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Positron annihilation and tribological studies of nano-embedded Al-alloys
Jerzy Dryzek1,2, Krzysztof Siemek2 and Krzysztof Ziewiec3
1Institute of Physics, Opole University, ul. Oleska 48, Opole, Poland 2Institute of Nuclear Physics PAN, ul. Radzikowskiego 152, Kraków, Poland 3Pedagogical University of Cracow, ul. Podchorążych 2, Kraków, Poland
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Embedded nanoparticles of metals and alloys are an important class of nanomaterials requiring understanding. Additionally alloys with embedeed nanoparticles have important applications.
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Motivation
Over 109 bearing shells for journal
bearings are produced annually.
The Pb-Sb-Sn system (Isaac Babbit
1839) is the first triboalloys used as the
shells.
The substituted the systems Al-Sn and
Al-Pb are also applied.
The Al-based alloys are predominate in
European and Asian markets for
compact engines.
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We intend to include the positron studies for such triboalloys. We expect some new results, especialy positron localiztion at nanoparticles. However, our research interests is focused also on the subsurface zone (SZ) in the triboalloys based on Al.
-friction force,
-wear,
-subsurface zone with
defects,
-…
-emission of electrons,
-transfer of mass
between bodies.
-…
sliding
body
sample
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Plane
Introduction to positron annihilation techniques
The production procedure of the triboalloys based on aluminium
The XRD and SEM detection of nanoparticles
The results of tribological studies
Positron and microhardness studies of isochronal annealing of the
triboalloys
The subsurface zone in Al-In10 alloy
Conclusions
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Few words about positron annihilation techniques
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Positron and electron pair annihilation
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Beta+ decay of 22Na isotope; common positron source
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Doppler broadening (DB) measurement
e
e
+
-
Na22
sample
LN2
HpGe
e+
(511+ )keV
(511- )keV
90
m
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Annihilation line of defects free copper
photon energy (keV)
501 506 511 516 521
norm
aliz
ed c
ounts
1e-5
1e-4
1e-3
1e-2
Well annelad copper
background
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Annihilation line for copper after deep deformation
photon energy (keV)
501 506 511 516 521
norm
aliz
ed c
ounts
1e-5
1e-4
1e-3
1e-2
Well annelad copper copper after deep deformation
background
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The line shape parameter, S-parameter
photon energy (keV)
501 506 511 516 521
norm
aliz
ed c
ounts
1e-5
1e-4
1e-3
1e-2
Well annelad copper copper after deep deformation
S-parameter
background
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Dependency of the S-parameter versus the degree of deformation for copper
thickness reduction (%)
0 10 20 30
S-p
ara
mete
r
0.53
0.54
0.55
0.56
0.57
0.58
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Coincidence Doppler broadening (CDB) measurement
e
e
+
-
Na22
sample
HpGe
e+
(511+ )keV
(511- )keV
LN2
HpGe
LN2
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CDB spectrum of pure alumnium
photon energy (keV)
496 498 500 502 504 506 508 510 512 514 516 518 520 522 524 526
counts
1e+0
1e+1
1e+2
1e+3
1e+4
1e+5
1e+6
Aluminium
core regioncore region band region
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Positron lifetime measurement
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Al
=165 ps
bulk,perfect lattice
=248 ps
monovacancy
270 ps
divacancy
=174 ps
edge dislocation
=165 ps
interstital atom
vacancynear dislocation line
215 ps< <230 ps
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Dependency of the positron lifetime on the size of vacancy cluster in Al and Fe.
M.J. Puska, P. Lanki, R.M. Nieminen, J. Phys.:Condens Master, 1 (1989) 6081.
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Saka H, Nishikawa Y, Imura T Melting temperature of In particles embedded in an Al matrix. Philos. Mag.
A57: (1988) 895.
Sasaki K, Saka H In situ high-resolution electron microscopy observation of the melting process of In
particles embedded in an Al matrix. Philos. Mag. A63: (1991) 1207.
B. Klobes, B. Korff, O. Balarisi, P. Eich, M. Haaks, I. Kohlbach, K.Maier, R. Sottong and T E M Staab.
Defect investigations of micron sized precipitates in Al alloys, Journal of Physics: Conference Series
262 (2011) 012030.
