“Rietveld refinement is one of those few fields of ...
Transcript of “Rietveld refinement is one of those few fields of ...
Neutron Rietveld RefinementR.B. Von DreeleAPS/IPNSArgonne National LaboratoryArgonne, Il [email protected]
“Rietveld refinement is one of those few fields of intellectual endeavor wherein the more one does it, the less one understands.” (Sue Kesson)
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Powder - polycrystalline mass
All orientations of crystallites possible
Sample: 1cc powder of 10μm crystallites - 109 particlesif 1μm crystallites - 1012
particles
Single crystal reciprocal lattice - smeared into spherical shells- broadened by instrumental & sample effects
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Neutron Diffractometers - Constant Wavelength
Reactor
Sample
α1
Detector (can be many)Debye Scherrer geometry
Monochromator
2ΘM - fixed
2Θ - varied
α3
0.8 ≤ λ ≤ 5.0Å
λ = 2dsinΘ
Vary Θ
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Neutron Diffractometers - Time-of-Flight
Sample
Detectorbank
L1 ~ 1-2m
Pulsedsource
9 ≤ Lo ≤ 100m
2Θ - fixed
λ = 2dsinΘVary λ (Τ)
Φ
Also Debye Scherrer
T=Cd+Ad2+Z
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Reactor Spectrum
Inte
nsity
0.0 2.0 4.0 6.0 8.0 10.0
λ, ÅTypical monochromator cut at 1.54 Å
T = 300K
0 2 4 6 8 10
Incident Spectrum
log(
I)
Wavelength, Å
Maxwellianpart
Epi-thermalpart
Useful band
TOFCW
Source comparison: CW vs TOF
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Rietveld refinement – multiparameter curve fitting
Exact overlaps - symmetry
Incomplete overlaps
Io
∑∑ −
= 2
2
o
cowp wI
)Iw(IR
Residual:
Rietveld minimize ∑ −= 2)( coR IIwM
Ic
⎥⎦
⎤⎢⎣
⎡+Δ= ∑
hbhhhhhic IPLmFkII )(2
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Least Squares Theory - simple
and a function:
then the best estimate of the values pi is found by minimizing
This is done by setting the derivative to zero
Results in n “normal” equations (one for each variable) - solve for pi
)...,,,( 321 nc ppppgG =
Given a set of observations: Go
2)( co GGwM −= ∑
0)( =∂∂
−∑j
cco p
GGGw
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Least Squares Theory - continued
Problem - g(pi) is nonlinear & transcendental (sin, cos, etc.) for crystallography - so can’t solve directlyExpand g(pi) as Taylor series & toss high order terms
∑ Δ∂∂
+=i
ii
cicic p
pIaIpI )()(
Substitute above
ai - initial values of piΔpi = pi - ai (shift)
)(0 icoj
c
ii
i
c aIIIpIp
pIIw −=Δ=
∂∂
⎥⎦
⎤⎢⎣
⎡Δ
∂∂
−Δ∑ ∑
Normal equations - one for each Δpi; outer sum over observationsSolve for Δpi - shifts of parameters, NOT values
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Least Squares Theory - continued
Rearrange
111 pIIwp
pI
pIw c
i
n
i i
cc
∂∂
Δ=⎟⎟⎠
⎞⎜⎜⎝
⎛Δ
∂∂
∂∂ ∑∑∑
=...
n
ci
n
i i
c
n
c
pIIwp
pI
pIw
∂∂
Δ=⎟⎟⎠
⎞⎜⎜⎝
⎛Δ
∂∂
∂∂ ∑∑∑
=1
Matrix form: Ax=v
i
cijj
j
c
i
cji p
IIwvpxpI
pIwa
∂∂
Δ=Δ=∂∂
∂∂
= ∑∑ )(,
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Least Squares Theory - continued
Matrix equation Ax=vSolve x = A-1v = Bv; B = A-1
This gives set of Δpi to apply to “old” set of ai
repeat until all xi~0 (i.e. no more shifts)
Rietveld refinement - this process applied to powder profiles – curve fitting!Note: Starting model REQUIREDIo – observed powder profile (including background)Ic - model function for the powder profile
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Least Squares Theory - continued
