at 300 ºC
proved the coarsening of tin and precipitate of Si in the coating [7, 8].
Based on the feasibility of preparing oxygen sensitive metal coatings,
cold spray was also introduced to deposit Al-Sn binary alloy coatings
[9]. Al-5Sn coating can be deposited by high pressure cold spray
with nitrogen while Al-10Sn can only be deposited by low pressure
cold spray with helium gas. Both Al-5Sn and Al-10Sn coatings
present dense structures. The coarsening and/or migration of Sn
phase in the coatings were observed when the annealing temperature
exceeds 200 ºC. Furthermore, the microhardness of the coatings
decreased significantly at the annealing temperature of 250 ºC [10].
Aluminum tin and leaded aluminium alloys slightly differ in
mechanical properties. Frictional states created during sliding against
steel shaft under oil lubrication were not much different. Leaded
aluminium alloy bushes show marginally lower friction than the
conventional ones [11]. Adding Cu/Pb to Sn-Sb alloy improve their
elastic modulus, internal friction, hardness and thermal conductivity
[12]. The friction coefficients of Sn-20.2%Sb-16.6%Pb-2.6%Cu are
lower than that of Sn–7.2%Sb–0.4%Pb–3%Cu under all scratch test
conditions [13]. Structure, hardness, mechanical and electrical
transport properties of Sn90-x Sb10Bix (x = 0, or x ≥1) alloys have been
studied and analyzed [14]. The effects of solidification rate and
microadditions on mechanical properties and micromorphology of
SnSb10.4 alloy have been studied [15]. Creep behaviour, elastic
modulus and internal friction of SnSb10Cu2X2 (X=Pb, Ag, Se, Cd and
Zn) alloys have been investigated also stress exponent values have
been determined using Mulhearn-Tabor method [16]. The aim of this
research was to investigate the effect of adding titanium oxide
nanoparticles (TiO2) on structure, elastic moduli, Vickers hardness,
internal friction and thermal properties of tin-antimony-lead and tin-
aluminum bearing alloys.
Experimental work
Two groups of quaternary bearing alloys, tin- antimony-
lead- titanium oxide and tin- aluminum- titanium oxide, were used.
These groups' alloys were molten in the muffle furnace using (high
purity more than 99.95%) tin, antimony, lead, aluminum and titanium
oxide. The resulting ingots were turned and re-melted several times
to increase the homogeneity of the ingots. From these ingots, long
ribbons of about 3-5 mm width and ~ 70 m thickness were prepared
as the test samples by directing a stream of molten alloy onto the
outer surface of rapidly revolving copper roller with surface velocity
31 m/s giving a cooling rate of 3.7 × 105
k/s. The samples then cut
into convenient shape for the measurements using double knife cuter.
Structure of used alloys was performed using an Shimadzu X–ray
Diffractometer (Dx–30, Japan)of Cu–K radiation with =1.54056 Å
at 45 kV and 35 mA and Ni–filter in the angular range 2 ranging
from 0 to 100° in continuous mode with a scan speed 5 deg/min.
Electrical resistivity of used alloys was measured by double bridge
method. The melting endotherms of used alloys were obtained using
a SDT Q600 V20.9 Build 20 instrument. A digital Vickers micro-
hardness tester, (Model-FM-7- Japan), was used to measure Vickers
hardness values of used alloys. Q-1
, the elastic modulus E and

2. International Journal of Science and Engineering Applications
Volume 4 Issue 2, 2015, ISSN-2319-7560 (Online)
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thermal diffusivity Dth of used alloys were determined using the
dynamic resonance method [17- 19].
Where  is the density of the sample under test, L is the length of the
vibrated part of the sample, k is the radius of gyration of cross section
perpendicular to its plane of motion, f0 is the resonance frequency
and z is the constant depends on the mode of vibration and is equal to
1.8751. f is the half width of the resonance curve.
Results and discussions
Effect of adding TiO2 nanoparticles on structure of Sn-Sb-Pb
alloy
X-ray diffraction patterns of Sn87-xSb10Pb3(TiO2)x (x=0.5, 1
and 1.5 wt. %) rapidly solidified alloys have lines corresponding to
β- Sn, Pb/or Sb and SbSn intermetallic phases as shown in Figure 1.
X-ray analysis show that, adding TiO2 to Sn87Sb10Pb3 alloy caused a
change in Sn matrix structure such as lattice parameters and formed
crystal structure (crystallinity, crystal size and the orientation) as seen
in Table 1(a and b). That is because TiO2 nanoparticles dissolved in
Sn matrix formed a solid solution and other accumulated particles
formed a traces of phases.
