Skin effect for different copper bar dimensions.
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For the sake of safety, the standards and regulations limit the supply voltage level for the electric vehicles drive system. The standards dealing with the very low voltage systems (VLV) provide a general guidance. For example, the 2014/35/UE European Directive for the CE marking fixes the voltage level at 75 V DC, hence, in practice this could be the choice for the battery voltage.
Furthermore, in the automotive realm, the European Regulation R100 concerning the approval of vehicles with regard to specific requirements for the electric powertrain, has even reduced the maximum voltage level to 60 V (Class A). This range of voltage will therefore ease the design constraints and the operational maintenance of the vehicle. The 60 V is generally considered as the reference level of VLV for electric vehicles.
At this low voltage range, there is a large choice of commercially available off-the-shelf components for the power electronics needed to drive the electric motor, regardless its technology, DC motor, synchronous motor or induction motor, though knowing that the permanent magnet synchronous motors are emerging as one of the best candidate to dominate the market of powertrain electrification.
However, at low voltage, when the level of the required electrical power reaches a certain threshold, which is around 30 kW, the availability of the power electronics components becomes considerably limited given the high current level to be handled by the controller, which is greater than 500A at a battery voltage of 60 V. Indeed, this poses very challenging constraints on the design of the power modules where the high current gets closer to the switching capability limit of the transistors available on the market (very low voltage MOS technology). We will be detailing the challenges and the associated solutions related to this topic in a later section of the chapter.
The technology outlined in this chapter, where many validation prototypes are presented, brings some original solutions to the design of very low voltage electric powertrains, even at high power level. Many electric vehicles presented in this chapter involving a power as high as 100 kW.
First of all, we will discuss the design techniques of an electric motor being optimised to operate at very low voltage. Afterwards, several techniques of power distribution have been described, which enables the required total electrical power to be shared between several controllers. Finally, we present an overview of the limits of feasibility of the power electronics that would be required to drive electric motors at very low voltage, based on the current available technologies of the semiconductors components.
When an electric motor is operating at very low voltage, there is an opportunity to optimise its winding in order to significantly enhance its performance. Conventionally, the windings of electric motors are based on an enamelled round wire (loose random conductors), as illustrated in the Figure 1b. In this case, the copper fill factor inside the stator slot is very poor, where, unless relying on non-conventional manufacturing processes (segmentation, etc.), only around 40% can be achieved in the best case (pure copper CSA/naked slot area), it can be even less than 30% when considering very small size motors with tiny slots.
(a) Solid bar winding vs. (b) Round wire winding.
At very low voltage, the conductors inside the slot are connected in parallel where the number of turns is inherently very low. In the case of a winding design with one turn per slot, which is often the case at VLV, it appears to be more judicious to replace the multi-strand conductor with a single solid copper bar adjusted to the slot dimensions, as illustrated in the Figure 1a. In the latter case, the copper fill factor inside the slot can reach approximately 80%, which consequently doubles, even triples, the copper volume for a given motor size.
At a constant copper loss and a given slot cross sectional area, the relationship between the RMS current, Ib, in the solid bar conductor and the total RMS current, If, in the equivalent slot wound with multi-strand round conductor is as follows:
The coefficients σrb and σrf represent the copper fill factor inside the slot with solid bar conductor and with multi-strand round conductor, respectively. With the 80% fill factor in the first case and 35% in the second one, the current carried by the solid bar conductor is 50% higher, and, consequently, the output torque of the motor increases in the same proportion.
The Figure 2 illustrates how difficult it is to perform a high quality winding with loose round wire. It can be easily noticed that a non-negligible part of the copper is located outside the active part of the motor (i.e. stator). This bulky copper outside the stator slots increases the volume, the weight and the loss of the machine. All these drawbacks are addressed with the use of a solid bar conductor.
Electric motor end-windings wound with loose round wires.
Figures 3 and 4 illustrate some of our products made using a solid bar winding. It can be easily seen that the useless copper at the end-windings (overshooting the stator core pack) is less bulky and well controlled. These proposed winding techniques are most convenient for low voltage electrical machines.
Solid bar winding, distributed winding.
Solid bar winding, wave concentrated winding.
