Improved super-elastic Ti-Ni alloy wire for the angle class III patient with anterior open bite:A case report

BACKGROUND Orthodontic treatment for open bite and crossbite cases is always challenging.In this paper,we demonstrate a skeletal class III patient with anterior open bite and crossbite whose problem was successfully corrected with improved super-elastic Ti-Ni alloy wire(ISW).CASE SUMMARY A 19 years old male came to our clinic with a chief complaint of anterior open bite and crossbite and not able to chew food well.Clinical examination revealed an angle class III malocclusion with anterior open bite,crossbite and spaced arch.Ra-diographic and clinical examination showed a skeletal class III pattern.We used ISW to level the upper and lower arch and to correct the anterior open bite and crossbite.Intermaxillary elastics were also used to achieve a better interdigitation.Finally,adequate overbite,overjet and a desirable occlusion were achieved.The active treatment time took 2 years and 2 months.CONCLUSION In a case of class III angular malocclusion with open bite and crossbite in the ante-rior teeth,ideal results were achieved using the ISW technique and the patient was satisfied with the outcome.

Electocbemical Process of Ti-Ni Alloy Electrodes by Cyclic Voltammetry

The electrochemical process of Ti-Ni alloy electrode was studied by using cyclic voltammetry. The hydrogen-absorbing electrode could be approximately regarded as a reversible hydrogen elecrede. The con- trolling steps of the discharging process varying with the anodic overpotentials were investigated and the effect ofelecrode constituent modification or Zr adulteation on the electrochemical behavior was also studied.

Preparation of Ti-Ni Porous Alloys and Its Hydrogen Isotope Effects

Ti-Ni porous alloy was made from titanium and nickel powder mixture in equiatomic composition by combustion synthesis technique (self-propagation high temperature synthesis). The result analyzed by SEM and XRD shows that the alloy possesses high porosity (50%～70%), and mainly consists of TiNi phase as well as rare Ti_2Ni and TiNi_3 transition phase. Then it was activated, cracked and used as sorbent for hydrogen isotope separation. Through experiment investigation, it was discovered that the alloy is able to absorb hydrogen in very large quantities in the lattice thereof, but deuterium only very slightly or not at all, at temperatures up to 623 K, especially at temperatures from about 323 to 423 K. According to this characteristic, the Ti-Ni porous alloys may replace noble metal palladium(Pd) as used for hydrogen isotope separation and purification. Study illustrated that the technology would have a promising engineering application, such as being used for reprocessing Tokamak exhaust gases and producing high purity deuterium.

THIN FILM PREPARATION OF AMORPHOUS Ti-Ni ALLOY AND THEIR HYDROGEN ABSORPTION PROPERTIES

Amorphous Ti_(0.88)Ni_(1.00) and Ti_(1.69)Ni_(1.00) alloy films are prepared by means of ion beam sputtering using TiNi and Ti_2Ni alloy targets, respectively. Their hydrogen absorption properties are investigated by a galvanostatic method. The results show th the discharge capacity of the Ti_(1.69)Ni_(1.00) sample is higher than that of the Ti_(0.88)Ni_(1.00) sample. And the film electrodes have high durability and long cycle life.

Mechanical alloying and subsequent annealing effects on evolution of microstructure and morphology of TiH_2-Ni powders

Mechanical alloying and subsequent annealing treatment were carried out to investigate the evolution of the microstructure and morphology of the TiH2-Ni system. The Ni（Ti） solid solution was formed in the initial milling process. When the milling time was 60 h, the alloy with uniform elemental distribution showed an amorphous structure containing a small amount of TiH2 nanocrystalline phase. The annealing treatment at 693 K contributed to a completion of amorphization for the alloy milled for 60 h. For the treatment at 1 073 K, a crystallization reaction for the amorphous phase occurred, leading to the formation of Ti2Ni, TiNi, and TiNi3 compounds by a short time treatment. Moreover, a separation of Ni-rich phases from the matrix and a phase transition among these three compounds occur by a long time treatment.

