Hydrogen-induced Internal Friction Research Articles

Hydrogen-induced high damping of bulk metallic glasses

There are two important topics concerned with the recent researches on the damping materials of hydrogenated metallic glasses (HMGs). One is the mechanism of the high hydrogen-induced internal friction of HMGs. The other is the materials processing of “bulk” HMGs for engineering. This article describes the summary of our recent studies on these topics. The first one is closely related to the local structure of the metallic glasses. Therefore, our recent results on the intermediate-range local structure of the simple two Zr-based metallic glasses are described, which has been clarified by the Voronoi analysis using the experimental data of the neutron diffraction measurements. The hydrogen-induced internal friction of HMGs is also discussed on the basis of these recent results of the local structure of the metallic glasses. In terms of the second topic, the first successful preparation of heavily hydrogenated Zr-based bulk HMG rods without hydrogen-induced surface embrittlement is described. They are prepared by a powder-compact-melting and liquid-casting process using Zr–Al–Ni–Cu metallic glass and ZrH 2 powders as the starting materials. It has been found that they have high damping properties.

Internal friction induced by interstitial atoms in multicomponent glassy alloy and composite

Effects of the 2 at.% Nb addition on the stability and hydrogen-induced internal friction behavior of the Ti 34Zr 11Cu 47Ni 8 multicomponent glassy alloy have been investigated. Thermal analysis indicates that the supercooled liquid region decreases by adding Nb, indicating that 2 at.% Nb addition reduces glass forming ability. On the other hand, there is no effect of the Nb addition on the hydrogen content dependence of the peak internal friction and the peak temperature. Nb has no attractive interaction with Ti and Zr but is attracted to Ni atoms. The contrasting effects of Nb addition are thus attributable to its alternative effects on the local atomic structure, i.e. no effect of Nb on the local atomic structure around Ti and Zr having high affinity with hydrogen but strong effect on the environment of Ni.

Internal Friction and Mechanical Strength of Hydrogenated Ti-Rich Multicomponent Glassy Alloys

The hydrogen-induced internal friction and mechanical strength of the Ti-rich Ti34Zr11Cu47Ni8 and (Ti34Zr11Cu47Ni8)98Si2 hydrogenated glassy alloys have been investigated. It is found that the tensile strength is more than 0.8 GPa at room temperature when the hydrogen content is below about 20 at% for both alloys. The frequency dependence of peak temperature of the hydrogen-induced internal friction of (Ti34Zr11Cu47Ni8)98Si2-17.3 at%H hydrogenated glassy alloys has been clarified. Activation energy and pre-exponential factor are estimated to be 0.35 eV and 1.3x10-12, respectively. Compared with these values with those of Zr40Cu49Al10Si1 hydrogenated glassy alloys which show an internal friction peak around 300 K at about 300 Hz, it is found that the activation energy is much smaller than that of the latter although the pre-exponential factor is almost the same. Considering their similar composition and different component (Al), it is suggested that the component Al of the latter glassy alloys is effective for the higher activation energy which results in the increase of the peak temperature.

Hydrogen-induced internal friction of Ti-rich multicomponent glassy alloys

Hydrogen-induced internal friction of hydrogenated quaternary Ti 34Zr 11Cu 47Ni 8 (number indicate at.%) and quinary Ti 34Zr 11Cu 47Ni 8–M (M = 2 at.% Si, 5 at.% Pd, 3 at.% Nb) glassy alloys has been investigated and compared with each other. It is found that Si is most influential on the hydrogen content dependence of peak temperature and peak internal friction. It is also found that Nb does not affect both peak temperature and peak internal friction. These differences are discussed from the viewpoint of alloying effects on the local atomic structure around Ti and Zr where hydrogen is located.

Light-induced anelastic change in a-Si(H)

The thermal desorption spectra between 400 and 1100 K and the internal friction spectra between 80 and 423 K were studied for a-Si(H). The thermal desorption of hydrogen was observed around 650 K (TDH 650 K ) and around 900 K (TDH 900 K,L and TDH 900 K,H ). Both TDH 900 K,L and TDH 900 K,H with the activation energy of 1.6 eV were attributed to the desorption of bonded hydrogen. TDH 650 K was not a diffusion controlled process with the activation energy of 1.0 eV, where one part of TDH 650 K was attributed to the desorption of isolated hydrogen molecules. The hydrogen-induced internal friction, H- Q a-Si ( H ) − 1 , was observed between 80 and 423 K. Hydrogen responsible for H- Q a-Si ( H ) − 1 showed the thermal desorption around 650 K (TDH 650 K ), indicating that isolated hydrogen molecules in the amorphous structure may be responsible for H- Q a-Si ( H ) − 1 . Light soaking caused changes in H- Q a-Si ( H ) − 1 in the temperature ranges between 80 and 200 K and between 200 and 300 K, indicating that light soaking modified the local amorphous structures responsible for these changes in Q a-Si ( H ) − 1 .