Liu Yuan et al. Microstructures of rapidly solidified Al-In immiscible alloy. Trans. Nonferrous Met. Soc.
China. Vol. 11 (2001) 84.
J.P. Pathak and S. Mohan. Tribological behaviour of conventional Al–Sn and equivalent Al–Pb alloys
under lubrication. Bull. Mater. Sci., vol. 26, (2003), 315–320.
V. Bhattacharya, K. Chattopadhyay. Morphology and phase transformation of nanoscaled indium–tin
alloys in aluminium. Materials Science and Engineering A 375–377 (2004) 932–935.
V. Bhattacharyay, K. Chattopadhyay and P. Ayyub. Synthesis, transformation and superconductivity of
dual phaseIn–Sn alloy nanoparticles embedded in an Al matrix. Philosophical Magazine Letters, Vol.
85, (2005), 577–585.
Papers devoted to the aluminium alloys with embedded particles
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A. Singh and A. P. Tsai. Melting behaviour of lead and bismuth nano-particles in
quasicrystalline matrix - The role of interfaces. Sadhana Vol. 28, (2003) 63–80.
V. Bhattacharya, K. Chattopadhyay. Melting of multiphase nano-scaled particles embedded in Al
matrix: Case of Pb–Sn and Bi–Sn alloys. Materials Science and Engineering A 449–451
(2007) 1003–1008.
V. Bhattacharya, K. Chattopadhyay. Melting of multiphase nano-scaled particles embedded in Al
matrix: Case of Pb–Sn and Bi–Sn alloys. Scripta Mater. 44 (2001) 1677-1682
(Al-Sn) P.G. Forrester, Met Rev. 5 (1960) 507.
P. Bhattacharya, V. Bhattacharya, K. Chattopadhyay. Morphology and thermal characteristics of
nano-sized Pb–Sn inclusions in Al. J. Mater. Res., Vol. 17, No. (2002) 2875.
V. Bhattacharya, K. Chattopadhyay. Microstructure and wear behaviour of aluminium alloys
containing embedded nanoscaled lead dispersoids. Acta Materialia 52 (2004) 2293–2304
R. Schouwenaars, V.H. Jacobo, A. Ortiz. Microstructural aspects of wear in soft tribological
alloys. Wear , 263 (2007) 727–735.
R. Schouwenaars, V.H. Jacobo, A. Ortiz, Microstructural aspects of wear in soft tribological
alloys. Wear, 263 (2007) 727-735.
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Soft dispersions in a hard matrix
Significant improvement of frictional properties under mild wear conditions of
nanoscaled dispersion of Pb, In and Bi in Al. host has been observed.
V. Bhattacharya, K. Chattopadhyay. Scripta Mater. 44 (2001) 1677-1682
S.N. Tiwari, Wear. 112 (1986) 341
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The melt-spinning technique for production of binary immiscible alloys
Argon gas under pressure
melt metalsinductionheating
rotatingcopper cylinder
melt-spunribbon
v=22 m/s
Al-In10 wt%
Al-Pb10 wt%
Al-Sn5 wt%
Al-Bi10 wt%
Al-Au0.5 wt%
Al as-cast
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XRD
30 40 50 60 70 80 90
Al90In10
Al95Sn5
Al90Bi10
Al90Pb10
Aluminum
Bi 1
10
Sn
Sn
Sn
Sn
10
1S
n 2
00
Sn
00
1
In
In
In 1
01
Pb
33
1
Pb
31
1
Pb
22
0
Pb
20
0
Pb
11
1
Al 2
22
Al 3
11
Al 2
20
Al 2
00
Al 1
11
Inte
nsity
2
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a Al90In10 b) Al95Sn5
c) Al90Pb10 d) Al99.5Au0.5
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Al-In10
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Nano-scaled eutectic lead–tin and bismuth–tin alloys embedded in aluminum matrix
