Microstructure and Texture Analysis: Theory and Case Studies
Transcript of Microstructure and Texture Analysis: Theory and Case Studies
D. Chateigner, and the SOLSA Consortium Normandie Université
Microstructure and Texture Analysis: Theory and Case Studies
Trento, Italy, 26-30th Nov. 2018
Structure |Fh|2Φ,L
Texture f(g)Φ,L
Residual Stress <Cijkl(g)>Φ,L
Real samples Layered samples
thicknesses roughnesses ρ(z)…
Phase SΦ,L
defects (0D .. nD) broadening asymmetry
X-ray scattering “sees”
Phase ID
Raman, IR, XRF
Element ID
XRF
∫ϕ
ϕϕ=~
Sh~d)~,g(f)(P y
Rietveld: extended to lots of spectra
∑∑ ∑= =Φ
ΦΦΦΦΦΦ
ΦΦ
ηθηθηθΩθν
+ηθ=ηθLN
1i
N
1ihh
2hh
h2c
i0bc ),,(A),,(P),,(Fj)(Lp
VI),,(y),,(y SSSSS yyyyy
Texture: E-WIMV, components, Harmonics, Exp. Harmonics …
Strain-Stress:
( ) geogeo1
N
1m
1m
N
1mm
1N
1mm
1geo CSSSSS m
mm ====⎥⎥⎦
⎤
⎢⎢⎣
⎡= −
=
ν−
=
ν−−
=
ν− ∏∏∏
Geometric mean, Voigt, Reuss, Hill …
Layering:
AiΦ =ν iΦ sinθi sinθoµ i (sinθi + sinθo )
1− e−µ iτ iW{ } e−µkτ kWk<i∏
W =1
sinθi+
1sinθo
Stacks, coatings, multilayers …
Popa, Delft: Crystallite sizes, shapes, microstrains, distributions 0D-3D defects
Line Broadening:
X-Ray Reflectivity (specular):
Matrix, Parrat, DWBA, EDP …
X-Ray Fluorescence/GiXRF:
De Boer
Electron Diffraction Patterns:
2-waves Blackman
Microstructure (Line Broadening) Analysis Line Broadening causes Instrumental broadening Main contributions
Evolution of FWHM with x Extraction of the sample contribution Peak profiles Constant wavelengths
TOF neutrons Calibration of the instrumental contribution Back on diffraction expression Simple peak broadening characterization
Full-Width at Half-Maximum Integral breadth
Crystallite’s size effect Accounts for instrument in simple cases What is size?
Microstrains effect Williamson-Hall analysis Whole-pattern analysis Warren-Averbach-Bertaut analysis Anisotropic sizes and microstrains Examples
Line Broadening causes
- Instrumental broadening
- Finite size of the crystals acts like a Fourier truncation: size broadening
- Imperfection of the periodicity due to dh variations inside crystals: microstrain broadening
- Generally: 0D, 1D, 2D, 3D defects
- All quantities are average values over the probed volume electrons, x-rays, neutrons: complementary distributions: mean values depend on distributions’ shapes
Irradiated Fluorapatites
Instrumental broadening
∫+∞
∞−
−+=+⊗= dy)yx(g)y(f)x(b)x(b)x(g)x(f)x(h
)x(g)x(g)x(g g⊗= λ
Energy dispersion
Geometrical aberrations
Measured profile Sample contribution Background
0,0 0,2 0,4 0,6 0,8 1,0
0
20
40
60
80
100
Intensity
x
Extraction of the sample contribution Single peak
∑∑
=+
kj
)n(jkj
'kki)n(
i)1n(
ifg
hgff
f(x) obtained by deconvolution from h(x) [g(x) removal]
