Как выбрать гостиницу для кошек
14 декабря, 2021
Thermal expansion has been investigated via low — and high-temperature X-ray diffraction,60-67 neutron diffraction,68 and dilatometry.32,54,57,69-74 Elongation (AL/L298) and linear coefficient of thermal expansion (CTE) are plotted as a function of temperature with respect to 298 K in Figures 18 and 19, respectively. Elongation results are generally consistent between lattice parameter and dila — tometric methods, diverging at high temperatures. Scatter is magnified on the CTE versus T curve, which is akin to the second derivative of length versus T experimental data. Elongation is fairly linear, permitting authors to report a mean CTE over various temperature ranges; slope increases slightly with temperature, consistent with an observed rising CTE with temperature. Increase in CTE is more pronounced at temperatures up to 500 K with a more modest increase at higher temperature, although more lower-temperature values are needed to fully understand this behavior. At subambient temperatures, elongation (or contraction, as the reference temperature is 298 K) is nonlinear with temperature.
CTE values with respect to 298 K lie in the range (5-7) x 10~6K~ but the degree of scatter
T—1—1——- 1—1—1—1—I—1—1—l— — Gangler,71 hot-pressed ZrC0 332-0 354 Mauer and Bolz64 Elliott and Kempter,61 ZrC0g57 powder Neel et a/.,32 sintered ZrC0g2 Krikorian et a/.,63 ZrC0 97 Houska,62 hot-pressed ZrC0g5 Richardson,66 are-melted Aronson et a/.,60 ZrC0g1 powder Chang and Graham85 — Samsonov et a/.57 Fridlender and Neshpor,70 pyrolytic ZrC0gg4 Rahimzadeh et a/.,65 ZrC0gg3 powder Lawson et a/.,68 hot-pressed |
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|||||
|
|
|
|||
|
|||||
-0.005
Figure 18 Elongation with respect to 298 K of ZrCx as a function of temperature.
precludes a more precise recommended value. Thermal expansion coefficient at 1273 K as a function of C/Zr ratio is plotted in Figure 20, where a trend of increasing CTE with deviation from
stoichiometry can be seen. This composition dependence of CTE confirms the general picture of decreasing bond strength as C atoms are removed from the lattice.5
The results of diffusion studies are summarized in Table 1. The temperature dependence of diffusion
coefficient conforms to an Arrhenius relationship, according to
D(T) = D0e~Q/RT [10]
D0 (cm2s 1) |
Activation energy (kJ mol-1) |
Temperature range (K) |
D1600K (cm2 s 1) |
Ref. |
|
Diffusion of C in a-Zr |
5 x 10-8 |
385 |
898-1013 |
— |
|
6 x 10-5 |
134 |
1013-1103 |
— |
||
0.002 |
152 |
873-1123 |
— |
||
Diffusion of C in p-Zr |
0.089 |
133 |
1143-1523 |
4.0 x 10-6 |
|
0.0048 |
112 |
1173-1533 |
1.0 x 10-6 |
||
0.036 |
143 |
1873-2353 |
7.6 x 10-7 |
||
0.37 |
319 |
1473-2173 |
1.4 x 10-11 |
||
0.95 |
329 |
2273-3133 |
1.7 x 10-11 |
||
Self-diffusion of C in ZrCx |
332 |
477 |
1873-2353 |
8.9 x 10-14 |
|
132 |
474 |
1973-2423 |
4.6 x 10-14 |
||
56.4 |
519 |
2563-3123 |
6.5 x 10-16 |
||
14.1 |
456 |
2563-3123 |
1.9 x 10-14 |
||
Self-diffusion of Zr in ZrCx |
1030 |
720 |
2563-3123 |
3.3 x 10-21 |
aZotov and Tsedilkin,75 14C tracer diffusion. bAgarwala and Paul,76 14C tracer diffusion on Zr rod, vacuum. cPavlinov and Bykov,77 ZrI4/14C-ZrI4 diffusion couple, vacuum. dAndrievskii et a/.,78 14C tracer diffusion on ZrI4, vacuum.
eUshakov et a/. ,79 rate of ZrC layer growth on alternating ZrI4 and graphite pellets stacked in Mo crucible, vacuum. fAdelsberg et a/. ,23 rate of ZrC layer growth on Zr bar melted in graphite crucible, vacuum.
