Effect of Spun Velocities and Composition on the Microstructure and Transformation Temperatures of TiNi Shape Memory Ribbons

Abstract

Ti‒50.13Ni and Ti‒49.62Ni (at.%) shape memory alloy ribbons were fabricated by melt-spinning method at different circumferential wheel velocities. The effects of wheel velocity, chemical composition and heat treatments on microstructure and Transformation temperature were investigated. Differences in wheel velocity led to differences in cooling rate and sample dimension, as well as in phase transformation temperatures. Two heat treatment conditions were studied, 350°C for 1h and 350°C for 5h. In the samples produced at high wheel velocity and heat-treated at 350°C for 5h, nanosized Ti-rich precipitates were observed in both chemical compositions. Cross-sectional microstructure was studied by optical microscopy; SEM was used to study the nanometric grains and nano precipitation. The transformation temperatures were analyzed by DSC.

Keywords: Ti‒Ni Shape memory alloys Ribbons; Melt-spinning process; Ti rich nanoprecipitate; Transformation temperature

1. Introduction

Among all the shape memory alloys (SMAs), the near equiatomic TiNi alloy is one of the most used due to the their excellent properties like corrosion resistance, biocompatibility and its superior mechanical properties such as large deformation and recovery force^1,2. In addition, TiNi thin films show shape memory effects comparable to those of bulk materials^2,3. TiNi ribbons manufactured by melt-spinning technique have demonstrated to be easily manufactured having control over chemical composition and can be manufactured with less than 20 µm thick. TiNi-based ribbons have attracted much attention because of their potential applications on microactuators such as microvalves, micropumps and microgrippers. These devices are considered part of the micro-electro-mechanical systems (MEMS)^4-7. Furthermore and despite that the ribbons are thicker than the thin film, it is known that grain size of the ribbons produced by melt-spinning are reduced to nanoscale and along with the rapid solidification, the shape memory properties can be obtained in the ribbons even without further heat treatments⁸.

The microstructure of the melt-spun ribbons depend on values of different parameters such as wheel speed, gas pressure, melt temperature and nozzle-wheel gap. In this study two different TiNi ribbons were fabricated by the melt-spinning method with wheel velocities of 30 m/s and 50 m/s, and the relation between the wheel speed and microstructure were analyzed by optical and scanning electron microscopy. The effects on transformation temperature were analyzed by DSC, showing in this case, that R phase transformation temperature can be measured using the slope change on the curves of percent phase transformation vs. temperature.

2. Experimental Section

The conventional vacuum induction melting (VIM) process was employed to elaborate binary Ti‒Ni SMAs. The buttons had a nominal composition of Ti‒50.13Ni and Ti‒49.62Ni (at.%), hereafter called M1 and M2, respectively. Their transformation temperatures obtained by DSC are presented in Table 1. After that, the buttons were placed in a melt-spun equipment to produce the ribbons.

Table 1
Phase transformation temperatures of the row materials^a.

Alloy	As (°C)	Af (°C)	Ms (°C)	Mf (°C)
M1	58.0	77.9	49.7	34.9
M2	67.6	87.8	59.3	44.0

• ^a
  Grade 1 Ti, 99.80 wt.% purity (balance); electrolytic Ni, 99.95 wt.% purity.

The melt-spun ribbons were produced under a 200 mbar argon atmosphere using a quartz crucible with a nozzle diameter of 1.0 mm; the melt was ejected onto the surface of a polished copper wheel having a tangential wheel speed fixed at 30 and 50 m/s. The distance between the nozzle and the copper wheel was 0.5 mm; the thickness average of the ribbons varied from 30 up to 50 µm, depending on the casting parameter, for example higher linear velocity produces smaller thickness⁹. In order to decrease in defects like dislocations, which are generated during melt-spinning, the samples were heat treated at 350°C for 1 and 5 hours. Table 2 shows some characteristics of the obtained ribbons, focusing on the chemical composition measured by energy dispersive X-ray (EDX) to corroborate the composition initially used in the VIM process. As can be seen EDX results was very close to the initial composition.

