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Metals 2013, 3(2), 178-187; doi:10.3390/met3020178
Published: 15 April 2013
Abstract: Current-activated tip-based sintering (CATS) is a novel process where spark plasma sintering conditions are applied through an electrically conducting tip on a locally controlled area on a green powder compact/bed. The localization of electric current in CATS allows for unique temporal and spatial current and temperature distributions within the tip and powder compact. In this paper, special experimental setups were used to monitor the temperature profiles in the tip and at multiple locations on the surface of nickel powder compacts. A variation in the initial green density was found to have a significant effect on the maximum temperature in the tip as well as the temperature distribution across the powder compact. In general, the lowest green density specimens displayed the best conditions for localized densification. The concept of effective current density is introduced and results are discussed in relation to the densification parameter.
Despite the intense research and interest in spark plasma sintering (SPS) as a fast powder consolidation process, other methods have emerged combining the effect of electric current with plastic deformation such as electric rolling of powders [1,2] and spark plasma extrusion [3,4]. Most recently, current-activated tip-based sintering (CATS)  developed by the authors, has provided the means to localize SPS conditions, and open the door to multi-scale processing of 1D, 2D and 3D shapes.
CATS is a new process in which an electric current is allowed to pass through a small conducting tip (that could be stationary or moving) to a powder compact/bed thus enforcing SPS conditions on a locally controlled area depending on the size and shape of the tip. Figure 1 shows a schematic of a CATS setup.
Recently, CATS has been used to locally sinter different material systems such as nickel and copper powders , as well as Ni-Ti intermetallics . It was also recently used to enable an ignition of a macro-scale current-activated combustion synthesis process for Ni–Al powder mixtures which would spontaneously convert to an intermetallic phase . Due to the potentially small tip sizes used in CATS, it can be extremely difficult to obtain temperature measurements through conventional routes such as those used in SPS. This is also due to the absence of a die in CATS; moreover, optical pyrometers are excluded due to spot size limitations. Therefore, it was necessary to introduce an experimental setup that allows for monitoring of spatial and temporal temperature distributions. This paper, therefore, for the first time, provides an initial insight into the expected temperature distributions in green compacts and tips during CATS. In this work, temperatures from the surface of the tip, as well as the green compact, were taken using high response thermocouples that were placed at pre-specified exact locations using specially designed devices. Due to the inherent tip-specimen geometry in CATS and the very small thickness of the specimens, it was impossible to obtain subsurface temperature measurements. The concept of effective current density is introduced and the densification parameter was used to explain results for specimens of varying green densities (with different starting resistivity values) that undergo CATS.
2. Experimental Section
Nickel powder (INCO type 123) with 5 µm average particle size (Figure 2) was used in all the experiments. The powders were compacted in a 12 mm inner diameter steel die to different initial green densities ranging from 55%–76% of theoretical density of nickel (8.9 g/cm3). All compacts had a thickness of 1 mm (squat specimens) to ensure minimum internal density variations within the specimens. Compacts that had a green density less than 55% were excluded from the investigations due to their lack of adequate strength for handling.
A direct “nominal” current density (applied current divided by the specimen-tip initial contact area) of ~50,000 A/cm2 (using a power supply, Power Ten, Model P63C-51000) was applied through a conducting 0.5 mm diameter flat CATS tip (with a pressure of ~5 MPa) for 60 s on all investigated green densities in an inert argon atmosphere. A special device was designed to enable temperature measurements using K-type thermocouples at different radial locations from the tip circumference on the top surface of the powder compact as seen in Figure 3 (taking advantage of the axi-symmetric nature of the setup). The base aluminum block had to be modified so that the tip positioning is central to ensure that all three thermocouples are properly spaced and to ensure positioning repeatability. Other experiments were also conducted using flat tip K-type thermocouples cemented on the sintering tip at a ~2.5 mm distance from the tip-compact interface (Figure 4) and a data acquisition system (PDAQ view OMB-DAQ-55) was used to collect the temperature data from the thermocouples at a frequency of 2.88 Hz.
For microstructural characterization, the top surface of the processed specimens were lightly ground and polished to at least 1-µm finish using diamond suspension. Microstructural characterization was conducted using a field emission scanning electron microscope (FESEM quanta FEG 450). Porosity contents were measured using image analysis software (UTHSCSA Image Tool version 3.0; Department of Dental Diagnostic Science at The University of Texas Health Science Center: San Antonio, TX, USA, 2002). Additionally, green densities were determined using mass and volume measurements.
3. Results and Discussion
Figure 5 shows temperature profiles during CATS (up to 60 s electric current exposure) of Ni 123 powder compacts with initial average green densities ~55%, 67% and 76% of theoretical. Since the current is applied for only 60 seconds, in the figure, times greater than 60 seconds represent cooling curves in the absence of current. The “tip” temperatures at ~2.5 mm away from the specimen surface were measured by using the thermocouple configuration shown in Figure 4. For all initial green densities investigated, the initial heating rate was found to be the same; however, higher temperatures were observed with a decline in green density. Steady state temperatures were reached for the 67% and 76% dense specimens within the duration of the experiment. This was not, however, the case for the lowest green density specimens where a continuously increasing temperature was observed within the investigated current exposure time. This could be explained if we consider the comparatively higher resistivity of these specimens. This high resistivity will give rise to comparatively higher temperatures immediately under the tip, leading to rapid consolidation of this local region. This consolidated region will possess a low resistivity, and therefore becomes highly electrically conductive. Thus, an electric current passing through the tip would now travel through the consolidated region (process zone) to the significantly unsintered (more resistive) areas beneath/around it. The surrounding area will then heat through Joule heating and that heat is then transferred to the tip through the already-consolidated region above it (in addition to other regions of the compact). This process is progressive in nature leading to the observed continuous increase in temperature, during the timeframe of the experiment. Such progressive growth of the process zone has also been previously documented for NiTi during CATS .
