Photonic crystals in biology
Photonic crystals in biology
Photonic crystals in biology
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Poster Session, Tuesday, June 15<br />
Theme A1 - B702<br />
Melt<strong>in</strong>g evolution of Fe nanoparticles from molecular dynamics simulations<br />
Serap Senturk Dalgic ,1 *, Cem Canan 1 and Oguz Gulseren 2<br />
1 Department of Physics, Trakya University, Edirne, 22030, Turkey<br />
2 Department of Physics. Bilkent University. Bilkent, Ankara 06800, Turkey<br />
Abstract–In order to study the melt<strong>in</strong>g properties of bcc metal iron nanoparticles, molecular dynamics calculations have been performed for<br />
various nanoparticles with different number of atoms. The modified analytic embedded atom method (MAEAM) <strong>in</strong>teratomic potentials are<br />
used to describe the <strong>in</strong>teraction between Fe atoms. The melt<strong>in</strong>g process can be described as occurr<strong>in</strong>g <strong>in</strong> two stages, firstly the stepwise<br />
premelt<strong>in</strong>g of the surface layer with a thickness of 2–3 times the perfect lattice constant, and then the abrupt overall melt<strong>in</strong>g of the whole<br />
nanoparticle. The melt<strong>in</strong>g po<strong>in</strong>t and heat of fusion of nanoparticles are <strong>in</strong>versely proportional to the reciprocal of the nanoparticle size. We<br />
have also studied the structural evolution of Fe nanoparticles with different temperature. Radial distribution functions are adopted to explore<br />
structural transition. In addition, dynamic properties of Fe nanop articles such as diffusion coefficient (D), mean square displacement (MSD)<br />
have been calculated.<br />
There are various reasons for the great <strong>in</strong>terest <strong>in</strong> iron<br />
(Fe) nanoparticles. Generally, magnetic nanoparticles are<br />
receiv<strong>in</strong>g a lot of attention today because of several<br />
possible applications. Hence, ow<strong>in</strong>g to its magnetic<br />
properties, there is special <strong>in</strong>terest <strong>in</strong> iron. Indeed, iron<br />
nanoparticles have attracted special attention because they<br />
may be used <strong>in</strong> power-transformer cores and magnetic<br />
storage media as well as for catalysis (see the good review<br />
about the synthesis, properties and applications of Fe<br />
nanoparticles of Huber [1]). Iron nanoparticles can be<br />
produced <strong>in</strong> both forms, i.e. <strong>in</strong> crystall<strong>in</strong>e and amorphous<br />
phases, and much attention has been paid to the latter <strong>in</strong><br />
recent years [2]. We found only a few works related to the<br />
computer simulation of crystall<strong>in</strong>e Fe nanoparticles [3–5].<br />
In the present study, the melt<strong>in</strong>g process of Fe<br />
nanoparticles with the number of atoms rang<strong>in</strong>g from 2741<br />
to 44375 (diameters around 4–10 nm) has been simulated<br />
by us<strong>in</strong>g modified analytic embedded atom method<br />
(MAEAM) [6]. Dur<strong>in</strong>g melt<strong>in</strong>g process, we have studied<br />
mean atomic energy changes with respect to the<br />
temperature for bulk Fe and four Fe nanoparticles. Then,<br />
we have also <strong>in</strong>terested <strong>in</strong> how the melt<strong>in</strong>g temperature and<br />
heats of fusion depend on size of nanoparticles. The static<br />
and dynamic structural properties have been calculated for<br />
four nanoparticles with different sizes and then structural<br />
transitions have been <strong>in</strong>vestigated <strong>in</strong> detail. The <strong>in</strong>itial<br />
configurations of spherical nanoparticles, with<br />
nanoparticles diameter 4, 6, 8, 10 nm, are extracted from a<br />
large BCC crystal structure of spherical cutoff centered at a<br />
core of cubes. All of the atoms are located on their lattice<br />
