Dislocation avalanches

<h2 id="background">Background</h2>

Macroscopic plasticity are well-described by continuum model. Dislocations motions are characterized by an average velocity

τ
        =
        ρ
        b
        
          
            
              v
              ¯
            
          
        
      
    
    {\displaystyle \tau =\rho b{\bar {v}}}

which is known as Orowan's equation. However, this approach completely fails to account for well-known intermittent deformation phenomena such as the spatial localization of dislocation flow into "slip bands"<a class="footnote-ref" id="fnref:8" href="#fn:8">8</a>(also known as <a href="/facts/L%C3%BCders_band/79McdJT0">Lüders band</a>) and the temporal fluctuations in stress-strain curves (the <a href="/facts/Portevin%E2%80%93Le_Chatelier_effect/LKEuJChF">Portevin–Le Chatelier effect</a> first reported in the 1920s).<a class="footnote-ref" id="fnref:9" href="#fn:9">9</a><a class="footnote-ref" id="fnref:10" href="#fn:10">10</a>

<h2 id="experimental-approach">Experimental Approach</h2>
Although evidence of intermittent flow behavior is long known and studied, it is not until past two decades that a quantitative understanding of the phenomenon is developed with help of novel experimental techniques. 

<h3>Acoustic emission</h3>
<a href="/facts/Acoustic_emission/IcTQprTL">Acoustic emission</a> (AE) is used to record the crackling noise from deforming crystals.<a class="footnote-ref" id="fnref:11" href="#fn:11">11</a><a class="footnote-ref" id="fnref:12" href="#fn:12">12</a> The amplitudes of the acoustic signals can be related to the area swept by the fast-moving dislocations and hence to the energy dissipated during deformation events. The result shows that cracking noise is not smooth, with no specific energy scale. Effect of grain structure for "supercritical" flow has been studied in polycrystalline ice.<a class="footnote-ref" id="fnref:13" href="#fn:13">13</a>

<h3>Direct mechanical measurement</h3>
Recent developments in small scale mechanical testing, with sub-nm resolution in displacement and sub-μN resolution in force, now allow to directly study discrete events in stress and strain. Currently, the most prominent method is a miniaturized compression experiment, where a nanoindenter equipped with a flat indentation tip is used. Equipped with in-situ techniques in combination with <a href="/facts/Transmission_electron_microscopy/Rpr8jpCn">Transmission electron microscopy</a>, <a href="/facts/Scanning_electron_microscopy/yzK0hsSx">Scanning electron microscopy</a>, and micro-diffraction methods, this nanomechanical testing method can give us rich detail in nanoscale plasticity instabilities in real time. 
One potential concern in nanomechanical measurement is: how fast can the system respond? Can indentation tip remain contact with the sample and track the deformation? Since dislocation velocity is strongly effected by stress, velocity can be many orders different in different systems. Also, multiscale nature of dislocation avalanche event gives dislocation velocity a large range. For example, single dislocations have been shown to move at speeds of ~10 ms−1 in pure Cu, but dislocation groups moved with ~10−6 ms−1 in Cu-0.5%Al. The opposite is found for iron, where dislocation groups are found to move six orders of magnitude faster in a FeSi-alloy than individual dislocations in pure iron.
To resolve this issue, Sparks et al. has designed an experiment to measure first fracture of Si beam and compare with theoretical prediction to determine the respond speed of the system.<a class="footnote-ref" id="fnref:14" href="#fn:14">14</a> In addition to regular compression experiments, in-situ electrical contact resistance measurements (ECR) were performed. During these in-situ tests, a constant voltage was applied during the deformation experiment to record current evolution during intermittent plastic flow. Result shows that indentation tip remains contact with the sample throughout experiments, which proves the respond speed is fast enough. 

<h2 id="theoretical-analysis-and-simulations">Theoretical analysis and simulations</h2>
Avalanche strain distributions have the general form<a class="footnote-ref" id="fnref:15" href="#fn:15">15</a>

P
        (
        s
        )
        =
        C
        
          s
          
            −
            τ
          
        
        e
        x
        p
        [
        −
        (
        s
        
          /
        
        
          s
          
            0
          
        
        
          )
          
            2
          
        
        ]
      
    
    {\displaystyle P(s)=Cs^{-\tau }exp[-(s/s_{0})^{2}]}

where C is a normalization constant, t is a scaling exponent, and s0 is the characteristic strain of the largest avalanches.
Dislocation dynamic simulations have shown that 
 
 
 
 τ
 
 
 {\displaystyle \tau }
 
 can be sometimes close to 1.5, but also, many times higher exponents are observed, with values that may even approach 3 in special circumstances.<a class="footnote-ref" id="fnref:16" href="#fn:16">16</a><a class="footnote-ref" id="fnref:17" href="#fn:17">17</a> While traditional mean-field theory predictions suggest the value of 1.5,<a class="footnote-ref" id="fnref:18" href="#fn:18">18</a><a class="footnote-ref" id="fnref:19" href="#fn:19">19</a>
more advanced mean-field investigations have demonstrated that larger exponents can be caused by non-trivial, but prevalent mechanisms in crystal plasticity that suppress mobile dislocation populations.<a class="footnote-ref" id="fnref:20" href="#fn:20">20</a><a class="footnote-ref" id="fnref:21" href="#fn:21">21</a>

<h2 id="effect-of-crystal-structure-on-dislocation-avalanches">Effect of crystal structure on dislocation avalanches</h2>
In FCC crystals, scaled velocity shows a main peak in distribution with relatively smooth curve, which is expected from theory except for some disagreement at low velocity.<a class="footnote-ref" id="fnref:22" href="#fn:22">22</a> However, in BCC crystal, distribution of scaled velocity is broader and much more dispersed.<a class="footnote-ref" id="fnref:23" href="#fn:23">23</a> The result also shows that scaled velocity in BCC is a lot slower than FCC, which is not predicted by mean field theory. A possible explanation this discrepancy is based on different moving speed of edge and screw dislocations in two type of crystals. In FCC crystals, two parts of dislocation move at same velocity, resulting in smooth averaged avalanches profile; whereas in BCC crystals, edge components move fast and escape rapidly, while screw parts propagate slowly, which drag the overall velocity. Based on this explanation, we will also expect a direction dependence of avalanche events in HCP crystals, which currently lack in experimental data.

<h2 id="see-also">See also</h2>
<ul><li><a href="/facts/Dislocation/m1tkJYIq">Dislocation</a></li>
<li><a href="/facts/Slip_(materials_science)/P29xbKBu">Slip (materials science)</a></li>
<li><a href="/facts/Intermittency/CEIrNsP0">Intermittency</a></li>
<li><a href="/facts/L%C3%BCders_band/79McdJT0">Lüders band</a></li>
<li><a href="/facts/Portevin%E2%80%93Le_Chatelier_effect/LKEuJChF">Portevin–Le Chatelier effect</a></li>
<li><a href="/facts/Barkhausen_effect/dpr34Pwk">Barkhausen effect</a></li></ul>

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

<ol>
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</ol>

Dislocation avalanches open-in-new

Dislocation avalanches