Error estimates (mostly from W.C. Hamilton)Given observations n > m parameterswith distributions that have finite 2nd moments (no need to be “normal”)Then LS gives parameter estimates (shifts in our case) with the minimum variance in any linear combinationThe error estimates (“esd’s” or “su’s”) are
mnIIwb coii
i −−
=χχ
=σ ∑ 22
2)(
bii - diagonal elements of the inverted A matrixNote: There is little justification for additional scaling of the σi
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Rietveld refinement in GSAS - minimization function ( )
( )( )( )( )( )( )( )
2
2
2
4
2
2
2
2
2
)( ciiR
cioiix
cioiih
cioiiv
ciip
cioiit
cioiid
cioiia
cioii
Rwf
xxwf
hhwf
vvwf
pwf
ttwf
ddwf
aawf
IIwM
−+
−+
−+
−+
−+
−+
−+
−+
−=
∑∑∑∑∑∑∑∑
∑ Powder profiles (Rietveld)Bond anglesBond distancesTorsion anglesPlane RMS displacementsvan der Waals distancesHydrogen bondsChiral volumes“φ/ψ or χ1/χ2” pseudopotential
wi = 1/σ2 weighting factorfx - weight multipliers (typically 0.1-3)
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Model - represent each profile intensity
Ii - incident intensity - variable for neutron TOFkh - scale factor for particular phase
Fh2 - structure factor for particular reflection
mh - multiplicity of the reflection
Lh - correction factors on intensity
P(Δh) - peak shape functionMinimize thus need all
⎥⎦
⎤⎢⎣
⎡+Δ= ∑
hbhhhhhic IPLmFkII )(2
2co )II(w∑ −
i
cpI
∂∂
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Profile Functions - Basics
Gaussian profile - generally instrumental origin
Lorentzian profile - largely sample effect
⎥⎦
⎤⎢⎣
⎡Γ
Δ−Γπ
=ΓΔ 2
2
2)T(2ln4exp2ln4),T(G
ΔT = Treflection-Tprofile
2T21
12),T(L⎟⎠⎞
⎜⎝⎛
γΔ+
πγ=γΔ
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Constant Wavelength Profile Function - GSAS
Thompson, Cox & Hastings (with modifications)
Pseudo-Voigt ),T(G)1(),T(L)T(F ΓΔη−+ΓΔη=Δ
Mixing coefficient j3
1jj )(k∑ Γ
γ=η=
FWHM parameter 55
1i
ii5gic∑ γΓ=Γ
=
−
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CW Function Coefficients - GSAS
Asymmetry
Sample shift
Sample transparency
Gaussian profile
Lorentzian profile
As or H/L & S/L
36000RSs sπ−
=
seff RT
9000π
−=μ
Θ++Θ+Θ=Γ 2
22g cos
PWtanVtanU
Θ+Θ
=γ tanYcos
X
(plus anisotropic broadening terms)
Microstrain Broadening – simple model
a*
b*
tconsdd tan=
Δ
ΘΔΘ=Δ
=Δ cot
**
dd
dd
ΘΔ
=ΘΔ tan22d
d
Lorentzian term - usual effect ""180
%100 LYS π=
Gaussian - Remove instrumental part
""180
%100 GUS Δπ
=
Crystallite Size Broadening
a*
b*
Δd*=constant
dcot
dd*d 2
ΘΔΘ=
Δ=Δ
λΘΘΘΔ
=sincot2
ΘΔλ
=ΘΔcosd
d2 2
Lorentzian term - usualK - Scherrer const. "LX"
K180pπ
λ=
Gaussian term - rareparticles same size? "GP"
K180pπ
λ=
Neutron TOF Neutron Profile FunctionVon Dreele, Jorgenson & Windsor (with modifications)Convolution of paired exponentials and a Gaussian
where u, v, y & z are functions of profile coefficients
exponential rise
exponential decay
Gaussian variance - also anisotropic terms
H (ΔT) = N [eu erfc(y) + ev erfc(z)]
α = αo + α1/d
β = β0 + β1/d4
σ 2 = σ 02 + σ 1
2d2
+ σ 22d
4+ (σ 1e
2 d2
+ σ 2e2 d
4)c o s 2φ
peak displacement - macrostress
ΔΤ = (Τ−Τp,h) - εid - εadcosφ - εAd(h
2+k
2+l
2)2
(hk)2+(hl)
2+(kl)
2
microstrain
macrostrain
eατ e-βτ
⊗
G(ΔT,σ)
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Microstrain broadening – physical model
Stephens, P.W. (1999). J. Appl. Cryst. 32, 281-289.Also see Popa, N. (1998). J. Appl. Cryst. 31, 176-180.
