Miller index

<h2 id="definition">Definition</h2>

There are two equivalent ways to define the meaning of the Miller indices:<a class="footnote-ref" id="fnref:4" href="#fn:4">4</a> via a point in the <a href="/facts/Reciprocal_lattice/jYCjcEpH">reciprocal lattice</a>, or as the inverse intercepts along the lattice vectors. Both definitions are given below. In either case, one needs to choose the three lattice vectors a1, a2, and a3 that define the unit cell (note that the conventional unit cell may be larger than the primitive cell of the <a href="/facts/Bravais_lattice/7gQKTsXk">Bravais lattice</a>, as the examples below illustrate). Given these, the three primitive reciprocal lattice vectors are also determined (denoted b1, b2, and b3).
Then, given the three Miller indices 
 
 
 
 h
 ,
 k
 ,
 ℓ
 ,
 (
 h
 k
 ℓ
 )
 
 
 {\displaystyle h,k,\ell ,(hk\ell )}
 
 denotes planes orthogonal to the reciprocal lattice vector:

g
          
          
            h
            k
            ℓ
          
        
        =
        h
        
          
            b
          
          
            1
          
        
        +
        k
        
          
            b
          
          
            2
          
        
        +
        ℓ
        
          
            b
          
          
            3
          
        
        .
      
    
    {\displaystyle \mathbf {g} _{hk\ell }=h\mathbf {b} _{1}+k\mathbf {b} _{2}+\ell \mathbf {b} _{3}.}

That is, (hkℓ) simply indicates a normal to the planes in the <a href="/facts/Basis_(linear_algebra)/89IPoN6c">basis</a> of the primitive reciprocal lattice vectors. Because the coordinates are integers, this normal is itself always a reciprocal lattice vector. The requirement of lowest terms means that it is the shortest reciprocal lattice vector in the given direction.
Equivalently, (hkℓ) denotes a plane that intercepts the three points a1/h, a2/k, and a3/ℓ, or some multiple thereof. That is, the Miller indices are proportional to the inverses of the intercepts of the plane, in the basis of the lattice vectors. If one of the indices is zero, it means that the planes do not intersect that axis (the intercept is "at infinity").
Considering only (hkℓ) planes intersecting one or more lattice points (the lattice planes), the perpendicular distance d between adjacent lattice planes is related to the (shortest) reciprocal lattice vector orthogonal to the planes by the formula: 
 
 
 
 d
 =
 2
 π
 
 /
 
 
 |
 
 
 
 g
 
 
 h
 k
 ℓ
 
 
 
 |
 
 
 
 {\displaystyle d=2\pi /|\mathbf {g} _{hk\ell }|}
 
.<a class="footnote-ref" id="fnref:5" href="#fn:5">5</a>
The related notation [hkℓ] denotes the direction:

h
        
          
            a
          
          
            1
          
        
        +
        k
        
          
            a
          
          
            2
          
        
        +
        ℓ
        
          
            a
          
          
            3
          
        
        .
      
    
    {\displaystyle h\mathbf {a} _{1}+k\mathbf {a} _{2}+\ell \mathbf {a} _{3}.}

That is, it uses the direct lattice basis instead of the reciprocal lattice. Note that [hkℓ] is not generally normal to the (hkℓ) planes, except in a cubic lattice as described below.

<h2 id="case-of-cubic-structures">Case of cubic structures</h2>
For the special case of simple cubic crystals, the lattice vectors are orthogonal and of equal length (usually denoted a), as are those of the reciprocal lattice. Thus, in this common case, the Miller indices (hkℓ) and [hkℓ] both simply denote normals/directions in <a href="/facts/Cartesian_coordinates/lkTqvMmB">Cartesian coordinates</a>.
For cubic crystals with <a href="/facts/Lattice_constant/h3gMKk6V">lattice constant</a> a, the spacing d between adjacent (hkℓ) lattice planes is (from above)

d
 
 h
 k
 ℓ
 
 
 =
 
 
 a
 
 
 h
 
 2
 
 
 +
 
 k
 
 2
 
 
 +
 
 ℓ
 
 2
 
 
 
 
 
 
 
 {\displaystyle d_{hk\ell }={\frac {a}{\sqrt {h^{2}+k^{2}+\ell ^{2}}}}}
 
.
Because of the symmetry of cubic crystals, it is possible to change the place and sign of the integers and have equivalent directions and planes:

<ul><li>Indices in angle brackets such as ⟨100⟩ denote a family of directions which are equivalent due to symmetry operations, such as [100], [010], [001] or the negative of any of those directions.</li>
<li>Indices in curly brackets or braces such as {100} denote a family of plane normals which are equivalent due to symmetry operations, much the way angle brackets denote a family of directions.</li></ul>
For <a href="/facts/Face-centered_cubic/92Co7BKM">face-centered cubic</a> and <a href="/facts/Body-centered_cubic/92Co7BKM">body-centered cubic</a> lattices, the primitive lattice vectors are not orthogonal. However, in these cases the Miller indices are conventionally defined relative to the lattice vectors of the cubic <a href="/facts/Supercell_(crystal)/s7ACMN5s">supercell</a> and hence are again simply the Cartesian directions.