V. Bhattacharya, K. Chattopadhyay. Materials Science and Engineering A 449–451 (2007) 1003–1008.
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The particle size distribution
diameter (nm)
0 100 200 300 400 500 600
fraction (
%)
0
2
4
6
8
10
12
14
16
18
Al-Pb10
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bi
diameter (nm)
50 100 150 200 250 300 350 400
fraction (
%)
0
5
10
15
20
Al-Sn5
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diameter (nm)
50 100 150 200 250 300 350
fra
ctio
n (
%)
0
5
10
15
20
Al-In10
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The properties of the Al alloys
Alloy Average
particle
diameter
(nm)
Variance
(nm)
Friction
coefficient
Specific wear
rate
[10-12 m3/mN]
Vickers
microhar
dness
Positron
lifetime
(ps)
Al-In10 83 48 0.38 0.058 71.6 256.9(0.5)
Al-Sn5 108 64 0.39 0.099 41.3 253.7(0.5)
Al-Pb10 173 92 0.40 0.084 39.2 257.2(0.5)
Al-Bi10 671 374 - - - -
Al-Au0.5 - - 0.42 0.066 59.3 224.1(0.5)
Al as-cast - - 0.82 3.295 28.6 229.7(0.5)
AK12 0.46 0.066 178(1)
AK 12 (with the following composition: Si 12.0–13.5 wt.%, Cu 0.5–1.5 wt.%, Mg 1.0–1.5 wt.%,
Ni 0.5–1.5 wt.%, Mn 0.2 wt.%, Zn 0.2 wt.%, Fe 0.6 wt.%, Al. balance)
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Tribo test, pin on disc device
load
friction force
pin (rod)
measurementdevice
disc
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The specific wear rate measurements
distance (m)
0 10 20 30 40 50 60
mass loss (
mg)
0
1
2
3
4
5
Al-Au0.5
Ar-Sn5
Al-In10
A--Pb10
Al as-cast
alloys
Al as-cast
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The properties of the Al alloys
AK 12 (with the following composition: Si 12.0–13.5 wt.%, Cu 0.5–1.5 wt.%, Mg 1.0–1.5 wt.%,
Ni 0.5–1.5 wt.%, Mn 0.2 wt.%, Zn 0.2 wt.%, Fe 0.6 wt.%, Al. balance)
Alloy Average
particle
diameter
(nm)
Variance
(nm)
Friction
coefficient
Specific wear
rate
[10-12 m3/mN]
Vickers
microhar
dness
Positron
lifetime
(ps)
Al-In10 83 48 0.38 0.058 71.6 256.9(0.5)
Al-Sn5 108 64 0.39 0.099 41.3 253.7(0.5)
Al-Pb10 173 92 0.40 0.084 39.2 257.2(0.5)
Al-Bi10 671 374 - - - -
Al-Au0.5 - - 0.42 0.066 59.3 224.1(0.5)
Al as-cast - - 0.82 3.295 28.6 229.7(0.5)
AK12 0.46 0.066 178(1)
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Temperature dependences of microhardness
temperature (oC)
0 100 200 300 400 500
mic
rohard
ness (H
V)
10
20
30
40
50
60
70 Al-In10
Al-Au0.5
Al-Sn5
Al-Pb10
Al as-cast
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Temperature dependences of S-parameter
temperature (oC)
0 100 200 300 400 500 600
S-p
ara
mete
r
0.525
0.530
0.535
0.540
Al as-cast
Al-In10
Al-Sn5
bulk
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Diffusion positron trapping model with grain size increase
( / )3( )
1 ( / )
m g b g
b
L L R LS S S S
R LL R L
bL D
( ) coth( ) 1/L z z z
J. Dryzek, Acta Physica Polonica A, 95 (1999) 539
J. Dryzek, Appl. Phys. A 114 (2014) 465-475
0 0( , ) expn n
B
QR t T R t M
k T
where Q is the activation energy of boundary migration
n=2
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Temperature dependences of S-parameter
temperature (oC)
0 100 200 300 400 500 600
S-p
ara
mete
r
0.525
0.530
0.535
0.540
Al as-cast
Al-In10
Al-Sn5
bulk
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Temperature dependences of S-parameter
temperature (oC)
0 100 200 300 400 500 600
S-p
ara
mete
r
0.525
0.530
0.535
0.540
Al as-cast
Al-In10
Al-Sn5
bulk
DTM [Q=(2.12 ±0.4)] eV)
DTM [Q=(0.65 ± 0.2)] eV)
F.J. Humphreys and M.Hatherly, „Recrystallization and related annealing
phenomena”, Elsevier (2004) QB=0.87 eV
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Temperature dependences of S-parameter
temperature (oC)
0 100 200 300 400 500 600
S-p
ara
mete
r
0,520
0,522
0,524
0,526
0,528
0,530
0,532
0,534