Table 2
Thermal and chemical characteristics of the obtained ribbons

Alloys	Tangential Wheel Speed, m/s	HT‒1	EDX		HT‒2	EDX
			Ti (at %)	Ni (at %)		Ti (at %)	Ni (at %)
M1	30	350°C	49.7	50.3	350°C	49.3	50.7
	50	1h	49.1	50.9	5h	49.7	50.3
M2	30	350°C	50.6	49.4	350°C	51.0	49.0
	50	1h	50.4	49.6	5h	50.2	49.8

Differential Scanning Calorimetry (DSC) was employed to determine the martensitic transformation temperatures of the produced Ti‒Ni ribbons for all conditions. The measurement was carried out by a DSC model Q20 of TA Instruments (temperature accuracy ± 0.1°C), in a temperature range from 120°C to -40°C and cooling/heating rate controlled at 5°C/min. In order to analyze the microstructural changes due to the wheel velocities and heat treatments, a Nikon FX-35WA optical microscopy was used. Furthermore, a FEI Nova NanoSEM 200 scanning electronic microscopy was used for a better understanding of the effects on the microstructure.

3. Results and Discussion

3.1. Effects of wheel velocities and heat treatment on microstructure

The Figure 1 shows the optical micrographs of the transversal section of the as-spun specimens. The contact side is indicated in the figure. This side consists in very fine equiaxed grains. On other hand, as we move to the right on the image, well defined columnar grains grew from the equiaxed grains in opposite direction of heat flux (Q), see Figure 1a and 1b for M1 and M2, respectively, at 30 m/s. In the Figure 1c and 1d the specimens manufactured at 50 m/s are shown respectively for M1 and M2, showing the same behavior, but as it was expected, the specimens were thinner due to the higher velocity of the wheel, which means quicker solidification, more defects and smaller grains than grains of samples at 30 m/s.

Figure 1
Optical micrograph for specimen manufactured at 30 m/s a) M1 and b) M2. For specimen manufactured at 50 m/s c) M1 And d) M2.

Now, another interesting phenomenon takes place in the contact zone, in M1 smaller grains were developed than in M2, but in the noncontact zone bigger grain size were observed in M1 in both conditions, concerning to the wheel velocity. I.e. the sample rich in Ni or M1, promotes a more heterogeneous microstructure between the contact and no contact zone, along with the heterogeneity a lot of defects are present due to the rapid cooling velocities, which means a bigger difference between the temperature of the beginning and the end of transformation and also in properties. For this reason heat treatments were carried out.

Figure 2 shows the SEM micrographs of the contact zone from heat-treated M1 and M2 ribbons at 350°C for 5h manufactured at 30 m/s a) and b) and at 50 m/s c) and d) respectively. The grain size for M1 after the heat treatment in Figure 2a is around 1 µm and in Figure 2b for M2 is around 2 µm, confirming that the sample rich in Ni in the contact zone favors the formation of small grains. And also this was the reason why in Figure 1, it was difficult to observe by optic microscope the grains of the contact zone for both as spun samples. In Figure 2c and 2d, manufactured at 50 m/s, well-defined nanosize grains (<100 nm) can be observed for both specimens. This kind of microstructure retards the martensitic transformation and diminishes the strain recovery due to the large amount of grain boundaries that imposes constraints to the martensitic transformation. As it was already mentioned, the grain size is smaller as consequence of the higher wheel velocity, attributed to the higher cooling rate that allows a faster nucleation and growth process.

Figure 2
SEM micrograph for specimens heat treated at 350°C for 5h manufactured at 30 m/s a) M1 and b) M2 and at 50 m/s c) M1 and d) M2.