<h2 id="case-of-hexagonal-and-rhombohedral-structures">Case of hexagonal and rhombohedral structures</h2>

With <a href="/facts/Hexagonal_lattice_system/sSSok8wo">hexagonal</a> and <a href="/facts/Rhombohedral_lattice_system/sSSok8wo">rhombohedral</a> <a href="/facts/Lattice_system/dMQLk1q4">lattice systems</a>, it is possible to use the Bravais–Miller system, which uses four indices (h k i ℓ) that obey the constraint

h + k + i = 0.
Here h, k and ℓ are identical to the corresponding Miller indices, and i is a redundant index.
This four-index scheme for labeling planes in a hexagonal lattice makes permutation symmetries apparent. For example, the similarity between (110) ≡ (1120) and (120) ≡ (1210) is more obvious when the redundant index is shown.
In the figure at right, the (001) plane has a 3-fold symmetry: it remains unchanged by a rotation of 1/3 (2π/3 rad, 120°). The [100], [010] and the [110] directions are really similar. If S is the intercept of the plane with the [110] axis, then

i = 1/S.
There are also <a href="/facts/Ad_hoc/IYxx5Ha8">ad hoc</a> schemes (e.g. in the <a href="/facts/Transmission_electron_microscopy/Rpr8jpCn">transmission electron microscopy</a> literature) for indexing hexagonal lattice vectors (rather than reciprocal lattice vectors or planes) with four indices. However they do not operate by similarly adding a redundant index to the regular three-index set.
For example, the reciprocal lattice vector (hkℓ) as suggested above can be written in terms of reciprocal lattice vectors as 
 
 
 
 h
 
 
 b
 
 
 1
 
 
 +
 k
 
 
 b
 
 
 2
 
 
 +
 ℓ
 
 
 b
 
 
 3
 
 
 
 
 {\displaystyle h\mathbf {b} _{1}+k\mathbf {b} _{2}+\ell \mathbf {b} _{3}}
 
. For hexagonal crystals this may be expressed in terms of direct-lattice basis-vectors a1, a2 and a3 as

h
        
          
            b
          
          
            1
          
        
        +
        k
        
          
            b
          
          
            2
          
        
        +
        ℓ
        
          
            b
          
          
            3
          
        
        =
        
          
            2
            
              3
              
                a
                
                  2
                
              
            
          
        
        (
        2
        h
        +
        k
        )
        
          
            a
          
          
            1
          
        
        +
        
          
            2
            
              3
              
                a
                
                  2
                
              
            
          
        
        (
        h
        +
        2
        k
        )
        
          
            a
          
          
            2
          
        
        +
        
          
            1
            
              c
              
                2
              
            
          
        
        (
        ℓ
        )
        
          
            a
          
          
            3
          
        
        .
      
    
    {\displaystyle h\mathbf {b} _{1}+k\mathbf {b} _{2}+\ell \mathbf {b} _{3}={\frac {2}{3a^{2}}}(2h+k)\mathbf {a} _{1}+{\frac {2}{3a^{2}}}(h+2k)\mathbf {a} _{2}+{\frac {1}{c^{2}}}(\ell )\mathbf {a} _{3}.}

Hence zone indices of the direction perpendicular to plane (hkℓ) are, in suitably normalized triplet form, simply 
 
 
 
 [
 2
 h
 +
 k
 ,
 h
 +
 2
 k
 ,
 ℓ
 (
 3
 
 /
 
 2
 )
 (
 a
 
 /
 
 c
 
 )
 
 2
 
 
 ]
 
 
 {\displaystyle [2h+k,h+2k,\ell (3/2)(a/c)^{2}]}
 
. When four indices are used for the zone normal to plane (hkℓ), however, the literature often uses 
 
 
 
 [
 h
 ,
 k
 ,
 −
 h
 −
 k
 ,
 ℓ
 (
 3
 
 /
 
 2
 )
 (
 a
 
 /
 
 c
 
 )
 
 2
 
 
 ]
 
 
 {\displaystyle [h,k,-h-k,\ell (3/2)(a/c)^{2}]}
 
 instead.<a class="footnote-ref" id="fnref:6" href="#fn:6">6</a> Thus as you can see, four-index zone indices in square or angle brackets sometimes mix a single direct-lattice index on the right with reciprocal-lattice indices (normally in round or curly brackets) on the left.
And, note that for hexagonal interplanar distances, they take the form

d
          
            h
            k
            ℓ
          
        
        =
        
          
            a
            
              
                