Improved stability of superelasticity and elastocaloric effect in Ti-Ni alloys by suppressing Lüders-like deformation under tensile load

Functional stability of superelasticity is crucial for practical applications of shape memory alloys.It is degraded by a Lüders-like deformation with elevated local stress concentration under tensile load.By increasing the degree of solute supersaturation and applying appropriate thermomechanical treatments,a Ti-Ni alloy with nanocrystallinity and dispersed nanoprecipitates is obtained.In contrast to conventional Ti-Ni alloys,the superelasticity in the target alloy is accompanied by homogeneous deformation due to the sluggish stress-induced martensitic transformation.The alloy thus shows a fully recoverable strain of 6%under tensile stress over 1 GPa and a large adiabatic temperature decrease of 13.1 K under tensile strain of 4.5%at room temperature.Moreover,both superelasticity and elastocaloric effect exhibit negligible degradation in response to applied strain of 4%during cycling.We attribute the improved functional stability to low dislocation activity resulting from the suppression of localized deformation and the combined strengthening effect of nanocrystalline structure and nanoprecipitates.Thus,the design of such a microstructure enabling homogeneous deformation provides a recipe for stable superelasticity and elastocaloric effect.

Rapid Growth of TiNi intermetallic compound within undercooled Ti_(50)Ni_(50)alloy under electrostatic levitation condition

The undercooling dependence of the solidification mechanism was systematically explored by the electrostatic levitation(ESL)facility.During the experiments,the maximum undercooling reached up to 406 K(0.26 T_L)and the growth velocity of the primary TiNi phase was in-situ determined at various undercoolings.At the initial increase of alloy undercooling,the value of growth velocity sluggishly rose followed by a power function.In this case,the primary TiNi phase preferentially developed as the equiaxed dendrite,then the remnant liquid participated as Ti_(2)Ni andα-Ti phases on the grain boundary.Once the undercooling exceeded the critical value of 350 K,the growth velocity of the primary phase displayed a sharply increase tendency.Meanwhile,the TEM results demonstrated that the precipitation of the intermetallic Ti_(2)Ni compound was gradually restrained during the rapid solidification and the R-phase existing in the TiNi matrix at large undercooling implied that the martensitic transformation was incomplete.

Vacuum brazing TiAl intermetallic to K4169 alloy using amorphous filler metals Ti_(56.25–x)Zr_(x)Ni_(25)Cu1_(8.75)

A series of Ti_(56.25-x)Zr_(x)Ni_(25)Cu1_(8.75)(x=0–25,at.%) filler metals were designed based on a cluster-plus-glue-atom model to vacuum braze TiAl intermetallic to K4169 alloy. The impact of Zr content on the interfacial microstructure and shear strength of joints was examined. And the relationship between the interfacial lattice structure and the fracture behavior of the joint was investigated. The findings reveal a sectionalized characteristic with three reaction zones (Zone I, Zone II and Zone III) in the microstructure of the TiAl intermetallic to K4169 alloy joint. As the Zr content in filler metals increased, the diffusion of Ti transitioned from long-distance to short-distance in Zone I, changing the initial composition from TiNi_(3) /TiNi/NiNb/(Cr, Fe, Ni)SS to NiCrFe/(Cr, Fe, Ni)SS /TiNi. In Zone II, the initial composition altered from TiNi_(3) /TiNi to TiNi/Ti_(2) Ni/TiNi_(3) /TiCu/TiNi. The interface between Zones II and III altered from a non-coherent and semi-coherent interface of TiNi/TiAl/Ti_(3) Al with significant residual stress to a semi-coherent interface of TiNi/TiNi_(3) /TiAl_(2) /Ti_(3) Al with a gradient distribution. The shear strength of the joint initially decreased and then increased. When the Zr content of filler metal was 25 at.%, the shear strength of the joint reached 288 MPa. The crack initiation position changed from non-coherent TiNi/TiAl interface with high angle grain boundaries (HAGBs) and lattice mismatch of 65.86 at.% to a semi-coherent Ti3 Al/TiAl2 interface with a lattice mismatch of 20.07 at.% when the Zr content increased. The brittle fracture was present on the fracture surfaces of all brazed joints.