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Notation con-vention
Let G' stand for total free energy and in a similar fashion S', V', H', etc.
Then we will let = G'/n represent the free energy per mole, n, and in a similar fashion. S', V', H', etc.
Partial Molar & Excess Quantities
G
Consider a solution of volume V’ containing n, moles of a component 1, n2
moles of a component 2 and etc.
,2,1 nnVV
2
,,,21
,,,13232
dnn
Vdn
n
VVd
nnPTnnPT
def
jnPTin
VV
,,
Partial molar volume of component i
iiG Where the def the chemical potential of i
2211 dnVdnVVd
2211 dnHdnHHd
2211 dnGdnGGd
2211 dndnGd
A
Integrating the set of equation A ,
2211 nnG
2211 nVnVVB
etc
22221111 dndndndnGd
02211 dndn etc
Can also be written as
02211 dxdx
Gibbs-Duhem eqns.
Differentiating the set B
and comparing and A B
*In the derivation of the Gibbs phase rule the Gibbs-Duhem eqns.
play an important rule in restricting the allowed variations.
Activity and the activity coeffi-cient
Def : activity
0i
ii p
pa
Ideal Solution
Let Poi correspond to the equilibrium vapor pressure of the pure component, i.
ai
1.0
xi 1
Raoult’s Law
Raoult’s law iii pxp
by def of aiii xa
Regular Solution
Henry’s law
by def of ai
gi is known as the activity coeff. (* g = 1 for ideal solution)
gi is independent of Xi only when Xi is “small”
ai
1.0
xi 1.0Henry’s law
pos. and neg. deviations (g > or < 1)
from ideality
ii bxp
iiiii
ii xx
p
b
p
bxa
Consider a regular solution of components A and B
in a Regular Solution the solute will often follow Henry’s law and
the solvent Raoults law when the solution is “dilute”.
< 0ai
1.0
xB 1.0
Henry’s law
Raoult’s Law
Partial molar Quantities in Ideal and regular solution
Grouping terms in and comparing coefficients of XA and XB in
and
AA
B
AAA xRT ln0
BBB xRT ln0
Where AA G0 and
BB G0
Ideal Solution
ln lnA A B B A A B BG x G x G RT x x x x A
We can also write the Gibbs potential as
A A B BG x x B
Regular Solutions:
0 0 ln lnA A B B A B A A B BG x x x x RT x x x x A
Using the identity ABBBABABA xxxxxxxxxxA
22
Again comparing and A B
AAAA xRTx ln1 20
BBBB xRTx ln1 20
This can be written in the form:
AAA aRT ln0
BBB aRT ln0
so that in the regular solution model:
2
01exp AA
A
AA x
RTx
p
pa
2
01exp BB
B
BB x
RTx
p
pa
Summarizing
Ideal Solution
ii xa
Regular Solution
21exp iii xRT
xa
How are the partial molar quantities related to the molar quantities ?
Consider :
BBAA dxdxdG
ABBdx
dG
Since xA + xB = 1BA dxdx
A
BAB dx
dG
and substituting for A from A
BBB dx
dGxG 1
And similarly
A BB
dGG x
dx
Also usingA A B BG x x
B
BBA x
xG
1
Graphical Interpretation
*
*** )()(BxxB
BBBA dX
dGxxGx
*
)1()()( ***
BxxBBBBB dx
dGxxGx
Given G as a function of xB as above, the chemical potential @ a composi-
tion xB* can be obtained graphically by extrapolating the tangent of the G
curve @ xB= xB* to xB= 0 and xB= 1
*B
B X
dG
dx
0 1
G (XB*)
ΔGmix
X*B
G
XB
A
A
B
B
Chemical Equilibrium
aA + bB + … xX + yY + …
A, B … reactantsX, Y … products
} standard states
a, b, …., x, y,…. Stoichiometric Coefficients
Equilibrium is defined by the condition
0 BAyx bayxGd
Since iii aRT ln0
0 0 0 0
y A BxdG x y a b
( ln ln ) ( ln ln ) 0x y A BRT x a y a RT a a b a
≣ standard free energy change /mole
0 ln lnx yX Ya bA B
a aRT RT K
a a
K is the equilibrium constant for the reaction.
Solving for
The equilibrium constant is defined by
When components are not in standard state:
bB
aA
yY
xX
aa
aaRT ln0
)exp(RT
K
Equilibrium in multiphase Solutions
Consider 2 phases containing the same component i in α and β
The component i has and activity aαi and aβ
i .
Imagine and infinitesimal amount of i is transferred from α to β so that
the compositions have not been altered.
The reaction is:
)()( ii aiai
The chemical potential of i in each phase is
lnoi i iRT a
lnoi i iRT a
i
i
a
aRTG ln if
ii aa => spontaneous (ΔG < 0)
Equilibrium is defined by ΔG = 0 or
ii aa
ii ;
In general for a multicomponent system with different phases
present, equilibrium is defined by:
Equal P & T for all phases
pA A A A
pB B B B
pC C C C
…
The free energy change for the reaction at const T, P is,
The Gibbs Phase Rule
Equilibrium for different phases, , , , …p in contact with one another is given by the conditions;
pp p p p A pT T T T B
pA A A A
pB B B B
pC C C C
…
C
Equilibrium will in general not be maintained if the parameters are arbi-trarily varied. The Gibbs phase rule restricts the manner in which the parameters can be varied such that equilibrium is maintained.
The composition of a given phase is set by the additional condition.
... 1P P P
A B Cx x x C - 1 composition variables per phase
C components present
p phases present (p-1) eqns. for each component
For each phase there are (C – 1) + 2 = C + 1 independent variables ordegrees of freedom.