Figure 1:- x-ray diffraction patterns of Sn87-xSb10Pb3(TiO2)x alloys
Table 1a:- x-ray diffraction analysis of Sn87-xSb10Pb3(TiO2)x alloys
Sn87Sb10Pb3
hklPhaseFWHMInt.%d Å2
101SbSn0.27554.373.0718629.0695
200Sn0.24001002.9286830.4985
200Sn0.072069.412.9255730.6095
101Sn0.192034.112.79643931.9779
012SbSn0.57600.772.1724641.5347
220Sn0.43205.132.0716043.6580
211Sn0.336012.292.0230444.7618
301Sn0.33603.751.6653955.1013
112Sn0.33605.811.4864862.4237
400Sn0.38404.051.4610663.6354
321Sn0.43203.591.4460964.3731
113SbSn0.57600.411.3724368.2871
420Sn0.28803.631.3087472.1128
411Sn0.28802.751.2963572.9123
321Sn0.28803.591.2069879.3161
432Sn0.24002.051.0984089.0610
103Sn0.38401.461.0420595.3295
330Sn0.48000.641.0339696.3177
521Sn0.48000.751.0278397.0846
2
0
22/1
kz
fL2E 








0
2
th
fd2
D 
0
1
f
f
5773.0Q



3. International Journal of Science and Engineering Applications
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Sn86. 5Sb10Pb3(TiO2)0.5
hklPhaseFWHMInt.%d Å2
200Sn0.25581002.9205230.6118
101Sn0.255880.392.7943332.0305
220Pb0.47231.742.4830436.1764
220Sn0.334625.532.0671543.7948
211Sn0.295256.582.0215244.8366
021SbSn0.39361.681.7492652.2999
301Sn0.275513.941.6621455.2681
112Sn0.255818.621.4863962.4854
107Sb0.27555.281.4597463.759
321Sn0.216516.611.4438564.5448
018Sb0.216510.531.3061172.3498
411Sn0.25588.951.2940973.1307
321Sn0.196816.981.2065679.4279
432Sn0.19686.941.0970689.2927
103Sn0.19686.041.0415495.4951
440Sn0.23621.821.032596.6061
521Sn0.243.091.0262297.2882
Sn86Sb10Pb3(TiO2)1
hklPhaseFWHMInt.%d Å2
200Sn0.255886.522.9203830.6133
101Sn0.25581002.7967932.0016
220Sn0.275522.172.0652543.8373
211Sn0.236266.022.0217844.8304
301Sn0.334612.861.6616955.2842
112Sn0.255825.711.4869762.4583
107Sb0.21657.611.4603863.7276
321Sn0.216517.751.4452564.4749
018Sb0.177110.421.3059472.3608
411Sn0.177110.521.2947173.0899
321Sn0.26415.711.2055279.4307
321Sn0.1928.871.2045379.7468
432Sn0.2647.471.0959489.3151
431Sn0.1924.461.0952389.6708
103Sn0.241.751.0444995.0358
103Sn0.2165.281.0405195.5155
332Sn0.2163.211.0401395.8764
440Sn0.243.091.0315896.6134
521Sn0.244.551.0255497.3745
Sn85.5Sb10Pb3(TiO2)1.5
hklPhaseFWHMInt.%d Å2
200Sn0.275588.932.921430.6023
101Sn0.25581002.7948532.0244
220Sn0.196831.182.0657443.8265
211Sn0.236260.272.0175344.9301
301Sn0.177116.361.6623755.2598
112Sn0.196820.781.4866862.4719
107Sb0.31495.731.4588963.8004
321Sn0.196814.031.4445864.5084
018Sb0.15748.851.3063872.3331
411Sn0.177110.061.2944473.1077
321Sn0.177112.821.206779.417
432Sn0.17717.161.0968289.3181
103Sn0.17717.271.0415495.4954
521Sn0.5762.881.0245897.4966
Table 1b:- lattice parameters and crystal size of β-Sn in
Sn87- xSb10Pb3(TiO2)x alloys
 ÅV Ǻ3
c Åa ÅAlloys
355.44108.8833.1745.857Sn87Sb10Pb3
514.283108.623.185.841Sn86. Sb10Pb3(TiO2)0.5
508.035109.153.25.841Sn86Sb10Pb3(TiO2)1
529.678108.833.195.843Sn85.5Sb10Pb3(TiO2)1.5
Scanning electron micrographs, SEM, of Sn87-
xSb10Pb3(TiO2)x (x=0 and 1.5 wt. %) alloys show heterogeneity
structure as shown in Figure 2. SEM micrographs of Sn87-
xSb10Pb3(TiO2)x alloys show β- Sn matrix and other accumulated
particles formed traces of phases and that is agreed with x-ray results.