Effect of Pd additions on phase stability and hydrogen-induced internal friction of TiZrCuNi glassy alloys

The effects of additions of Pd below 10 at.% on the stability and hydrogen-induced internal friction behavior of Ti 34 Zr 11 Cu 47 Ni 8 glassy alloys have been investigated. Thermal analyses indicate that the supercooled liquid region decreases distinctly with increasing Pd content. It was found that internal friction peak temperatures of Ti 34 Zr 11 Cu 47 Ni 8 –Pd hydrogenated glassy alloys (HGAs) in the hydrogen content range below approximately 30 at.% H were higher than those of the original Ti 34 Zr 11 Cu 47 Ni 8 HGAs, especially at hydrogen contents below ∼10 at.% H. It was also found that the internal friction peaks of Ti 34 Zr 11 Cu 47 Ni 8 –Pd HGAs increased with increasing hydrogen content below ∼15 at.% H, after which they tended to saturate. These results are in contrast to the effects of Si addition as previously reported. The effects of Pd are discussed from the viewpoint of the interstitial site distribution for hydrogen and local atomic structure of the glassy alloy.

Stability and hydrogen-induced internal friction of Ti-rich multicomponent glassy alloys

Hydrogen-induced internal friction behavior of ternary Ti 37 Zr 12 Cu 51 and quaternary Ti 34 Zr 11 Cu 47 Ni 8 , which is also expressed by (Ti 0.37 Zr 0.12 Cu 0.51 ) 92 Ni 8 , glassy alloys with a wide supercooling region have been investigated by measuring temperature dependence of internal friction above 90 K. It is found that they show a broad peak depending hydrogen content. With increasing hydrogen content, the peak internal friction of both glassy alloys increases, while the peak temperature decreases. It should be noted that the peak internal friction of quaternary Ti 34 Zr 11 Cu 47 Ni 8 glassy alloys are larger than that of ternary Ti 37 Zr 12 Cu 51 glassy alloys in the hydrogen content dependence of the peak internal friction. This is attributable to the increase of local strain anisotropy due to the change of local atomic arrangement when adding Ni, i.e. the change from ternary to quaternary. On the other hand, there are no distinguished effects of the change on the hydrogen content dependence of the peak temperature, suggesting changes not only the activation energy but also the frequency factor (pre-exponential factor) in the relaxation process by the change.

Effects of a small amount of Si or Ge addition on stability and hydrogen-induced internal friction of Ti 34Zr 11Cu 47Ni 8 glassy alloys

Effects of a small amount of Si or Ge addition on stability and hydrogen-induced internal friction behavior of Ti 34Zr 11Cu 47Ni 8 glassy alloys have been investigated by X-ray diffraction, thermal analysis and temperature dependence of internal friction. It is found that the addition of 1 at.% Si, 2 at.% Si or 1 at.% Ge is effective to stabilize the glassy state and that Si is more effective than Ge. The peak internal friction of the single glassy phase alloy increases with increasing hydrogen content below about 20 at.% H. It is found that (Ti 34Zr 11Cu 47Ni 8) 99Si 1 glassy alloys have lower peak internal friction than the Ti 34Zr 11Cu 47Ni 8 glassy alloys, while (Ti 34Zr 11Cu 47Ni 8) 98Si 2 and (Ti 34Zr 11Cu 47Ni 8) 99Ge 1 glassy alloys have much higher peak internal friction. It should be noted that a (Ti 34Zr 11Cu 47Ni 8) 98Si 2 glassy alloy containing 14.4 at.% H shows high internal friction, Q −1 of about 4 × 10 −2. The peak temperature of the single glassy phase alloys decreases with increasing hydrogen content below about 20 at.%. It should be noted that the addition of an extremely small amount of Si is effective to increase the peak temperature of the single glassy phase alloys. The relationship between the tensile strength and specific damping capacity indicates that the hydrogenated (Ti 34Zr 11Cu 47Ni 8) 98Si 2 glassy alloys have almost the same potential for a damping material as crystalline Mn–Cu–Al and Cu–Al–Ni alloys and hydrogenated Zr–Cu–Al glassy alloys.