positions. The stable structure at 0 °K is obta<strong>in</strong>ed through<br />
the <strong>in</strong>itial configurations annealed fully at T=300 °K and<br />
then cooled to T=0 °K at a cool<strong>in</strong>g rate 0.5 K/ps. In order to<br />
get an energy-optimized structure dur<strong>in</strong>g heat<strong>in</strong>g at a given<br />
temperature for bulk systems, molecular dynamics<br />
calculations under constant temperature and constant<br />
pressure conditions (NPT) with periodic boundary<br />
conditions have been performed. For the nanoparticles, we<br />
used the constant volume and constant temperature (NVT)<br />
molecular dynamics without the periodic boundary<br />
conditions. The temperature is controlled by Nose-Hoover<br />
thermostat. Newtonian equations of motion are <strong>in</strong>tegrated<br />
us<strong>in</strong>g the Leapfrog Verlet method with a time step 2 fs. For<br />
bulk and nanoparticles, system is subjected to heat<strong>in</strong>g<br />
process consist<strong>in</strong>g of a series of MD simulations with<br />
temperature <strong>in</strong>crements T=50 °K and relax<strong>in</strong>g time 100ps.<br />
However, for a temperature near the melt<strong>in</strong>g region, we<br />
have used smaller temperature <strong>in</strong>crement, T=10 °K, wh ile<br />
keep<strong>in</strong>g the relaxation time as 100 ps.<br />
For the <strong>in</strong>vestigation of melt<strong>in</strong>g evolution and<br />
dist<strong>in</strong>ctive surface properties, two spherical shell regions<br />
with the same thickness of a 0 are divided and labeled as A,<br />
B, start<strong>in</strong>g fromthe outmost shell, and the rema<strong>in</strong><strong>in</strong>g core is<br />
labeled as C analyzed respectively as shown <strong>in</strong> Figure 1.<br />
T =300 °K T =900 °K T =1200 °K T =1800 °K<br />
Figure 1. x-y coord<strong>in</strong>ate snapshot views of the MD sample with<br />
N=9577 (D=6nm) at a series of temperatures dur<strong>in</strong>g heat<strong>in</strong>g with<br />
layers A, B, C(core) yellow, brown and red respectively.<br />
To conclude, we have <strong>in</strong>vestigated the melt<strong>in</strong>g evolution<br />
of iron nanoparticles from molecular dynamics simulations<br />
us<strong>in</strong>g a modified analytic embedded-atom potential. The<br />
evolution of atomic configuration and energy with<br />
temperature reveals that the melt<strong>in</strong>g process of iron<br />
nanoparticles can be described <strong>in</strong> two stages, the stepwise<br />
premelt<strong>in</strong>g from the outmost surface and the sudden<br />
melt<strong>in</strong>g <strong>in</strong> the <strong>in</strong>ner core. The thickness of the liquid sk<strong>in</strong><br />
result<strong>in</strong>g from the surface premelt<strong>in</strong>g is discrepant for<br />
particles with different diameters. Ow<strong>in</strong>g to the two stages<br />
melt<strong>in</strong>g, the heat of melt<strong>in</strong>g for nanoparticles should<br />
<strong>in</strong>volve two parts. As the particle size decreases, the heat of<br />
melt decreases correspond<strong>in</strong>gly. The atomic diffusion <strong>in</strong><br />
nanoparticles is ma<strong>in</strong>ly localized to the surface layers<br />
before the melt<strong>in</strong>g temperature and <strong>in</strong>creases with the<br />
reduction of particle size at the same temperature.<br />
* Correspond<strong>in</strong>g author: dserap@yahoo.com<br />
[1] Huber D L Small 1, 482 (2005)<br />
[2] Hoang V. V, Nanotechnology, 20, 295703 (2009).<br />
[3] Postnikov A V, Entel P and Soler J M, Eur. Phys. J. D 25<br />
261 (2003)<br />
[4] Rollmann G, GrunerM E, Hucht A, Meyer R, Entel P,<br />
Tiago M L and Chelikowsky J R, Phys. Rev. Lett. 99 083402<br />
(2007)<br />
[5] Shibuta Y and Suzuki T, Chem. Phys. Lett. 445 265 (2008)<br />
[6] 0TZhang J, Wen Y, Xu K, Central European Journal of<br />
Physics, 4, 481 (2006)<br />
6th Nanoscience and Nanotechnology Conference, zmir, 2010 342