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4-1
C H A P T E R 4
C R Y S T A L S T R U C T U R E S
4.1 ATOMIC ARRANGEMENTS
4.2 LATTICES AND UNIT CELLS 4.2.1 Unit Cel l s in Space
Fig. 4.5-2 Locations of the interstitial sites in FCC, BCC and HCP structures.
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4.6 CRYSTALLOGRAPHIC DIRECTIONS AND PLANES
Some physical and mechanical material properties vary
with the direction or plane within a crystal in which they
are measured. Miller Indices provide a convenient system
of describing points, directions and planes in crystals.
4.6.1 Coordinates of Points
• It is customary to use the right-hand coordinate system.
• The most common orientation is to align the coordinate
axes with the edges of the unit cell, putting the origin at
one corner of the cell.
• Each lattice point is defined by u, v, w, which correspond
to fractions of the lattice parameters, a, b, c.
Fig. 4.6-1 Coordinates of some points
in a unit cell. Note that coordinate axes are not necessarily perpendicular to one another and lattice parameters
may not be the same length. The choice of origin is arbitrary.
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4.6.2 Indices of Directions Procedure for finding Miller indices of directions: 1. Determine the coordinates of 2 points that lie in the
direction of interest. 2. Subtract coordinates of ‘start’ point from ‘end’ point. 3. Clear fractions and/or reduce to lowest integers. 4. Write the indices in square brackets [ ] without commas.
Negative integer values are indicated by placing a bar over the integer. (Fig. 4.6-3)
Fig. 4.6-2 Some common directions in a cubic unit cell.
Worked Example (Fig. 4.6-3) 1. Coordinates of ‘end’ and ‘start’
points: 0,0,1; 12, 1, 0.
2. ‘End’ - ‘start’ coordinates:
(0 - 12), (0 - 1), (1 - 0) = -
12
, -1, 1
3. Clear fractions:
2(- 12
, -1, 1) = -1, -2, 2
4. Miller index: [ 1 2 2]
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4.6.3 Families of Directions
• Certain directions in a unit cell, e.g. the cube edges, have
identical atomic arrangements. Their Miller indices are
different because of the choice of origin and axes (Fig. 4.6-4).
These directions are said to be symmetrically equivalent.
Fig. 4.6-4 Symmetrically equivalent directions in the <100> family.
• Equivalent directions that are related by symmetry may be
grouped as a family of directions. 'Members' in the same
family share the same set of Miller indices, but in different
permutations, including negative indices (Fig. 4.6-4).
• The family is represented by the Miller indices of one
family ‘member’, but enclosed in angle brackets <u v w>. It
is customary to choose one of the positive indices.
• In cubic systems, the directions along the cube edges
belong to the same family of <100> directions. Face
diagonals form a different family, <110>, and body
diagonals yet another family, <111>.
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4.6.4 Hexagonal Crystals (Miller-Bravais Indices)
• Due to the hexagonal geometry, equivalent directions will
not have the same set of Miller indices. To reflect the
symmetry of hexagonal systems, a 4-axis Miller-Bravais
coordinate system may be used instead (Fig. 4.6-5).
Fig. 4.6-5 3- and 4-axis coordinate systems for hexagonal crystals. Since only 3 axes are
required to define any 3D geometry, the extra axis, a3, in the basal plane is actually redundant; the 3rd index, t , in the Miller-Bravais system [uvtw],
is thus a function of u and v, such that t = -(u + v).
• For directions in hexagonal system, first find Miller indices
(Sec. 4.6-2), then convert to Miller-Bravais indices as follows:
• Miller to Miller-Bravais:
[u’ v’ w’] ! [uvtw]
u =
n3 (2u’ - v’)
v =
n3 (2v’ - u’)
t = -
n3 (u’ + v’)
w = w’
• Miller-Bravais to Miller:
[uvtw] ! [u’ v’ w’]
u’ = u - t
v’ = v - t
w’ = w
where n is the integer required to clear fractions and/or reduce to lowest integers
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4.6.5 Indices of Planes Procedure for finding Miller indices of planes:
1. Find the coordinates of the points where the plane
intercepts the 3 axes. If the plane passes through the
origin, shift the origin of the coordinate system.