Stability and hydrogen-induced internal friction of Ti-rich multicomponent glassy alloys

Hydrogen-induced internal friction behavior of ternary Ti 37Zr 12Cu 51 and quaternary Ti 34Zr 11Cu 47Ni 8, which is also expressed by (Ti 0.37Zr 0.12Cu 0.51) 92Ni 8, glassy alloys with a wide supercooling region have been investigated by measuring temperature dependence of internal friction above 90 K. It is found that they show a broad peak depending hydrogen content. With increasing hydrogen content, the peak internal friction of both glassy alloys increases, while the peak temperature decreases. It should be noted that the peak internal friction of quaternary Ti 34Zr 11Cu 47Ni 8 glassy alloys are larger than that of ternary Ti 37Zr 12Cu 51 glassy alloys in the hydrogen content dependence of the peak internal friction. This is attributable to the increase of local strain anisotropy due to the change of local atomic arrangement when adding Ni, i.e. the change from ternary to quaternary. On the other hand, there are no distinguished effects of the change on the hydrogen content dependence of the peak temperature, suggesting changes not only the activation energy but also the frequency factor (pre-exponential factor) in the relaxation process by the change.

Hydrogen-induced internal friction of Zr-based bulk glassy alloys in a rod shape above 90 K

Hydrogen-induced internal friction of Zr 65Al 7.5Ni 10Cu 17.5 bulk glassy alloys in a short rod shape (1.5 mm in diameter, 44 mm in length) have been investigated above 90 K using a vibrating reed technique. A quite broad and asymmetric peak is observed around 240 K ( H=2.21 at.%) in the temperature dependence of internal friction. Strain amplitude dependence of internal friction of Zr 63.57Al 7.32Ni 9.79Cu 17.11H 2.21 have been also measured at about the peak temperature and room temperature. It is found that the internal frictions at both temperatures are independent of the strain amplitude. Effects of hydrogen concentration ( H=0.24–2.21 at.%) on the temperature dependence of internal friction have been also clarified. The peak temperature decreases with increasing hydrogen concentration and the peak internal friction increases almost linearly. These results are compared with the reported results of Zr–Al–Ni–Cu–Pd bulk glassy alloys and discussed from the viewpoints of local structure of the Zr-based glassy alloys.

Hydrogen-induced internal friction in nanocrystalline palladium

The influence of H and D on the internal friction of nanocrystalline Pd was studied in vibrating-reed experiments (temperatures between 5 and 250 K; frequencies between 300 and 2000 Hz, H and D concentrations of about 2 and about 4 at.%). The data demonstrate a strong H- or D-induced internal-friction peak at around 160 K. The comparison with literature results for H-doped ordinary coarse-grained or single-crystal Pd suggests that the peak is caused by a Snoek-Köster relaxation of H or D atoms in the grains of the nanocrystalline Pd. The data show further a relaxation at around 70 K which is probably due to relaxation processes of H or D atoms in the grain boundaries.

Hydrogen-induced internal friction in NiZr 2

The H-induced internal friction (IF) in the C16 compound NiZr 2 was measured, at temperatures between 80 and 500 K and H concentrations from about 0.3 to 3 at.%, on samples crystallized from amorphous ribbons using the vibrating reed technique. With some variation between individual ribbons, three IF peaks (I–III) were found at temperatures near 160 K, 250 K, and below 100 K respectively. Peaks I and II are interpreted as reorientation peaks and discussed in terms of a recent microscopic model relating interatomic distances to activation energies, which can account qualitatively also for the large difference in width between these two peaks. A preliminary explanation for the third peak is a ‘reaction mode’ (an exchange of H atoms between two types of interstitial sites without reorientation), but other processes are also possible.

Hydrogen-Induced Internal Friction in Amorphous and Crystalline Intermetallic Phases

Hydrogen-Induced Internal Friction in Amorphous and Crystalline Intermetallic Phases

Crystallization of hydrogen-containing Co33Zr67: an internal friction study

Abstract The crystallization sequence of amorphous Co 33 Zr 67 containing small amounts of hydrogen was studied by DSC, TEM and the vibrating-reed technique. Additional structural information was obtained from the hydrogen-induced internal friction spectra. The transformation into the stable, tetragonal CoZr 2 equilibrium phase is preceded by the formation of metastable, cubic CoZr 2 that can be produced in a nanocrystalline state. The structure of the grain boundaries in this state was found to be similar to that of the glass. After additional hydrogen charging, a simultaneous formation of both the cubic and tetragonal CoZr 2 phases from the amorphous state was observed.

Effect of Plastic Deformation on the Hydrogen-Induced Internal Friction Peak in Austenitic Stainless Steel

Effect of Plastic Deformation on the Hydrogen-Induced Internal Friction Peak in Austenitic Stainless Steel

A hydrogen-induced internal friction peak in cold-worked nickel

A hydrogen-induced internal friction peak in cold-worked nickel