Stokes (1948): direct Fourier extraction Delhez et al. (1980): biases due to f(x) < g(x) and background
Richardson (1972): Bayesian deconvolution by iteration
Peak Profiles
⎟⎟
⎠
⎞
⎜⎜
⎝
⎛ θ−θ−
π=θ
2k
2ki
k
0i
H
)22(2ln4exp
H
2lnI2)2(GGauss:
Lorentz: m
2
k
kik
0i
H22
C1
1HCI
)2(L
⎟⎟⎟⎟⎟⎟
⎠
⎞
⎜⎜⎜⎜⎜⎜
⎝
⎛
⎟⎟⎠
⎞⎜⎜⎝
⎛ θ−θ+
π=θ
m: Lorentzian order, [0,∞[ m = 1 "pure" Lorentzian function m = 1.5 "intermediate" Lorentzian function [Malmros et Thomas 1977] m = 2.0 "modified" Lorentzian function [Sonneveld et Visser 1975], Pearson VII
Constant wavelengths
V(x) = L(x) ⊗ G(x) Voigt:
Pseudo-Voigt: η)G(x)(1x)L(ηx)(pV −+=
η: mixing parameter
12
k
ki1
2
0k H
xxCAsAs11L
HQ)x(PVII
−
⎟⎟⎟
⎠
⎞
⎜⎜⎜
⎝
⎛
⎥⎥
⎦
⎤
⎢⎢
⎣
⎡
⎟⎟⎠
⎞⎜⎜⎝
⎛ −⎟⎠
⎞⎜⎝
⎛ ++=Split Pearson VII:
( )12
k
ki2
20
k HxxCAs11H
HQ)x(PVII
−
⎟⎟⎟
⎠
⎞
⎜⎜⎜
⎝
⎛
⎥⎥
⎦
⎤
⎢⎢
⎣
⎡
⎟⎟⎠
⎞⎜⎜⎝
⎛ −++=
xi ≤ xk
xi > xk
12C 0L/11 −= 12C 0H/12 −=
k2
kk θsin/(3)Assinθ/(2)As(1)As)θ(As ++=
k2
0k00k0 θsin/(3)Lsinθ/(2)L(1)L)θ(L ++=
k2
0k00k0 θsin/(3)Hsinθ/(2)H(1)H)(θH ++=
Variable, parameterised Pseudo-Voigts, anisotropic …
TOF neutrons
∫+∞
∞−
−=⊗= t)E(t)dtG(xE(x)G(x)GE(x)h
βt-
hαt
tfor teβ)2(α
αβE(t)
tfor teβ)2(α
αβE(t)
>+
=
<+
=
Convolved Gaussian and rising and falling exponentials:
α and β: account for rising and falling exponential behaviours of the neutron pulse
∫+∞
∞−
−=⊗= t)E(t)dtpV(xE(x)pV(x)pVE(x)
Convolved pV and back-to-back exponentials:
0for teβα
αβE(t)
0for teβα
αβE(t)
βt-
αt
>+
=
≤+
=
Moderator pulse-shaped function (Ikeda et Carpenter 1985):
moderator theof constantsdecay :,
leakageneutron fast et2α
(t)S
leakageneutron slow Re(t)R)(1(t)R
with(t)R(t)S(t)I
αt23
k
βtk
kkk
βα
=
+δ−=
⊗=
−
−
Convolved pV and Ikeda-Carpenter …
Calibration of the instrument contribution
LaB6 NIST srm660b: flat-sample reflection geometry
FWHM (ω, χ, 2θ …) 2θ shift gaussianity asymmetry misalignments ...
0 20 40 60 80 100 1200.0
0.2
0.4
0.6
0.8
1.0
1.2
1.4FW
HM
(2θ°
)
2θ(°)
D1B INEL CPS120
FWHM2 = U tan2θ + V tanθ + W (Thermal neutrons, Caglioti et al. 1958)
Evolution of the FWHM versus x: Laboratory X-rays and thermal neutrons
slits) ng(collimati W .const)2(
)dispersion(energy U tan2)2(
G
L
!
!
=θΔ
θλ
λΔ=θΔ (Lab. X-rays, Klug et Alexander 1974)
Accounts for instrument in simple cases Considering Gauss functions: )x(g)x(f)x(h ⊗=
)]x(g[FT)]x(f[FT)]x(h[FT =
]texp[)0(H)t(H ]/xexp[)0(h)x(h
]texp[)0(G)t(G ]/xexp[)0(g)x(g
]texp[)0(F)t(F ]/xexp[)0(f)x(f
2h
22h
2
2g
22g
2
2f
22f
2
βπ−=⇒βπ−=
βπ−=⇒βπ−=
βπ−=⇒βπ−=
spacedirect t ), (e.g. space reciprocal x ∈θ∈
]texp[)0(G]texp[)0(F ]texp[)0(H 2g
22f
22h
2 βπ−βπ−⇒βπ−
2g
2f
2h β+β=β
Lorentz functions: gfh ω+ω=ω
Gauss functions:
]h.csin[]h.c)1q(sin[
]h.bsin[]h.b)1p(sin[
]h.asin[]h.a)1n(sin[)h(T
)h(TFA
cba
cbahh
!!