The distributed winding shown in Figure 3, with one slot per pole and per phase, is well suited to medium range power machines (a few tens of kW) operating at few hundreds Hz electric frequency [1, 2, 3]. The structure shown in Figure 4 is more original where the phases are wound around the tooth (wave concentered winding) and grouped in separate sectors [1, 4, 5], without phase overlaps at the end-windings of the machine. This structure is rather well suited for small electrical machines which can then operate at very high frequency (up to 2000 Hz), the resulting winding is very compact.
This technique is not commonly used in practice due to the fact that the solid bars are prone to very high AC copper loss (under alternating regime) which can be much higher than the DC ohmic loss.
Additional losses in massive conductors can be prohibitive, but a detailed study of these phenomena [1, 4] shows that the advantages of the approach largely outweigh the disadvantages if the winding is appropriately designed [1, 3, 4]. Paradoxically, the concept can be perfectly applied, as we will see, to high pole count electric motors operating at high frequency, which is the case for all machines with high power density for embedded applications.
Many industrial motor manufacturers, especially for electric vehicles, are using the solid bar copper winding, in particular via the “hairpin” technique consisting in a “pin” forming that can ease the overlapping of conductors at the end-windings (cf. Figure 5), but the overall design approach of these machines remains conventional, especially because it uses several conductors per slot. The approach presented in this chapter is distinguished by the use of a single solid bar per slot (one turn per slot), which allows to optimise many parameters and to reach unmatched level of compactness, for high power electric motors operating at very low voltage.
Hairpin winding (courtesy of special machine tool company).
In summary, the main pros in using solid bars are:
Enhanced copper fill factor (80% filling instead of 40%).
The iron-copper thermal resistance is reduced.
The slots opening width can be very small which increases the flux density in the air gap and decreases the cogging torque and eventually the torque ripple.
The copper overhangs are very compact and controlled.
The winding manufacturing process is simplified and can be easily automated.
The machine is more robust and reliable.
And the main cons are:
Higher copper loss density
The connection of the copper bars in order to form the whole winding is more complex.
In order to be able to effectively implement the technique of winding with single bar per slot, it is mandatory to fully control the additional copper losses associated with the operation at high electrical frequency.
The different phenomena related to alternating flux density inside the copper yielding to excessive loss are well describes in the literature [6, 7], however we recall here the two main ones.
In order to quantify the loss increase, the kAC coefficient is introduced, which is the ratio of the total AC copper loss, PAC, to the DC copper loss, PDC, in the winding, at given current:
The best known phenomenon causing these additional losses is called “skin effect”, it appears in any electrical conductor carrying an alternating current. The skin effect tends to push the current back to the periphery of the conductor, as shown in the following Figure 6.
Current density distribution in two conductors having the same cross-section with round and rectangular shape at different frequencies [
The current density, J, in a round conductor, as a function of the distance from the periphery, r, in sinusoidal regime, is expressed by the following relationship:
where δ represents the skin depth at a conductivity σ of the conductor:
The current density at the skin depth is roughly equal to 37% of its value at the surface, while it is only equal to 5% at three times δ.
In the case of a rectangular conductor the relationships of the skin effect are more complex. The following equation [1, 6] is valid for both cases round conductor and rectangular conductor, and allows to precisely quantify the increase in copper loss due to the skin effect:
S and p respectively represent the cross section area and the perimeter of the conductor.
Table 1 gives the values of KAC for different bar shapes (used in the prototypes presented later) and different frequencies. The dimensions of the bar are defined in Figure 7.
# | Dimensions hbar x tbar (mm) | Frequency (Hz) | δ (mm) à 100 °C | KAC |
---|---|---|---|---|
1 | 4x5 | 800 | 2,7 | 1,003 |
2 | 3x5 | 1666 | 1,9 | 1,009 |
3 | 8x4 | 800 | 2,7 | 1,009 |
4 | 8x3 | 133 | 6,6 | 1 |
Skin effect for different copper bar dimensions.
Main dimensions of the slot and the copper conductor.
According to the Table 1, in the worst case scenario, the increase in copper loss due to the skin effect is less than 1%, so this phenomenon is not significant at the considered frequencies.
The second observed phenomenon causing excess copper loss is known as field effect or inductance effect. Unlike the skin effect, it only takes place in the copper volume surrounded by a magnetic circuit (stator). This phenomenon is depicted in Figure 8. In this case, the additional loss is due to the transverse flux (slot leakage flux) produced by the armature current, which closes in the slot width (tenc), creating induced currents in the solid bar which will lead to an uneven current density distribution, being much higher in the lower part (near the slot opening) than in the upper part of the solid bar.