                  
                    4
                    3
                  
                
              
              
                (
                
                  
                    h
                    
                      2
                    
                  
                  +
                  
                    k
                    
                      2
                    
                  
                  +
                  h
                  k
                
                )
              
              +
              
                
                  
                    
                      a
                      
                        2
                      
                    
                    
                      c
                      
                        2
                      
                    
                  
                
              
              
                ℓ
                
                  2
                
              
            
          
        
      
    
    {\displaystyle d_{hk\ell }={\frac {a}{\sqrt {{\tfrac {4}{3}}\left(h^{2}+k^{2}+hk\right)+{\tfrac {a^{2}}{c^{2}}}\ell ^{2}}}}}

<h2 id="crystallographic-planes-and-directions">Crystallographic planes and directions</h2>

Crystallographic directions are <a href="/facts/Line_(mathematics)/gJqsr4Gj">lines</a> linking nodes (<a href="/facts/Atom/FoQ4kGN5">atoms</a>, <a href="/facts/Ion/3bePpDna">ions</a> or <a href="/facts/Molecule/N9ljSfFq">molecules</a>) of a crystal. Similarly, crystallographic <a href="/facts/Plane_(mathematics)/tAUtRFcn">planes</a> are planes linking nodes. Some directions and planes have a higher density of nodes; these dense planes have an influence on the behavior of the crystal:

<ul><li><a href="/facts/Optics/p0vq4S1T">optical properties</a>: in condensed matter, <a href="/facts/Light/jeofpMn4">light</a> "jumps" from one atom to the other with the <a href="/facts/Rayleigh_scattering/o0MQtPMM">Rayleigh scattering</a>; the <a href="/facts/Velocity_of_light/sKSQwdNx">velocity of light</a> thus varies according to the directions, whether the atoms are close or far; this gives the <a href="/facts/Birefringence/J4lLuR3a">birefringence</a></li>
<li><a href="/facts/Adsorption/ARH9peYM">adsorption</a> and <a href="/facts/Reactivity_(chemistry)/PuJ2pmRT">reactivity</a>: adsorption and chemical reactions can occur at atoms or molecules on crystal surfaces, these phenomena are thus sensitive to the density of nodes;</li>
<li><a href="/facts/Surface_tension/EuluYmSM">surface tension</a>: the condensation of a material means that the atoms, ions or molecules are more stable if they are surrounded by other similar species; the surface tension of an interface thus varies according to the density on the surface
<ul><li>Pores and <a href="/facts/Crystallite/nXSgR0wp">crystallites</a> tend to have straight grain boundaries following dense planes</li>
<li><a href="/facts/Cleavage_(crystal)/p4YHe01X">cleavage</a></li></ul></li>
<li><a href="/facts/Dislocation/m1tkJYIq">dislocations</a> (<a href="/facts/Plastic_deformation/z1LEmkQX">plastic deformation</a>)
<ul><li>the dislocation core tends to spread on dense planes (the elastic perturbation is "diluted"); this reduces the <a href="/facts/Friction/d0108Rpu">friction</a> (<a href="/facts/Peierls%E2%80%93Nabarro_force/mxGBvcCq">Peierls–Nabarro force</a>), the sliding occurs more frequently on dense planes;</li>
<li>the perturbation carried by the dislocation (<a href="/facts/Burgers_vector/ACoBg3r9">Burgers vector</a>) is along a dense direction: the shift of one node in a dense direction is a lesser distortion;</li>
<li>the dislocation line tends to follow a dense direction, the dislocation line is often a straight line, a dislocation loop is often a <a href="/facts/Polygon/yAq7RjPz">polygon</a>.</li></ul></li></ul>
For all these reasons, it is important to determine the planes and thus to have a notation system.

<h2 id="integer-versus-irrational-miller-indices-lattice-planes-and-quasicrystals">Integer versus irrational Miller indices: Lattice planes and quasicrystals</h2>
Ordinarily, Miller indices are always integers by definition, and this constraint is physically significant. To understand this, suppose that we allow a plane (abc) where the Miller "indices" a, b and c (defined as above) are not necessarily integers.
If a, b and c have <a href="/facts/Rational_number/VJQmyY05">rational</a> ratios, then the same family of planes can be written in terms of integer indices (hkℓ) by scaling a, b and c appropriately: divide by the largest of the three numbers, and then multiply by the <a href="/facts/Least_common_denominator/vdf2gKmo">least common denominator</a>. Thus, integer Miller indices implicitly include indices with all rational ratios. The reason why planes where the components (in the reciprocal-lattice basis) have rational ratios are of special interest is that these are the <a href="/facts/Lattice_plane/fLQ6pjdk">lattice planes</a>: they are the only planes whose intersections with the crystal are 2d-periodic.
For a plane (abc) where a, b and c have <a href="/facts/Irrational_number/Psv19TET">irrational</a> ratios, on the other hand, the intersection of the plane with the crystal is not periodic. It forms an aperiodic pattern known as a <a href="/facts/Quasicrystal/evHcQeCp">quasicrystal</a>. This construction corresponds precisely to the standard "cut-and-project" method of defining a quasicrystal, using a plane with irrational-ratio Miller indices. (Although many quasicrystals, such as the <a href="/facts/Penrose_tiling/usLcMvNN">Penrose tiling</a>, are formed by "cuts" of periodic lattices in more than three dimensions, involving the intersection of more than one such <a href="/facts/Hyperplane/2s2ycYYd">hyperplane</a>.)