!!!!!!
!!
!!!
!
!!!
!!!!!
π
+π
π
+π
π
+π=
=
directions c ,b ,a in the periods ofnumber :q p, ,n
function ceinterferen :)h(T
factor structure :F
amplitude scattered :A
cba
h
h
!!!
!!!!
!
!
Back on diffraction expression
0,0 0,2 0,4 0,6 0,8 1,0
0
20
40
60
80
100
H(α)
α
][sin])1n([sin)(H 2
2
πα
α+π=α
0,0 0,2 0,4 0,6 0,8 1,0
0
2000
4000
6000
8000
10000
H(α)
α
0,0 0,2 0,4 0,6 0,8 1,0
0
2
4
6
8
10
H(α)
α
n=9
n=2
n=99
(n+1)2
α+1/(n+1)
lh.ckh.bhh.a
:crystal infinite=
=
=
!!
!!!!
Simple peak broadening characterization
0,0 0,2 0,4 0,6 0,8 1,0
0
20
40
60
80
100
Intensity
θ(°)
ωω: Full-Width at Half-Maximum
θi θf
max2 I
d)(If
i
∫θ
θθ
θθ
=ββ: Integral Breadth (von Laue 1926)
θ0
Experimentally: β > ω
Crystallite’s size-shape effect
Scherrer formula (1918):
0h cos
KR
θω
λ=!
hR!
h!
K= 0.888 (Scherrer constant)
Depends on crystal shapes (Langford)
Since β > ω, Rh(β) < Rh(ω)
'Rh!
'h!
Scherrer analysis: Δθ
Δh
21
G0GIIIG ]H[H
1.8πε −=
]H[H1.8πε L0L
IIIL −=
Scherrer (1918)
Usually εL can be neglected (Delhez et al. 1993, Langford et al. 1993, Lutterotti et al. 1994)
cotanθβε
cotanθ4
βε
III
III
εIIImaxG,
εIIIG
><
><
=
= Stokes et Wilson 1944
If broadening only from microstrains
Williamson-Hall analysis
λsinθε4
R1
λcosθ
LIII
Lh
h
h +=ω Hall (1949), Lorentz-like
broadening
22
GIII
2G
2
λsinθε16
R
1λcosθβ
⎟⎠
⎞⎜⎝
⎛+=⎟⎠
⎞⎜⎝
⎛h
h
h Gauss-like broadening
λcosθhω
λsinθ
1LR −
h
LIIIε4 h
hkl 2h2k2l h’k’l’ 2h’2k’2l’
After Scherrer analysis …
Williamson-Hall (1949)
Warren-Averback-Bertaut (1952)
Whole-Pattern analysis: Langford (1978), de Keijser (1982), Balzar et Ledbetter (1982) …
But deconvolution of contributions (Stokes 1948) !
Rietveld (1969): convolution !
More infos: http://www.ecole.ensicaen.fr/~chateign/formation/course/Classical_Microstructure.pdf
More elegant, mandatory for whole-pattern: Stokes deconvolution
Warren-Averbach-Bertaut analysis
Let construct a crystal as an integral of column-heights of the crystals:
( ) 1(R)dR with (R)dRmRh(m)0
mR=−= ∫∫
∞
≥DD
h(m): volume formed by all the columns of unit-base m: integer coordinate of the columns D(R): column-size distribution function
∫∞
=∂
∂
m(R)dR
mh(m)- D Fraction of columns of lengths R larger than m
(R)mh(m)- 2
2D=
∂
∂ Column-size distribution function
More elegant, mandatory for whole-pattern: Stokes deconvolution Bertaut-Warren-Averbach treatment, e.g. for a 00l peak:
( )∑ −π=
h
h
hhL
ssL2i-L 0eCΩ D
LSLL
RLL CCCCC ==
ε IIIhh
AS(L)
L
<R>
1
σD (L)
dL
AdL and (L)dL
Ad
R1
dLdA
Sv2
SL
2SA2
SL
2
F0L
SL
DD ==
=⎟⎟
⎠
⎞
⎜⎜
⎝
⎛
→
What is size (coherent domain) ?