Separate experiments were also conducted for the same set of initial green densities. Here temperature measurements were instead taken on the powder compact surface at different radial distances (between 2.5 mm and 4.5 mm) from the tip circumference. For all investigated green densities, the temperature was found to decline radially away from the tip location. Figure 6a shows temperature profiles taken from the closest thermocouple to the tip (~2.5 mm away from the tip circumference). It shows that the maximum temperature was experienced by the lowest green density specimens as more heat generation is expected in the vicinity of the tip, while the 76% density specimen achieved a steady-state temperature higher than that of the 67% density. However, the temperature at this location in the 55% density specimens only becomes the highest after ~43 s of current exposure. The reason for this behavior is simply due to the difference in thermal conductivity of the two specimens (the 55% being the lowest). Immediately under the tip, the 55% specimen is expected to have the highest temperature. However, at 2.5 mm away from the tip, due to its low thermal conductivity, it will take longer for the heat to travel to the thermocouple location, hence the behavior observed in the plot. Figure 6b shows temperature profiles taken from the thermocouple that is farthest from the tip. However, at this location, the 55% density specimen achieved the lowest temperature rise. This is again due to the lower thermal conductivity of the 55% green density compact compared to higher green density specimens. The results also show that the maximum temperature read by the thermocouples out of all the specimens was ~140 °C at a distance ~2.5 mm from the tip circumference. At such temperatures, nickel is not expected to sinter which therefore favors a localized consolidation effect only for regions much closer to the tip. Finite element modeling (the subject of another publication ) showed that the maximum temperature reached at the maximum temperature reached under the current conditions was close to 1000 °C.
Figure 7 shows scanning electron micrographs of regions in the vicinity and under the tip for the 55% initial green density specimens. Some surface circular cracks were observed around the consolidated regions due to shrinkage and thermally induced stresses. However, it was observed that the radius, as well as the thickness of these cracks, decreased for the 67% density specimen as less shrinkage was experienced, while for the 76% density specimens (with an expected higher green strength), minimum shrinkage was observed and no circumferential cracks were detected. Further microscopic analysis showed that consolidation was mainly confined to the region immediately beneath the tip, and no consolidation took place in the area in between this region and the circular crack (since the observed microstructure was similar to that of the unsintered green compact) which is evidence of consolidation only being confined to the region under the tip.
One useful parameter in sintering, especially when comparing specimens with different initial green densities (different initial porosity levels), is the densification parameter (Ψ)  defined by Equation 1:
Figure 8 shows the average pore content (obtained through image analysis) at various locations at 150 µm beneath the tip–surface interface for all specimens and it shows that for all three initial green densities, a final density of ~0.85 of theoretical was reached after 60 s of current exposure. However, if the densification parameter (Ψ) (Equation 1) is considered, it is clear that it is inversely proportional to the initial green density.
All results show that, despite having the lowest initial green density, the 55% dense specimens observed the most significant and pronounced densification amongst all the specimens processed. Lower green density specimens are expected to have a lower electrical conductivity due to the presence of larger insulating air gaps and the minimum particle-to-particle contact areas , which enhances the Joule heating during current application. Furthermore, the assumed nominal current density (the applied current/the tip–material contact area) is in fact magnified as the actual contact area in powder compacts is less than the assumed area due to the presence of porosity and powder structure. In pressure-assisted powder densification, an effective pressure  is defined to take into account the powder/void structure of the material. For example, a fully consolidated material should result in an effective pressure equal to the applied pressure; however, a porous compact should result in a considerably higher effective pressure, generally due to a decline in the effective contacting area exposed to the same load. Although not previously reported to the best of the author’s knowledge, it becomes also logical in the case of electric current activated sintering, to introduce an “effective current density” term JE, analogous to the effective pressure, which should increase with a decrease in the initial green density. As such, the following equation can be introduced and may be assumed to represent effective current density, JE.
Although all green density specimens were exposed to the same nominal current density, the initial effective current density is expected to be highest for the lowest density specimens (Figure 9). All the above factors (including effective current density and effective pressure) have contributed to the enhanced densification/consolidation behavior of the lowest density specimens.
The following conclusions can be drawn from the present study:
Green compact temperature profiles were successfully generated for the first time in current-activated tip-based sintering under continuous DC current exposure.
The green density was found to have a major effect on the temporal and spatial temperature rise and distribution.
The lowest green density specimens resulted in the highest observed temperatures but more localized (closer to the tip) than higher green density specimens.
Despite all specimens attaining similar final relative densities following CATS, the 55% initial green density specimens experienced the highest degree of densification according to densification parameter calculations.
At increased radial distance significantly removed from the process zone, specimens with lower initial green densities experienced a limited rise in temperature due to their lower thermal conductivity. This shows that localization of densification is enhanced by a reduction in initial green density. This could be exploited in future studies for micro-fabrication of complex structures under moving-tip configurations.
The authors wish to thank The National Science Foundation (CMMI division: grant no.0826532, Engineering Research Center: grant no.1028725, and major research instrumentation (MRI) grant DBI-0959908) for their support. Thank you also to Dr. Steve Barlow for his assistance with the FESEM work. The authors express their thanks to Mr. Marc Capul, Mr. Aliou Diallo and Mr. Ross Johnson for building the thermocouple-holding device. Thanks are also due to Mr. Greg Morris and Mr. Mike Lester for general technical support.
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