Some defects as dendritic growths were found, which favors the nucleation and growth of pre-martensitic R phase¹⁰ (Figure 3a). Moreover, at higher wheel velocity very high strain energy is stored during the process, favoring the precipitation of fine, nanometric Ti-rich particles. The Figures 3d shows these nanoparticles precipitated in grain boundaries; it is important to notice that no matter the former composition, at this velocity Ti-rich precipitates were found in both specimens.

Figure 3
SEM micrograph showing defects as dendritic growth a) and b) Ti rich precipitates.

3.2. Effects of wheel velocities and heat treatment on transformation temperature

Figure 4 shows the DSC curves for the melt-spun Ti‒Ni ribbons at 30 and 50 m/s corresponding to M1 and M2 alloys which were annealed at HT‒1 (350°C for 1h) and HT‒2 (350°C for 5h), as well as, as-spun condition for comparison purposes. The start and finish temperatures of the phase transformation were determined by the inception of the slope change in the DSC curves. Figure 4a-b represents the as-spun states for M1 and M2 respectively. In the Figure 4a, it can be seen that the transformation temperatures (TTRs) decreased with increasing of the tangential velocity for M1 Ni-rich alloy, and this is in accordance with some references^11-13, which has been attributed to the fact that if speed increases the cooling rate increased, leading to a decrease in grain size and therefore in TTRs. An opposite behavior was observed for Figure 4b. For this later case, the phenomenon has been attributed to the Ti content¹⁴. As it was observed, all conditions including the as-spun ribbons, present the reversible austenite ↔ martensite transformation.

Figure 4
DSC results corresponding to the as-spun (a-b) and annealed ribbons at HT-1 and HT-2, (c-d) M1 and (e-f) M2.

Also, in general DSC curves with broad transformation temperature range and complex shape can be observed on cooling, mainly for heat-treated samples. The complexity is attributed to the well-known two-stage martensitic phase transformation B2→R→B19'. Clearly, after the heat treatments, the conditions that seemed to present a single transformation peak, now begin to split into two, this fact can be observed for most conditions. As was shown in microstructure section, the large number of grain boundaries and Ti-rich precipitates were found when the specimen were manufactured at high wheel velocity, as a result an additional energy is required to complete the martensitic transformation, this leading to lower the transformation temperature, as observed on DSC results.

However, because of their shape, it is complicated to determine exactly the finish of the R‒phase (R_f) temperature transformation and the start of B19' martensitic transformation (M_s) for ribbons fabricated at lowest wheel speed. Due to the complications, to determinate the R‒phase temperature from the DSC curves, the percent phase transformation as function of temperature was plotted to determinate the transformation temperatures using the change in slope.

The Figures 5 and 6 show the transformation hysteresis of the M1 and M2 specimen, respectively. The transformation temperatures were taken from the forward transformation where the slope changed. Transformation temperatures are indicated by an arrow. In the case of the M1 specimen, the effect of wheel velocity on transformation temperature can be followed in the as-spun specimen; Figures 5a and 5b correspond to the samples manufactured at velocities of 30 and 50 m/s respectively. The hysteresis increased when the velocity increased. In contrast the temperature transformation decreased, for instance Ms decreased about 7.5 °C. Also the Rs decreased, this is due to the decreased in grain size¹⁵. Heat treatment effect on transformation temperatures was in the same direction, i.e. the transformation temperatures decreased in heat-treated sampled. For the M1 specimen manufactured at 30 m/s, the slope change was neglected and the Rf and Ms could not be determined, for that reason only Rs and Mf are marked, see Figure 5c and 5d. For the specimen at 50 m/s the HT1 had more effect on Rs than the Ms and hysteresis grew in more than 2 °C. The hysteresis decreased for M1specimen treated for 5 h and for the M2 the effect on the H_T was negligible.

Figure 5
Transformation hysteresis for M1 as-spun specimen a) 30 m/s, b) 50 m/s. Heat treated at 350 °C for 1 h c) 30 m/s, d) 50 m/s. And Heat treated at 350 °C for 5 h e) 30 m/s, f) 50 m/s.