⎟⎟⎟
⎠
⎞
⎜⎜⎜
⎝
⎛+==
θβ
λ=
θ2
h
2R
hh
2h
h2h
R
σ1R
R
R
cosR h
!!
!
!
!! !
Apparent linear size (Bertaut 1949)
3h
4h
Vh2h
3h
Ah
2h2
h
hh
R
RR ;
R
RR
moment second :dS
dSRR
mean arithmetic :dS
dSRR
!
!!
!
!!
!!
!!
==
=
=
∫∫∫∫
If crystals with same sizes and shapes:
VhAhh R RR !!! ==
Recognised that β2θ overestimates Rh
∑ ∑Φ
=ΦΦΦ
=ΦΦΦΦ Ω+=
N
1iki
2k
K
Kkkkkibic AFPLpjSyy
1
Whole-Pattern (Rietveld) analysis
n
nn G
HF =
kiΦΩ Includes f(x) and g(x), but from Fourier deconvolution (Stokes 1948), extraction of f(x) is possible:
⎥⎥⎦
⎤
⎢⎢⎣
⎡⎟⎟⎠
⎞⎜⎜⎝
⎛
πβ
β+
β
π
β
β=
G
L
GLi
xerfiRe)0(y)x(y
And, assuming Voigt profiles (Langford 1978, De Keijser et al. 1982, Balzar et Ledbetter
1993, Balzar 1999 ), separation of integral breadths are made is possible:
2gG
2hG
2fG
gLhLfL
β−β=β
β−β=β
Microstrains effect
λ=θsind2 h! 0dsin2cosd2 hh =∂θ+θ∂θ !!
h
hdd
tan !
!∂θ=θ∂ θε=ω tanIII
hh!!
IIIε
εIIε
Iε
r.m.s. d
d
h
hIIIh !
!!
∂=ε
Crystallite sizes, shapes, µstrains, distributions
X-rays
ω
(111)
(111)
<111>
X-rays
ω
(111)
(111)
<Rh> = R0 + R1P20(x) + R2P2
1(x)cosϕ + R3P21(x)sinϕ + R4P2
2(x)cos2ϕ + R5P22(x)sin2ϕ +
...<εh2>Eh4 = E1h4 + E2k4 + E3ℓ4 + 2E4h2k2 + 2E5ℓ2k2 + 2E6h2ℓ2 + 4E7h3k + 4E8h3ℓ + 4E9k3h +
4E10k3ℓ + 4E11ℓ3h + 4E12ℓ3k + 4E13h2kℓ + 4E14k2hℓ + 4E15ℓ2kh
Popa Line Broadening
• Texture helps the "real" mean shape determination
∑∑==
ϕχ=ℓ
ℓℓℓ
"
0m
mmL
0h ),(KRR
Symmetrised spherical harmonics
)msin()(cosP)mcos()(cosP),(K mmm ϕχ+ϕχ=ϕχ ℓℓℓ
R0 R0, R1 < 0 R0, R1 > 0
R0, R6 > 0 R0, R2 and R6 > 0 R0, R6 < 0
R0, R4 > 0 R0, R1 > 0 R0, R1 < 0
m3m 6/m
1
Crystallite size (Å) along
Film thickness 10nm 15nm 20nm 25nm 35nm 40nm
[111] 176 153 725 254 343 379 [200] 64 103 457 173 321 386 [202] 148 140 658 234 337 381
10 nm 15 nm 20 nm
25 nm 35 nm 40 nm
Gold thin films
EMT nanocrystalline zeolite
Ng, Chateigner, Valtchev, Mintova: Science 335 (2012) 70
New active Li–Mn–O compound for high energy density Li-ion batteries
Freire, Kosovab, Jordy, Chateigner, Lebedev, Maignan, Pralong: Nature Mat. 15 (2016) 173
Rock-salt-type nanostructured material: shows a discharge capacity of 355 mAh/g