9Andrievskii et a/. ,80 14C tracer diffusion on hot-pressed ZrC0 96, He atmosphere.
hSarian and Criscione,81 14C tracer diffusion on single crystal and arc-melted ZrC0 965, vacuum.
‘Andrievskii et a/. ,82 14C tracer diffusion on hot-pressed ZrC0 85, Ar atmosphere.
‘Andrievskii et a/. ,83 14C tracer diffusion on hot-pressed ZrC0 97 (Zr self-diffusion composition-independent from ZrC0 84-0 .97).
where Tis absolute temperature, R is the gas constant, Qis the activation energy for diffusion (kJ mol-1), and D0 is a preexponential factor having the same units as D, the diffusion coefficient, (cm2 s — ).
Diffusion of carbon in a-Zr (hcp) and p-Zr (bcc) has been investigated through diffusion of 14C tracer deposited onto Zr75-79 and by the rate of ZrC layer growth on Zr in contact with graphite.23,79
Self-diffusion of C in ZrCx has been determined by tracer diffusion.80-83 The study by Andrievskii et a/.83 provides the only reported value for self-diffusion of Zr in ZrC, which was found to be independent of C/Zr ratio. Activation energy for C self-diffusion in ZrCx increased with decreasing C/Zr ratio, while diffusion coefficient at a given temperature increased with increasing C/Zr ratio. However, O (0.16-0.19 wt%) and N (0.27-0.55 wt%) impurity content was substantial and varied for different samples. No further studies of C self-diffusion in ZrCx as a function of C/Zr ratio are available to clarify differences between C selfdiffusion in pure ZrCx versus oxycarbonitride phases.
Carbon and zirconium self-diffusion in ZrC is slower than the inter-diffusion of C in Zr, with correspondingly higher preexponential factors and activation energies. Pavlinov and Bykov77 remarked that the activation energy for C diffusion in Zr was close to that of Zr self-diffusion in Zr. As for self-diffusion,
Zr diffuses much slower than C, which may be understood in terms of the interstitial nature of C in ZrC: the smaller C atom is able to diffuse via either thermal metal vacancies or interstitial sites, the latter dwarfing the former in most cases.
Matzke84 proposed three potential mechanisms for C self-diffusion in ZrC. First, a C atom may jump along (110) directions to its nearest neighbor vacant C octahedral interstitial site, which, according to the author, requires a large lattice strain and the movement of two Zr atoms. Second, a C atom may jump along (111 ) directions to its nearest neighbor vacant C octahedral interstitial site via an unoccupied tetrahedral interstice, requiring lower strain energy. Third, a C atom may jump to a vacant octahedral site via a thermal metal vacancy. The author proposes that this divacancy mechanism requires the lowest energy, close to the activation energy for generation of a metal vacancy.
The operative diffusion mechanism depends on the C/Zr ratio. Upadhyaya5 suggested that carbon diffusion in near-stoichiometric compositions occurs via thermal metal vacancies, while jumps via tetrahedral interstices are favored at higher carbon vacancy concentration. No adequate explanations are available for the composition dependence of activation energy of C in ZrC, or the composition independence of that of Zr. Other properties (formation enthalpy, hardness) indicate a decrease in bond strength as the C/Zr ratio decreases, which would suggest that diffusion would be enhanced as well. This stands in opposition to measured activation energies for the diffusion of C in ZrC0.84-o.97, which increased with deviation from stoichiometry.83 As for Zr diffusion, Upadyaya5 suggested that two effects in operation when the C/Zr ratio decreases, a decrease in the energy required to form thermal metal vacancies, and an increase in the energy required for metal vacancy motion due to the decreased interatomic distance, cancel each other out.
Further discussion of diffusion mechanisms in the context of mechanical creep are considered in Section 2.13.5.6.