Thermal Analysis of Solid State Amorphization: Predicted and Measured Reaction Enthalpies and Reaction Kinetics
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Rinze Benedictus
, Amarante Böttger and Eric J. Mittemeijer
Abstract
Measurements of heat released upon solid state amorphization (SSA) have been performed to evaluate quantitatively a recently proposed thermodynamic model for solid state amorphization in binary systems. Three types of Ni – Ti systems have been investigated: crystalline Ni/crystalline Ti multilayers with incoherent interfaces, crystalline Ni/crystalline Ti multilayers with coherent interfaces and amorphous Ni/crystalline Ti multilayers. The heat released during SSA has been determined by differential scanning calorimetry (DSC) measurements. For the crystalline/crystalline multilayers with incoherent interfaces the reaction heats measured agree with the reaction heats derived from the thermodynamic model. For the crystalline Ni/crystalline Ti multilayers with coherent interfaces and the amorphous Ni/crystalline Ti multilayers the experimental reaction heats differ 30 to 40 % from the calculated values. The activation energies for SSA in the three Ni/Ti systems have been determined, too, from the DSC measurements. Within experimental accuracy the same value for the activation energy was obtained for the three types of Ni/Ti multilayers. The activation energy was found to be 130 ± 15 kJ/mol. This value agrees with the one obtained previously from X-ray diffraction analysis. The evolution of heat during SSA could be described as a function of annealing time upon isochronal annealing adopting a Johnson-Mehl-Avrami type reaction rate equation.
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The work described in this paper was made possible by financial support from the Netherlands Technology Foundation (STW).
Literature
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Appendix A Instrumental and Thermal Lag
According to a simple RC scheme for the DSC apparatus [8, 12] and in the absence of a transformation involving enthalpy change, the heat flux to the sample
where Ts is the temperature of the sample, Ta is the temperature imposed on the sample holder of the DSC apparatus (= T0 + ϕt, where ϕ is the constant heating rate and t is annealing time) and Rs is the heat resistance from the sample holder to the sample via the sample container within the sample holder. A similar expression can be derived for the heat flux to the reference (here consisting of only an aluminium container),
where tx is the power response time constant (instrumental lag) and
Using Eq. (A1) and its pendant for
where Cs and Cr are the heat capacities of sample (including the aluminium container) and reference and ts = RsCs and tr = RrCr.
The RC-times and K can be estimated from the beginning of the DSC measurement by fitting Eq. (A4) to a DSC run (either first run or second run ; cf. Section 2). This fit can best be made directly after the start of the DSC run, because then the difference in thermal lag between sample and reference can be appreciable, recognizing that in the present experiment the reference consists of an empty sample container. Results of such fits are shown in Fig. A1 for DSC runs for the three types of specimens studied. It follows that the RC times (data gathered in Table A1) range from 1 s to 4 s, and thus in view of the time scale pertaining to a DSC run, are negligible indeed.

Fit of Eq. (A4) to the beginning of the first run of the DSC measurements with a heating rate of 10 K/min in order to obtain values for ts, tr and tx (i.e., thermal lag of the specimen and the reference, and the instrumental lag, respectively) for the three types of Ni/Ti multilayers. (Fits to the second run give similar results.)
Thermal and instrumental lag times pertaining to the current DSC measurements. ts is the thermal lag of the specimen, tr the thermal lag of the reference and tx is the instrumental lag.
| Specimen | ts [s] | tr [s] | tx [s] |
|---|---|---|---|
| 22 × [Ni (10 nm) Ti (16 nm)] | 3.1 | 2.8 | 1.8 |
| 80 × [Ni (2 nm) Ti (5 nm)] | 4.0 | 3.5 | 1.7 |
| 60 × [Ni (1.3 nm) Ti (8 nm)] | 2.9 | 2.8 | 1.8 |
Appendix B Approximation of β
The state variable β (cf. Eq. (7b)) can be rewritten by partial integration as
where the origin of time corresponds with T = 0 K (see discussion above Eq. (9) in Section 4.2). The integral in the second term on the right-hand side of Eq. (B1) is written as (see below Eq. (B4):
By substituting Eq. (B2) into Eq. (B1) if follows that
where B(t) is given by
The essence of the above treatment is that for practical values of ϕ and Q (say ϕ = 1 to 20 K/min.; Q = 50 to 300 kJ/mol), B(t) can be taken as independent of time: B = 0.90 ± 0.02 as determined by numerical calculation after substitution of A(t) according to Eq. (B2). (Note that the origin of the time scale corresponds to T = 0 K).
© 1998 Carl Hanser Verlag, München
Articles in the same Issue
- Frontmatter
- Aufsätze
- Thermal Analysis of Solid State Amorphization: Predicted and Measured Reaction Enthalpies and Reaction Kinetics
- Precipitation Trends in Highly Alloyed Austenitic Stainless Steels
- Condensed Phase Equilibria in the Mo-Ga-N System at 800 °C
- Interdiffusion in the β Mo–Ti Solid Solution at High Temperatures
- Nitride Phase Equilibria in the Fe–Cr–Mn–N System at 1273 and 1073 K
- The Solubility of Nickel in Sodium Calculated from Corrosion Tests in Flowing Liquid Metal
- Influence of Heterogeneous Dislocation Arrangements on X-ray Diffraction Profiles Measured on Cyclically Deformed Nickel Single Crystals
- Change of Crystal Orientation in Straining and Dislocation Glide Systems
- On the High Temperature Creep Behavior of Two Rapidly Solidified Dispersion Strengthened Al–Fe–V–Si Materials
- Kinetics of Ferrite to Austenite Transformation in a High Strength Low Alloy Steel Containing Nb
- Mechanical Alloying of Zn-rich Zn–Al–Cu Alloys
- Mitteilungen der Deutschen Gesellschaft für Materialkunde e.V.
- Personen
- Terminkalender
Articles in the same Issue
- Frontmatter
- Aufsätze
- Thermal Analysis of Solid State Amorphization: Predicted and Measured Reaction Enthalpies and Reaction Kinetics
- Precipitation Trends in Highly Alloyed Austenitic Stainless Steels
- Condensed Phase Equilibria in the Mo-Ga-N System at 800 °C
- Interdiffusion in the β Mo–Ti Solid Solution at High Temperatures
- Nitride Phase Equilibria in the Fe–Cr–Mn–N System at 1273 and 1073 K
- The Solubility of Nickel in Sodium Calculated from Corrosion Tests in Flowing Liquid Metal
- Influence of Heterogeneous Dislocation Arrangements on X-ray Diffraction Profiles Measured on Cyclically Deformed Nickel Single Crystals
- Change of Crystal Orientation in Straining and Dislocation Glide Systems
- On the High Temperature Creep Behavior of Two Rapidly Solidified Dispersion Strengthened Al–Fe–V–Si Materials
- Kinetics of Ferrite to Austenite Transformation in a High Strength Low Alloy Steel Containing Nb
- Mechanical Alloying of Zn-rich Zn–Al–Cu Alloys
- Mitteilungen der Deutschen Gesellschaft für Materialkunde e.V.
- Personen
- Terminkalender