2. Take reciprocals of these intercepts.
3. Clear fractions but do not reduce to lowest integers.
4. Write the indices in round brackets ( ) without commas.
Negative integer values are indicated by placing a bar
over the integer. (Fig. 4.6-6)
Worked example (Fig. 4.6-6)
1. Plane passes through origin, so
shift axes to x’, y’, z’.
Intercepts: x = -1, y = 1, z = "
2. Reciprocals:
1x = -1,
1y
= 1, 1z
= 0
3. No fractions to clear.
4. Miller indices: ( 1 10).
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4.6.6 Families of Planes
• Planes that contain identical atomic arrangements in a unit
cell and are related by symmetry are equivalent.
• A family of equivalent planes share the same set of Miller
indices. The family is expressed by enclosing the Miller
indices of one ‘member’ in braces, {h k l}.
Fig. 4.6-7 The family of {110} planes contains (110) (101) (011) ( 11 0) ( 101 ) ( 01 1 ).
Fig. 4.6-8 Some planes in a cubic unit cell.
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4.6.7 Planes in Hexagonal Crystals
• In order that equivalent planes have the same indices, the
4-axis Miller-Bravais coordinate system may be used.
• Miller-Bravais indices for planes are determined using the
same procedure as in 3-index Miller systems (Sec. 4.6-1) (no
formulae required), except that 4 intercepts are found,
giving indices of the form (h k i l).
Worked Example (Fig. 4.6-9)
Reciprocals of intercepts for 4-axis Miller-Bravais system Miller Indices
• Note that with only 3 axes, Miller indices are different even
though the planes are equivalent. The 4-index Miller-
Bravais notation yields similar indices for equivalent planes.
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4.7 CRYSTALLINE MATERIALS
• In a single crystal, the same orientation and alignment of
unit cells is maintained throughout the entire crystal.
• Most materials are polycrystalline: their structures are
composed of many small crystals (grains) with identical
structures but different orientations (Fig. 4.7-1).
Fig. 4.7-1 The solidification of a polycrystalline material.
• Grain boundaries are the
interfaces where grains of
different orientations meet
(Fig. 4.7-2). Single crystals do
not contain grain boundaries.
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• The absence of grain boundaries in single crystals impart
unique properties but such crystals are extremely difficult
to grow, requiring carefully controlled conditions, which
are expensive. Single crystals are essential to some
applications; e.g. semiconductors and jet turbine blades,
piezoelectric transducers.
• Besides the absence of grain boundaries, single crystals
exhibit directionality in properties, such as magnetism, electrical conductivity and elastic modulus and creep resistance, which depend on the crystallographic direction of measurement. This directionality is called anisotropy.
• The random orientation of individual grains in a
polycrystalline material means that measured properties are independent of crystallographic direction. Such materials are said to be isotropic.
• Grain boundaries are disordered regions of atomic
mismatch where atoms are displaced from their
equilibrium positions (Fig. 4.4-1) and there are improper
coordination numbers (Sec. 4.2.2) across the boundaries.
Atoms at grain boundaries hence possess higher energy.
• This interfacial energy makes grain boundaries
preferential sites for chemical reactions and other chemical
changes.
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• Therefore, grain boundaries are attacked more aggressively
by chemical etchants. Under a microscope, the more
deeply etched grain boundaries scatter more light, and
appear darker (Figs. 4.7-3/4), thus revealing the microstructure.
This is the principle behind metallography.
Fig. 4.7-3 Observation of grains and grain boundaries in stainless steel sample. Note that different orientations of the grains result in differences in reflection.
Fig. 4.7-4 Observed microstructure in 2-D and the underlying 3-D structure.