Thermodynamics of surface and interfaces (Gibbs 1876 -78) Define : Consider to be a force / unit...
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Transcript of Thermodynamics of surface and interfaces (Gibbs 1876 -78) Define : Consider to be a force / unit...
Thermodynamics of surface and interfaces – (Gibbs 1876 -78)
Define :
Consider to be a force / unit length of surface perimeter.
(fluid systems)
If a portion of the perimeter moves an infinitesimal of distance in the plane o
f the surface of area A, the area change dA is a product of that portion of peri
meter and the length moved.
dAdNpdVTdSdU ii
i
Work term - dA; force x distance, and appear in the combined 1st an
d 2nd laws of thermodynamics as
J. W. Gibbs, collected works, Yale Univ. Press, New Haven, vol.1(1957), p. 219 ~ 331.
For a system containing a plane surface this equation can be reading integrated
:
i ii
U TS PV N A
Strictly speaking , is defined as the change in internal energy when
the area is reversibly increased at constant S, V and Ni (i.e., closed
system).
i
ii NPVTSU
A 1
where U – TS + PV is the Gibbs free energy of the system.
and rearranging for yields.
And ii
i N is the Gibbs free energy of the materials comprising the
system.
def Surface Excess Quantities
Macroscopic extensive properties of an interface separating bulk phases a
re defined as a surface excess.
Thus is an excess free energy due to the presence of the surface.
There is a hypothetical 2D “dividing surface” defined for which the para
meters of the bulk phases change discontinuously at the dividing surface.
def The excess is defined as the difference between the actual value of the
extensive quantity in the system and that which would have been prese
nt in the same volume if the phases were homogeneous right up to the
“ Dividing Surface ” i.e.,
xxxx totals
The real value of x in the system
The values of x in the homogeneous and phases
Solid and liquid Surfaces
In a nn pair potential model of a solid, the surface free energy can be thought of as the energy/ unit -area associated with bond breaking. :
work/ unit area to create new surface = 2An
Then letting A = a2 where a lattice spacing 22a
where n/A is the # of broken bonds / unit-area and the is the energy per bond i.e., the well depth in the pair-potential.
pair potential
r
U(r)
AddAdU
and dU df AdA dA
If the solid is sketched such that the surface area is altered
the energy ddAAA
daaa
The total energy of the surface is changed by an amount..surfS AU
Surface Stress and Surface Energy
Then in general the relationship between surface stress and surfaceenergy is given by,
1,2 j i, fij
ijij
For a surface with 3-fold or higher rotational symmetry fij is isotropicand the surface stress can be treated as a scalar.
dAdAf
def
f - The surface stress is the reversible work/unit area associated with the creation of new surface while altering its density by elastic stretching or compressing.
dAdAf
dAdU for an isotropic surface
For an anisotropic surface f is a tensor quantity and
ijijijf
where double sum in the strains and .)1(0 ijAA ijA
dA
The anisotropy of surface energy
Surface energy is a function of orientation – crystalline solid. For a liquid γ i
s isotropic and the equilibrium shape minimizes the surface / volume ratio. Fo
r example, the equilibrium hape of a soap bubble is a sphere.
Experimentally it has been found that cuts of crystals off a low index orient
ation equilibrate to form stepped structures such that the steps are composed
of low-index surfaces.
broken bond
( 1 0 ) plane
Bond density along direction defined by θ is greater than the bond density al
ong a low index direction owing to step structure.
2
sincos2
a
where a (lattice parameter) is the unit of length and ε/2 the bond energy,
θ is the mis-orientation with respect to a low-index plane.
In a nn. central force model, for surfaces forming a stepped structure
is given by:
(10)“cusps” @ 0
Polar Plot of
Low-index plane have cusps in plots at 0 K which tend to get ro
unded off at higher temperatures.
Inner envelope of normals defining the equilibrium of shape of crystal.
Equilibrium shape of a crystal obtained when minimumplanes
ii A
and this is given by the Wolff’s theorem.
( 0 1 )( 1 1 )
( 1 0 )
Example of a 2D polar plot of
Wulff construction
Wulff’s theorem : The equilibrium shape is obtained by taking the inner
envelope of the normals. This envelope defines a shape geometrically
similar to the equilibrium shape of the crystal
Any surface which does not appear in the equilibrium shape can lower
its energy by forming a stepped structure, composed of planes which do
appear in the equilibrium shape.
Often actual morphologies are determined by kinetic considerations.
Suppose the velocity of the interface is controlled by surface diffusion.
( 0 1 ) ( 1 1 )
( 1 0 )
Einstein mobility relation
MF
If the temp. dep M is about the same for all the orientation v is determined
by F. Generally the lower , the higher F so: e.g.
)11()01()11()01()11()01( ; ; vvFF
Faster growth
Slower growth
Faster growth
The surfaces which grow faster tend to shrink in size.
Growth of crystals occur by a ledge process.
Fast
Slow
Faster faces grow out; overall growth tends to be limited by slowest faces.
Estimation of interfacial energies
Recall: 2/aZ
Types of Interfaces
(d) Solid / solid
chemical
structural
(a) solid / vapor
(b) liquid / vapor
(c) solid / liquid
where is the bond energy, Z is the number of near neighbors
and is the atom density of surface.
a
For the liquid / vapor interface -
vapaLv LZ 2/
For the solid / liquid interface – entropic effects dominate.
/ 2SL a fusionZ S T
m
fusfusion T
LS
Note the temperature dependence.