CThe set of equations represent a system of coupled linear equations. There are ( P – 1) equations for each component and C components so we have (P – 1)(C+2) equations.
T, P
P (C +1) unknowns (P – 1)(C+2) equations
In order for a solution to these equations to exist, # unknowns # of equations
P (C +1) (P – 1)(C+2)
P C + 2
The Gibbs Phase Rule
P C + 2 For a system of C independent components not morethan C + 2 phases can co-exist in equilibrium.
Trivial Example: C = 1, P = 3 solid, liquid vapor
If P is less than C + 2 then C + 2 – P variables can take on arbitrary values(degrees of freedom) without disturbing equilibrium.
def. Thermodynamic degrees of freedom, f
2 0f C P Gibbs Phase Rule
The Gibbs Phase Rule
Geometrical Interpretation of Equilibrium in Multi-component Systems.
Consider a 2 phase binary : GpTxxGG BA ; ) , , ,(
AA BB } Equilibrium
x
x
x
10
G
xB →
ab
A A
B B
The intercepts of the common tangent to the free energy curve give the chemical potentials defining the heterogeneous equilibrium.
xxB 0
xxx B 1 Bxx
- single phase; a
- 2 phase; + field
@ T and P - single phase; b
Composition x* is in the 2 phase α + β field.Consider a simple rule of mixtures mass balance :
xfxfx *
fi is the fraction of alloy composed of i
1 ff
xfxfx )1(*
xx
xxf
*
xx
xxf
*
These formulas are analogous to mass balance for a lever with ful-crum @ x*. => “ Lever Rule”
Binary Phase Diagrams
xB →
A B
T1
G
S
l
xB →
A B
Tmp(A)
G
S
l
xB →
A B
T2
G Sl
xB →
G
A B
Tmp(B)
S
l
A and B complete miscibility in both solid and liquid
xB →
A B
T3
G
S
l
A B
T1
T2
T3
xB →x*
b
c
xs xl
At temp T2 x* is composed of some fl with composition c and fs at composition b:
* :s s l lx f x f x sb x
lc x
Lever Rule
sl
sl
sl
ls xx
xxf
xx
xxf
**
; Ag-AuSi-Ge
System with a miscibility gap
A B
T > Tc
G
xB → xB →
A B
T = Tc
G
xB →
A B
T << Tc
G
g h
G
xB →
A B
T < Tc
ef
2cTR
A B
T < T’c
T < <T’c
xB →
Tc
e f
g h+a a’’
• The miscibility gap is the region where the overall composition exceeds the
solubility limit.
• The solid solution a is most stable as a mixture of two phases a’ + a’’.
• Usually a, a’, and a’’ have the same crystal structure. Cu –Pb, Au-Ni, Fe-
Sn, Cr-W, NaCl-KCl, TiO2-SiO2.
G
T1
XB
Solid
Liquid
T2
a b c d
T3
fe
Negative Curvature
Negative Curvature
ab c
d
fe
a
+a a’’T3
T2
T1liquid
A BXB
Free energy curves and phase diagram for ∆Hsmix> ∆HL
mix= 0.
• The A and B atoms dislike each other.
• Note that the melting point of the alloy is less than that of either
of the pure phases.
xB →
A Ba’
a
liquid
Phase diagram for ΔHSmix <
ΔHlmix < 0
Phase diagram for ΔHSmix
<< ΔHlmix < < 0
Since ΔHSmix < 0, a maximum melting point mixture may appear.
Ordered AlloyFormation
B
liquid
xB →
A
+a b b+ g
a b
g
Ordered Alloy Formation
Eutectic Alloy; ΔHSmix >> ΔHl
mix > 0
A B
T1
Gsolid
l
xB → A B
T3
solid
l
lαa1
l+ a1
l+ αa2
a2
A B
T4
solidl
A B
T5
solid
l
A B
T3
T4
Tb
T2
T1
T5
xB →
T
TA
A B
T2
solid
l
la1
l+ a1
a1l+a1
l+a2
a2
a1a1+a2
a2
l
a1 a2
l+ a1
l+ a 2
a1+a2
• If Hsmix >> 0, the miscibility gap can extend into the liquid phase (T2, T3, T4)
resulting in a simple eutectic phase diagram. • A similar result can occur if the A and B components have a different crystal
structure.
A B
T2
l
α
β
l
α l+ α l+ β β
T4
l β
α
α βα+ β
A B
A B
T1
Gl
xB → β
β
α
α l+ α lA B
T3
lβ
α
α l+ α l+ β β
A B
α
l+ α
l+ β
α +β
β
T2
T3
Tb
T1
T4
xB →
T
TAl
Eutectic phase diagram where each solid phase has a different crystal structure.
A B
T1
liquid
βα
γ
A B
T2
βα
γ
α
α +β+l
l
l
A B
T3
βα
γ
α +β
l
lα β β+l
A B
T4
βα
α +β
l
l+γα β β+l
γ
l
A B
T5
βα
α +β
α β β+l+ γ
l
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
A B
T3T4
T2
T1
T5
Tl+α
liquid
α +β
β
α
β+γγ
l+ γ
l+β
P Q
The derivation of a complex phase diagram showing the formation of stable
intermediate phases(β). At a composition indicated by the red line, just above
T2, (green line) a solid at composition P is in equilibrium with a liquid at
composition Q. At a temperature just below T2 ( not shown ) the two phases
in equilibrium are solid b and liquid . The following peritectic reaction oc-
curs on cooling: l + α → β