Model – elastic deformation of crystallites
hkhlkllkhMd hkl
hkl654
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22
212
1 αααααα +++++==
d-spacing expression
( ) ∑ ∂∂
∂∂
=ji ji
ijhklMMCM
,
2
αασ
Broadening – variance in Mhkl
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hkMhlMklMlMkMhM=
∂∂
=∂∂
=∂∂
=∂∂
=∂∂
=∂∂
654
2
3
2
2
2
1
,,,,,αααααα
⎥⎥⎥⎥⎥⎥⎥⎥
⎦
⎤
⎢⎢⎢⎢⎢⎢⎢⎢
⎣
⎡
=∂∂
∂∂
2222233
2222323
2222332
23342222
32322422
33222224
khklhlhkhklhkkhklhlhhklhllhklhlhkhkllkkllkklh
hklhlklllklhhklhklklkkkh
khlhklhlhkhh
MM
ji αα
Microstrain broadening - continued
Terms in variance
Substitute – note similar terms in matrix
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( ) 42 =++= ∑ LKH,lkhSMHKL
LKHHKLhklσ
( ) ( )( )( )2
1122
1212
211
3013
3301
3130
3031
3103
3310
22022
22202
22220
4004
4040
4400
2
42
3
hklSlhkSklhS
klSlhShkSlkShlSkhS
lkSlhSkhSlSkShSM hkl
++
++++++
++++++=σ
Microstrain broadening - continued
Broadening – as variance
General expression – triclinic – 15 terms
Symmetry effects – monoclinic (b unique) – 9 terms( )
( ) lhkShkSlhS
lkSkhSlhSlSkShSM hkl2
1213
1033
301
22022
22220
22202
4004
4040
4400
2
42
)(33
++
++++++=σ
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Na benzoate test Hist 1Lambda 1.1475 A, L-S cycle 167 Obsd. and Diff. Profiles
2-Theta, deg
Counts
X10E 1 2.0 2.1 2.2 2.3 2.4 2.5 2.6 2.7 2.8 2.9 3.0
X10E 4
.0
2.0
4.0
6.0
Unusual line broadening effects
Sharp lines
Broad lines
Seeming inconsistency in line broadening- hkl dependent
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Na parahydroxybenzoate
Unusual micostrain effects - peak broadening
Directional dependence -Lattice defects?
XY
Z
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Exploded view of HIPPO DiffractometerSample chamber - 29.13” opening &32” from rim to beam center
150deg panels
10deg panels
40 & 20deg panels
90deg panels
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Neutron TOF Diffractometer - multiple detectors
Incident beam
150° detectors
90° detectors
40° detectors
Sample position
Fixed 2Θ, TOF ∝ λ ∝ d
E.g. HIPD & HIPPOat LANSCE;
POWGEN3 at SNS
High to low scattering anglesλ = 0.4Å to 10Å; d = 0.2Å to 30ÅΔd/d = 0.3% to 5%(other instr. <0.1%)
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Random powder - all crystallite orientations equally probable - flat pole figure
Crystallites oriented along wire axis - pole figure peaked in center and at the rim (100’s are 90ºapart)
Orientation Distribution Function - probability function for texture
(100) wire texture(100) random texture
What is texture? “Interesting Preferred Orientation”
Pole figure - stereographic projection of a crystal axis down some sample direction
Loose powder
Metal wire
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Texture - measurement by diffraction
Debye-Scherrer cones •uneven intensity due to texture •also different pattern of unevenness for different hkl’s•Intensity pattern changes as sample is turned
Non-random crystallite orientations in sample
Incident beamx-rays or neutrons
Sample(111)
(200)
(220)
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• Projection of orientation distribution function for chosen reflection (h) and sample direction (y)
• K - symmetrized spherical harmonics - account for sample & crystal symmetry
• “Pole figure” - variation of single reflection intensity as fxn. of sample orientation - fixed h
• “Inverse pole figure” - modification of all reflection intensities by sample texture - fixed y - Ideally suited for neutron TOF diffraction
• Rietveld refinement of coefficients, Clmn, and 3
orientation angles - sample alignment
Texture effect on reflection intensity - Rietveld model
)()(12
4),(0
yKhKCl
yhA nl
ml
l
lm
l
ln
mnl
l∑ ∑∑
−= −=
∞
= +=
π
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, , y
D-spacing, A
Coun
ts/mu
sec.
1.0 2.0 3.0 4.0
X10E
2
-2.0
.0
2.
0
4.0
6.
0
y
D-spacing, A
Coun
ts/mu
sec.
1.0 2.0 3.0 4.0 5.0 6.0
X10E
3
.0
1.0
2.
0
3.0
4.
0
• Two patterns from different sample orientations and different detector banks
• Very different reflection intensities from texture
• Any one pattern useless for Rietveld due to texture variation
• But all 52 combined in single LS gives texture and crystal structure
Example: CaCO3 calcite - “Standard Round Robin Sample”[H.R. Wenk, J. Appl. Cryst.(1991). 24, 920-927]
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calcite 0 0 6 Pole Figure - Equal Area
C
1
2
3
4
5
6
7
8
9
10
11
12 13 14
15
16
17
18
19
20
21
22
23
24 25 26
27 28
29
30
31
32
33
34
35
36
37 38
39
40
41
42
43
44
45
46
47
48
49 50
51
52
006 pole figure for calcite -shows sampling orientations
Other pole figures generated from harmonic coefficients
Match those from neutron measurements given by Wenk
Calcite pole figures - compute from Clmn
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Crystal structure of calcite - refined with texture
1/2 calcite unit cell
Result – matches “best” single crystal X-ray result