0,536
0,538
0,540
Al-Au0.5
Al-Pb10
bulk
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Temperature dependences of S-parameter
temperature (oC)
0 100 200 300 400 500 600
S-p
ara
mete
r
0,520
0,522
0,524
0,526
0,528
0,530
0,532
0,534
0,536
0,538
0,540
Al-Au0.5
Al-Pb10
bulk
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Activation energy of boundary migration determined from the DTM
Alloy Q
(eV)
Al-In10 2.12±0.4
Al-Sn5 1.12±0.2
Al-Pb10 1.43±0.3
Al-Au0.5 1.73±0.4
Al_cast 0.65±0.2
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CDB spectrum of pure alumnium and gold
photon energy (keV)
496 498 500 502 504 506 508 510 512 514 516 518 520 522 524 526
counts
1e+0
1e+1
1e+2
1e+3
1e+4
1e+5
1e+6
electron momentum (mrad)
-50 -40 -30 -20 -10 0 10 20 30 40 50
Aluminium
Gold
core regioncore region band region
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The ratio curve for Au related to Al spectrum
photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0
1
2
3
4
Au
Al
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The ratio curves for Au and Al as-cast related to Al spectrum
photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0
1
2
3
4
Au
Al
Al as-cast
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The ratio curves for Au and Al-Au0.5 related to Al spectrum
photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0
1
2
3
4
Au
Al-Au0.5Al
Al as-cast
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The ratio curves
photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0
1
2
3
4
Au
Al-Au0.5Al
Al as-cast
(1 )alloy Al cast metalN NN
=0.006
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photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0.0
0.5
1.0
1.5
2.0
electron momentum (mrad)
0 5 10 15 20 25 30 35
Al-In10
Al
In
Al as-cast
(1 )alloy Alas cast metalN NN
=0.38
Volume fraction
of In nanoparticles:
0.27
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photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0.0
0.5
1.0
1.5
2.0
electron momentum (mrad)
0 5 10 15 20 25 30 35
Sn
Al-Sn5
Al
Al as-cast
(1 )alloy Al cast metalN NN
=0.23
Volume fraction
of Sn nanoparticles:
0.12
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photon energy (keV)
511 512 513 514 515 516 517 518 519 520
ratio to a
nneale
d A
l
0.0
0.5
1.0
1.5
2.0
electron momentum (mrad)
0 5 10 15 20 25 30 35
Pb
Al-Pb10Al
Al as-cast
(1 )alloy Al cast metalN NN
=0.23
Volume fraction
of Pb nanoparticles:
0.26
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Subsurface zone for Al-In10 alloy
depth from the worn surface (m)
0 50 100 150 200 250 300 350
positro
n m
ean lifetim
e (
ps)
190
200
210
220
230
240
250
260
200 N
50 N
100 N
Al-In10 Load
200+46 exp(-d/95)
200+38 exp(-d/52)
the worn surface
the SZ or workhardening zone
interior
.
.
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Positron beam studies of the Al-Pb10 alloy after friction test.
incident positron energy (keV)
0 10 20 30
S p
ara
mete
r
0,49
0,50
0,51
0,52
depth (nm)
0 483 1664 3428
Al90Pb10_reference
Al90Pb10_10kg
Al90Pb10_20kg
L+=0.74 nm
L+=0.60 nm
doxides = 4.29 nm
L+oxides= 0.90 nm
L+= 55.49 nm
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Conclusions
The embedded nanopraticles in the aluminium host imporve the tribo-
properties, they reduce the wear rate and friction coefficient.
They prevent the grain motion and increase the migration energy
activation.
In the studied triboalloys positrons are trapped at vacancies, preasumbly
located at the interface of the nanoparticles and the aluminium host.
The subsurface zone induced by dry sliding is expanded in the interior at
the depth of 100-300 m depending on the applied load.
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Thank you for your attention