<h2 id="see-also">See also</h2>
<ul><li><a href="/facts/Crystal_structure/bJ4bCeHd">Crystal structure</a></li>
<li><a href="/facts/Crystal_habit/x2S1HVVY">Crystal habit</a></li>
<li><a href="/facts/Kikuchi_line_(solid_state_physics)/w5y3L2B2">Kikuchi line</a></li>
<li><a href="/facts/Reciprocal_lattice/jYCjcEpH">Reciprocal lattice</a></li>
<li><a href="/facts/Zone_axis/Knz4K9tU">Zone axis</a></li>
<li><a href="/facts/MTEX/vr0JNhaG">MTEX</a></li></ul>

<h2 id="external-links">External links</h2>

Wikimedia Commons has media related to Miller index.

<ul><li><a href="http://reference.iucr.org/dictionary/Miller_indices">IUCr Online Dictionary of Crystallography</a></li>
<li><a href="https://web.archive.org/web/20060208140059/http://www.ece.byu.edu/cleanroom/EW_orientation.phtml">Miller index description with diagrams</a></li>
<li><a href="http://www.doitpoms.ac.uk/tlplib/miller_indices/index.php">Online tutorial about lattice planes and Miller indices</a>.</li>
<li><a href="https://mtex-toolbox.github.io/">MTEX – Free MATLAB toolbox for Texture Analysis</a></li>
<li><a href="http://sourceforge.net/projects/orilib">http://sourceforge.net/projects/orilib</a>  – A collection of routines for rotation / orientation manipulation, including special tools for crystal orientations.</li></ul>

<h2 id="references">References</h2>

<ol>
<li id="fn:1">Ashcroft, Neil W.; Mermin, N. David (1976). Solid state physics. New York: Holt, Rinehart and Winston. ISBN 0030839939. OCLC 934604. <a href="0030839939" target="_blank">0030839939</a> <a href="#fnref:1" class="footnote-back-ref">↩</a></li>
<li id="fn:2">Weiss, Christian Samuel (1817). "Ueber eine verbesserte Methode für die Bezeichnung der verschiedenen Flächen eines Krystallisationssystems, nebst Bemerkungen über den Zustand der Polarisierung der Seiten in den Linien der krystallinischen Structur". Abhandlungen der physikalischen Klasse der Königlich-Preussischen Akademie der Wissenschaften: 286–336. <a href="https://archive.org/stream/abhandlungenderp16akad#page/286/mode/2up" target="_blank">https://archive.org/stream/abhandlungenderp16akad#page/286/mode/2up</a> <a href="#fnref:2" class="footnote-back-ref">↩</a></li>
<li id="fn:3">Oxford English Dictionary Online (Consulted May 2007) <a href="http://dictionary.oed.com" target="_blank">http://dictionary.oed.com</a> <a href="#fnref:3" class="footnote-back-ref">↩</a></li>
<li id="fn:4">Ashcroft, Neil W.; Mermin, N. David (1976). Solid state physics. New York: Holt, Rinehart and Winston. ISBN 0030839939. OCLC 934604. <a href="0030839939" target="_blank">0030839939</a> <a href="#fnref:4" class="footnote-back-ref">↩</a></li>
<li id="fn:5">Ashcroft, Neil W.; Mermin, N. David (1976). Solid state physics. New York: Holt, Rinehart and Winston. ISBN 0030839939. OCLC 934604. <a href="0030839939" target="_blank">0030839939</a> <a href="#fnref:5" class="footnote-back-ref">↩</a></li>
<li id="fn:6">J. W. Edington (1976) Practical electron microscopy in materials science (N. V. Philips' Gloeilampenfabrieken, Eindhoven) ISBN 1-878907-35-2, Appendix 2 <a href="/wiki/ISBN_(identifier)" target="_blank">/wiki/ISBN_(identifier)</a> <a href="#fnref:6" class="footnote-back-ref">↩</a></li>
</ol>

Miller index open-in-new

Miller index