Figure 2:- SEM of Sn87Sb10Pb3 and Sn85.5Sb10Pb3(TiO2)1.5 alloys

4. International Journal of Science and Engineering Applications
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Effect of adding TiO2 nanoparticles on mechanical properties of
Sn-Sb-Pb alloy
The elastic constants are directly related to atomic bonding
and structure. Elastic modului of Sn87-xSb10Pb3(TiO2)x alloys are
listed in Table 2. Elastic modulus of Sn87Sb10Pb3 alloy increased
after adding different ratio from TiO2 nanoparticles. The
Sn85.5Sb10Pb3(TiO2)1.5 alloy has highest elastic modulus.
Table 2:- elastic modului, internal friction and thermal diffusivity of
Sn87-xSb10Pb3(TiO2)x alloys
Dth x10-8
m2
sec
Q-1
B
GPa
µ
GPa
E
GPa
Alloys
9.430.02539.1512.1533.02Sn87Sb10Pb3
27.360.03145.314.138.3Sn86. 5Sb10Pb3(TiO2)0.5
21.430.02446.114.439.1Sn86Sb10Pb3(TiO2)1
41.870.01855.417.447.2Sn85. 5Sb10Pb3(TiO2)1.5
The resonance curves Sn87-xSb10Pb3(TiO2)x alloys are
shown in Figure 3. Calculated internal friction and thermal
diffusivity of Sn87-xSb10Pb3(TiO2)x alloys are listed in Table 2.
Internal friction of Sn87Sb10Pb3 alloy varied after adding different
ratio from TiO2 nanoparticles. The Sn85.5Sb10Pb3(TiO2)1.5 alloy has
lowest internal friction.
Figure 3:- resonance curves of Sn87-xSb10Pb3(TiO2)x alloys
The hardness is the property of material, which gives it the
ability to resist being permanently deformed when a load is applied.
Vickers hardness of Sn87-xSb10Pb3(TiO2)x alloys at 10 gram force and
indentation time 5 sec are shown in Table 3. The minimum shear
stress (m) value of Sn87-xSb10Pb3(TiO2)x alloys was calculated using
the equation [9], where is Poisson’s ratio of the elements in the
alloy and then listed in Table 3.
{ ( ) ( )[ ( )] }
Vickers hardness of Sn87Sb10Pb3 alloy increased after
adding TiO2 nanoparticles. That is because TiO2 dissolved in Sn
matrix formed a hard inclusion increased its hardness.
Sn85.5Sb10Pb3(TiO2)1.5 alloy has highest hardness.
Table 3:- Vickers hardness and minimum shear stress of
Sn87-xSb10Pb3(TiO2)x alloys
µs kg/mm2
Hv kg/mm2
Alloys
9.4128.52±1.8Sn87Sb10Pb3
10.4531.68±2.7Sn86. 5Sb10Pb3(TiO2)0.5
12.0536.53±3.3Sn86Sb10Pb3(TiO2)1
12.8138.83±2.4Sn85. 5Sb10Pb3(TiO2)1.5
Effect of adding TiO2 on thermal properties and electrical
resistivity of Sn- Sb- Pb alloy
Thermal analysis is often used to study solid state
transformations as well as solid-liquid reactions. Figure 4 shows
DSC thermographs for Sn87-xSb10Pb3(TiO2)x alloys. Little variation
occurred in exothermal peak of Sn87Sb10Pb3 alloy. The melting
temperature and other thermal properties of Sn87-xSb10Pb3(TiO2)x
alloys are listed in Table 4. Melting temperature of Sn87Sb10Pb3 alloy
decreased after adding TiO2 nanoparticles.
Crystalline defects serve as scattering center for conduction
electrons in metals, so the increase in their number raises the
imperfection. Electrical resistivity and calculated thermal
conductivities of Sn87-xSb10Pb3(TiO2)x alloys are shown in Table 4.
Electrical resistivity of Sn87Sb10Pb3 alloy varied after adding TiO2
nanoparticles. That is because TiO2 nanoparticles dissolved in the
Sn matrix playing as scattering center for conduction electrons
caused a change in matrix structure.