For many situations, these values provide reasonable estimates.
For the solid / vapor interface -
fusionvap LLL nsublimatio
subasv LZ 2/
( J / m2 ) near Tm
( J / m2 ) @ 25ºC
Sn 0.68 MgO 1.0
Ag 1.12CaF2 (111)
0.45
Pt 2.28CaCo3 (1010)
0.23
Cu 1.72LiF
(100)0.34
Au 1.39NaCl(100)
0.30
T (°C) ( J / m2 )
H2O 25 0.072
Pb 350 0.442
Cu 1120 1.270
Ag 1000 0.920
Pt 1770 1.865
NaPO 620 0.209
FeO 1420 0.585
Al2O3 2080 0.700
SV SV LV
Note that near Tm, lv ~ sv.
Values of SV Values of LV
( J / m2 ) near Tm
Al 0.093
Cu 0.177
Fe 0.204
Pb 0.033C2H2(CN)2 [succinonitrile] 0.009
Nylon 0.020
vdPsdTd p
sT
and for metals 3 210 / weak T dependences J m K
Values of (inferred from nucleation exp)SL
SL
Temperature dependence of ( solid / vapor, liquid / vapor ) recall that for a 1 component system:
Solid / Solid Interfaces
(i) Chemical bonding(ii) Structural bonding ( say phases have different crystal structure)
structuralchemical
y (distance)
xα
xβ
xα is the mole fraction of A in α
xβ is the mole fraction of A in β
Chemical contribution to :chemical
Consider a general inter-phase α/ β boundary. can be thought of as being composed of 2 terms :
Let U(x1, x2) be the sum of the bond energy per unit area between
planes of composition x1 and x2
1, 2 / 2 1 1 1 1 a AA BB ABU x x Z x x V x x V x x x x V
where VAA, VBB, and VAB are the bond energy.
In analogy with the regular solution model we define an excess energy, Ui, due to the interface:
2, 1/ 2 , , / 2 i aU U x x U x x U x x x x
where 2/1 BBAAAB VVVZ
Ω can be estimated from Ω/2R = T critical (see Reg. Sol. Theory)
Regular solution model of an interfaces (Becker 1938)
For metal / metal interfaces :
219 /10 2/ ma atJatomeV /10 / 1.0 ~ -20
For close to pure metal interfaces :
0 ,1 xx
so 21 /10~ mJU i
Typical values of lattice matched (coherent) interfaces energies range from 10-3 ~ 10-1 J/m2.
* The diffuse chemical interface (1-D estimates)
– variation in the mole fraction of A atom 1 plane to the nextx
interplaner spacinga
y (distance)a
x
x
x
2 2/ xxU ai generalize to a continuum
2
1,22
i
iiai a
xxΩa/ρU
, 1i ix x dx a dy
2
22
12i adx dx
dyU ρ a
dyK/ Ω
composition gradient
K1 Gradient energy coefficient in 1D
* important in spinodal decomposition
Cahn – Hilliard Free Energy (1958)
Consider a small region of material with a chemical inhomogeneity. :
The free energy per unit volume can be thought of as being composed oftwo terms:
(i) g0(C) homogeneous free energy per unit volume, if the material was of
homogeneous composition ( Regular sol. Model)(ii) g i(C) inhomogeneous free energy owing to the presence of the comp
ositional gradient K(C)2
The total free energy is expressed as a functional ( a function of afunction) i.e.,
20 ( ) ( )
VG g c K C dV
for metals K 10-19 J/m
Classification of structural interfaces:
(i) Coherent lattice matched systems some x’tal structure or ( 1 1 1 )fcc / ( 0 1 1 )hcp or ( 1 1 1 )fcc / ( 1 1 0 )bcc and etc.
(i i) Incoherent
The structural misfit energy is most easily accommodated by forming “misfit dislocation” in the interface.
Structural Interfacial energy: ( to be discussed in more detail later, see coherence)
Def misfita a
ma
For “large” m misfit dislocations form.
Grain boundaries, twin boundaries, stacking faults are examples of
structural interfaces which can have ( 1 component ) no chemical term.
Gbs are incoherent interfaces defined by the relative misoreintation between grains. To specify a gb define the orientation of the crystallites with respect to one another and the orientation of the boundary with respect to one of the crystallites. In 3D the specification of 3 angles ( with respect to the coordinate axes) is necessary to describe the relative orientation between crystals and 2 angles specify the boundary orientation with respect to one of the crystal axes. ( see Bollman, 1970, “ crystal defects and interfaces’)
Grain boundaries
Cut ABCD
Consider the triple point of a gb junction:
Grain 1
Grain 2
Grain 312
23
13
12
23
13
Rot @ y-axis
Twist boundaryTilt boundary
Rot @ x-axis
Ay
z
x
B C
D
Herring (1951) showed that by balancing the forces for a virtual change in the orientation of the triple junction :
1313
1323
23
232313132312 sinsincoscos
where the
i
i
terms are called “ surface torque” terms.
For high angle gb the torque terms can be neglected and
23
23
13
13
12
12
sinsinsin
d23
d13
13
23
12
Wetting (Contact) Angle
LV
solid
SVSL
Force Balance
cosLVSLSV
Def
s SL SV
s
LV
cos
is called the wetting or contact angle.
s SL SV s
LV
cos
θ = 0 Complete wettings LV
θ < 90º0s
θ > 90º0s
θ > 180ºs LV No wetting