Figure 6
Transformation hysteresis for M2 as-spun specimen a) 30 m/s, b) 50 m/s. Heat treated at 350 °C for 1 h c) 30 m/s, d) 50 m/s. And Heat treated at 350 °C for 5 h e) 30 m/s, f) 50 m/s.

The transformation temperatures for M2 specimen were different due to the changes in chemical composition and concerning to the wheel speed opposite behavior was observed, see Figure 6. The TTRs decreased with increases the wheel velocity. This was attributed to the higher Ti content¹⁵.

For better understanding, the effect of the spun velocity on the transformation temperatures is summarized in Table 3. As the wheel velocity increases from 30 to 50 m/s, a decreased in the transformation temperatures can be observed. For each case, the enthalpy of transformation decreased as well, in concordance with a previous work¹⁶. This can be attributed to the high cooling rate, causing a reduction of the grain size and increasing structural defects, such as dislocations. The presence of these defects lowers the Mf temperature. In addition, in high energy process as melt spinning where Ti−Ni alloys are highly deformed, the dislocations formed a net in the region close to the grain boundaries; thus, the TTRs decrease and the transformation occur in two stages, as can be seen in Figure 4 and previously reported by Goryczka, T¹².

Table 3
The values of transformation temperatures (°C) and enthalpy changes (J/g) of forward and reverse martensitic transformation for Ti‒Ni SMA ribbons at different annealing and wheel velocity.

Type of Ribbon	Wheel speed (m/s)	Rs	Rf	Ms	Mf	As	Af	ΔHA→M	ΔHM→A
as-spun:	30	37.36	32.32	31.30	16.18	50.85	66.08	24.62	21.89
M1	50	28.27	25.07	23.91	4.51	42.91	56.90	21.56	18.22
HT‒1:	30	32.46	-	-	7.50	45.32	61.30	24.61	23.54
M1	50	36.55	24.94	23.84	4.23	43.46	57.45	20.82	19.43
HT‒2:	30	40.74	33.86	31.88	11.90	47.58	64.41	22.17	20.12
M1	50	40.06	26.30	24.94	2.86	42.34	58.12	21.32	19.87
as-spun:	30	34.63	26.20	25.77	13.06	43.03	60.02	24.00	19.31
M2	50	46.18	42.17	41.15	23.20	62.73	76.25	21.06	19.37
HT‒1:	30	45.44	-	-	8.94	47.06	67.78	23.91	22.34
M2	50	46.24	35.50	32.03	9.21	53.14	64.74	23.23	18.56
HT‒2:	30	39.88	29.37	28.00	10.04	48.40	63.65	22.64	20.05
M2	50	45.14	38.51	37.10	14.47	57.30	68.02	26.68	22.78

Finally, it is important to mention that the transformation temperatures were calculated from graphics of martensite (%) vs temperature, the results confirm that one of the most important factors to take into account for melt spinning is the wheel speed.

4. Conclusions

Effects of wheel velocity on microstructure and transformation temperatures of two different composition shape memory ribbons were analyzed. The ribbons showed a heterogeneous microstructure between de contact and noncontact zone. Samples rich in Ni promote this heterogeneity. The results showed that with increasing the wheel velocity, the ribbons were thinner and with smaller grain size. At wheel velocity of 30 m/s and after the heat treatment, bigger grain sized were showed for both samples and they showed defects as dendritic growth, than can promote nucleation and growth of pre-martensitic R phase. Based on the result, at higher wheel velocity thinner ribbons with nanosized grain can be obtained.

5. Acknowledgments

This work was also supported by the project 107462 and 219535 from CONACYT.

6. References

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Publication Dates

• Publication in this collection
  12 Sept 2016
• Date of issue
  Sep-Oct 2016

History

• Received
  30 June 2015
• Reviewed
  28 June 2016
• Accepted
  10 Aug 2016