Table 4:- electric resistivity and other thermal properties of
Sn87-xSb10Pb3(TiO2)x alloys
Melting
point ºC
Cp x 103
J/kg. k
K W
m-1
K-1
ρ x10-6
Ω.cm
Alloys
236.871.842.3067.3Sn87Sb10Pb3
223.381.882.5559.04Sn86. 5Sb10Pb3(TiO2)0.5
229.523.932.3265.19Sn86Sb10Pb3(TiO2)1
229.333.291.9477.78Sn85. 5Sb10Pb3(TiO2)1.5

5. International Journal of Science and Engineering Applications
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Figure 4:- DSC of Sn87-xSb10Pb3(TiO2)x alloys
Effect of adding TiO2 nanoparticles on structure of Sn-Al alloy
X-ray diffraction patterns of Sn80-xAl20(TiO2)x (x=0.5, 1
and 1.5 wt. %) alloys have lines corresponding to β- Sn and Al
phases as shown in Figure 5. X-ray analysis show that, adding TiO2
to Sn80Al20 alloy caused a change in Sn matrix such as lattice
parameters and formed crystal structure (crystallinity, crystal size and
the orientation) as seen in Table 5 (a and b). That is because TiO2
nanoparticles dissolved in Sn matrix formed a solid solution and
other accumulated particles formed a traces of phases.
Scanning electron micrographs, SEM, of Sn80-xAl20(TiO2)x
alloys show heterogeneity structure as shown in Figure 6. SEM
micrographs of Sn80-xAl20(TiO2)x alloys show β- Sn matrix with other
accumulated particles formed traces of phases and that agree with x-
ray results
Figure 5:- x-ray diffraction patterns of
Sn80-xAl20(TiO2)x alloys

6. International Journal of Science and Engineering Applications
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Table 5a:- x-ray diffraction analysis of Sn80-xAl20(TiO2)x alloys
Sn80Al20
hklPhaseFWHMInt.%d Å2
200Sn0.121002.9202530.5888
200Sn0.09684.962.9203530.6656
101Sn0.21646.622.7951631.9935
220Sn0.16822.912.066143.7803
200Al0.1233.942.0202544.8271
301Sn0.4329.251.6603755.2821
112Sn0.249.21.4859662.448
400Sn0.2886.571.4588363.7441
220/321Al/Sn0.2410.041.4436364.4962
411Sn0.1927.21.3048972.3591
411Sn0.3366.011.2935373.0968
312Sn0.247.31.2057479.4138
431Sn0.1924.521.0957689.3336
103Sn0.7681.421.0395795.6292
521Sn0.2882.571.0254397.3885
Sn79. 5Al20(TiO2)0.5
hklPhaseFWHMInt.%d Å2
200Sn0.236263.712.9424630.378
101Sn0.598731.752.7974231.9942
220Sn0.21651002.0640943.8632
211Al0.354228.312.0212744.8424
301Sn0.354212.761.658855.3888
112Sn0.094.011.4845862.57
400Sn0.177125.991.4584363.8227
220/321Al/Sn0.314912.51.4414664.6647
420Sn0.19222.831.3040972.4103
411Sn0.177122.731.2936773.158
321Sn0.31499.171.2053879.5208
431Sn0.177117.471.0953989.4656
103Sn0.47232.831.0404395.6294
521Sn0.5764.621.0297596.8422
Sn79Al20(TiO2)1
hklPhaseFWHMInt.%Åd2
200Sn0.27551002.9207430.6095
101Sn0.236297.652.7974731.9936
220Sn0.216567.422.0590143.9771
211Sn0.334674.492.0132945.0299
301Sn0.0911.241.6582255.41
112Sn0.236222.271.4836862.6126
220/321Al/Sn0.236225.721.4413164.6723
420Sn0.0910.31.3011572.67
411Sn0.096.091.2892573.45
321Sn0.57611.971.2020679.7057
432Sn0.094.681.09489.61
103Sn0.093.281.040195.67
521Sn0.097.021.0239197.69
Sn78.5Al20(TiO2)1.5
hklPhaseFWHMInt.%Åd2
200Sn0.25581002.9199130.6183
101Sn0.236245.142.7963232.0071
220Sn0.255823.022.0608243.9365
211Al0.295230.742.0190144.8952
301Sn0.255810.961.6599655.3468
112Sn0.236211.371.4859162.5078
107Sb0.19684.341.4576463.8614
220/321Al/Sn0.216510.871.4422464.6256
018Sb0.19688.511.3054372.3939
411Sn0.17715.951.2929373.2067
321Sn0.17716.761.2061879.4578
432Sn0.19684.781.0961789.3848
103Sn0.17713.691.0407195.5964
521Sn0.5761.681.0239197.5817
Table 5b:- lattice parameters and crystal size of β-Sn in
Sn80-xAl20(TiO2)x alloys
 ÅV Ǻ3
c Åa ÅAlloys
461.64108.653.195.841Sn80Al20
390.49106.423.105.88Sn79.5Al20(TiO2)0.5
689.284107.693.165.84Sn79Al20(TiO2)1
432.55108.083.175.84Sn78.5Al20(TiO2).1.5

7. International Journal of Science and Engineering Applications
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Figure 6:- SEM of Sn80-xAl20(TiO2)x alloys
Effect of adding TiO2 nanoparticles on mechanical properties of
Sn- Al alloy
Elastic modului of Sn80-xAl20(TiO2)x alloys are listed in
Table 6. Elastic modulus of Sn80Al20 alloy increased after adding
different ratio from TiO2 nanoparticles. The Sn78.5Al20(TiO2)1.5 alloy
has highest elastic modulus.
The resonance curves Sn80-xAl20(TiO2)x alloys are shown in
Figure 7. Calculated internal friction and thermal diffusivity of Sn80-
xAl20(TiO2)x alloys are listed in Table 6. Internal friction of Sn80Al20
alloy increased after adding different ratio from TiO2 nanoparticles.
The Sn78.5Al20(TiO2)1.5 alloy has high internal friction value.
Table 6:- elastic modului, internal friction and thermal diffusivity
of Sn80-xAl20(TiO2)x alloys
Dth x10-
8
(m2
/sec)
Q-1
B
GPa
µ
GPa
E
GPa
Alloys
10.890.01137.3811.7331.85Sn80Al20
24.60.0244413.937.6Sn79.5Al20(TiO2)0.5
60.970.022745.414.338.9Sn79Al20(TiO2)1
9.600.022847.41540.8Sn78.5Al20(TiO2).1.5
Figure 7:- resonance curves of Sn80-xAl20(TiO2)x alloys
Vickers hardness of Sn80-xAl20(TiO2)x alloys at 10 gram
force and indentation time 5 sec are shown in Table 7. The minimum
shear stress (m) value of Sn80-xAl20(TiO2)x alloys was calculated then
listed in Table 7. Little variation occurred in Vickers hardness of
Sn80Al20 alloy after adding TiO2 nanoparticles.
Table 7:- Vickers hardness and minimum shear stress of
Sn80-xAl20(TiO2)x alloys
µn kg/mm2
Hv kg/mm2
Alloys
14.33±34.63 2.7Sn80Al20
11.8035.77±1.9Sn79.5Al20(TiO2)0.5
12.5037.88±2.2Sn79Al20(TiO2)1
12.8438.92±3.1Sn78.5Al20(TiO2).1.5
Effect of adding TiO2 on thermal properties and electrical
resistivity of Sn-Al alloy
Figure 8 shows DSC thermographs for Sn80-xAl20(TiO2)x
alloys. Little variation occurred in exothermal peak of Sn80Al20
alloy. The melting temperature and other thermal properties of Sn80-
xAl20(TiO2)x alloys are listed in Table 8. Melting temperature of
Sn80Al20 alloy increased after adding TiO2 nanoparticles.
Electrical resistivity and calculated thermal conductivities
of Sn80-xAl20(TiO2)x alloys are listed in Table 8. Electrical resistivity
of Sn80Al20 alloy varied after adding TiO2 nanoparticles. That is
because TiO2 nanoparticles dissolved in the Sn matrix playing as
scattering center for conduction electrons caused a change in Sn
matrix.
Table 8:- electric resistivity and other thermal properties of
Sn80-xAl20(TiO2)x alloys
Melting
point ºC
∆S
J/g. ºC
Cp x 103
J/g. ºC
K W
m-1
K-1
ρ x10-6
Ω.cm
Alloys
227.030.1220.7231.2167.3Sn80Al20

8. International Journal of Science and Engineering Applications
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228.220.1983.742.1137.30Sn79.5Al20(TiO2)0.5
228.920.1902.852.3177.76Sn79Al20(TiO2)1
229.630.23.343.2768.40Sn78.5Al20(TiO2).1.5
Figure 8:- DSC of Sn80-xAl20(TiO2)x alloys
Conclusion
Structure of Sn87Sb10Pb3 and Sn80Al20 alloys changed after
adding TiO2 nanoparticles. Elastic modulus and Vickers hardness of
Sn87Sb10Pb3 and Sn80Al20 alloys increased after adding TiO2
nanoparticles. Internal friction and mmelting temperature of
Sn87Sb10Pb3 alloy decreased but internal friction and melting
temperature of Sn80Al20 alloy increased after adding TiO2
nanoparticles. The Sn85.5Sb10Pb3(Ti2O)1.5 alloy has beast properties
for automotive industry. Also Sn78.5Al20(Ti2O)1.5 alloy has beast
properties for marine applications.
References
[1] Forrester P. G, Met. Rev. 5 (1960) 507
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