Illustration of the uneven distribution of the current density inside the conductor due to the slot transverse flux.
The field effect phenomenon is the main cause of increased losses, where the KAC coefficient can be greater than 4 if it is not well controlled, which would cancel out most of the benefits introduced by the use of the solid bar winding.
The coefficient KAC related the field can be precisely calculated using the following analytical relationship [1, 7]:
This relationship is only valid when KAC > 1. Table 2 summarises the value of KAC for exactly the same configurations considered in Table 1.
# | hbar (mm) | tbar/tenc | Frequency (Hz) | δ (mm) à 100°C | KAC |
---|---|---|---|---|---|
1 | 4 | 0,83 | 800 | 2,7 | 1,35 |
2 | 3 | 0,83 | 1666 | 1,9 | 1,44 |
3 | 8 | 0,8 | 800 | 2,7 | 2,65 |
4 | 8 | 0,75 | 133 | 6,6 | 1,05 |
Field effect for different copper bar dimensions.
According to the results presented in Table 2, it can been clearly seen that, as expected, the increase in copper loss due to the use of solid bars is significant, however, the solid bar still beneficial even at high frequencies when considering the overall performance of the machine. Indeed, in order to illustrate this point, we can consider the configuration # 2 operating at a nominal frequency of 1666 Hz. The use of a solid bar would increase the current in the slot, at constant DC losses, by about 50% (cf. relation (1)), while the increase in losses in AC mode would require it to be reduced by 20% (
The remaining examples of Table 2 will be analysed when their corresponding products are presented later in this chapter.
In electric vehicles, the electric motors can be fed by one or more power converters depending on one or multiple energy sources. Whether it is an airplane, an electric vehicle or a boat, several energy sources are available with different characteristics, operating modes and architectures. The most characteristic quantities are the voltage and the current levels requiring the use of specific power and passive components. The architecture design of these converters, whether forward, isolated or segmented, is a first issue that must be specific to the application. Another problem is the integration of static converters in order to increase their compactness (power-to-weight and power-to-volume ratios) because the high power and the low voltage imply very high currents which are not very favourable to a high efficiency and to a volume reduction. Of course, cost constraints are very important in the automotive field and must be integrated from the start of the design process.
The complex power conversion and management functions implemented in the vehicle concern the electric motor, its control electronics, the transmission and management of energy by the charger and the converters used to power the navigation and entertainment systems. All these elements are supplied with very low voltages ranging from 12 V to 48 V, sometimes 60 V, which leads to favouring the use of 100 V components. At the drive train level, it is recommended to stay at low voltage, in order to simplify the control and most important to optimise the efficiency and therefore enhance the autonomy by avoid putting converters in series to adapt the voltage levels (for example, low-voltage battery and high-voltage motor). In other words, it is better to avoid a DC/DC stage between the battery and the inverter and therefore to only have the inverter between the battery and the motor. Furthermore, in order to recover the energy during braking phases, the DC/DC converter has to be reversible which would make its design more complex. A classical architecture is given in Figure 9.
Example of a drive train with a single power inverter.
The electrical connection must also be appropriately designed because for a small vehicle, whether it is full electric or micro/mild hybrid type, with for example a power of around 30 kW at 48 V the currents are very high (650A for 48 V). The wiring with a large cross section must therefore be as short as possible and the inverter placed as close as possible to the motor and the battery, ideally in the same compartment and taking advantage of the car structure to dissipate the heat rejection.
Increasing the power of the electric motor quickly becomes a problem if the supply voltage does not increase proportionally because high DC bus and phase currents lead to an unreasonable increase in the number of semiconductor and passive components required. To reach the required switching capability, the surface area of the PCB, the volume of the cooling system and the size of the connectors should be increased accordingly, thus resulting in a weight increase of the electronic system and also a high cost incompatible with the requirements of the automotive field.
Alternatively, when the power becomes too high (at VLV) and therefore the currents are very high (>500A), the solution would be to segment the machine winding into many stars and supply them with several synchronised inverters as shown in Figure 10.
Distributed system for segmented winding.
In Figure 10, the power is shared between two inverters, which mean that there are not too many components in parallel in each inverter arm, and that the inverters are less complex, less cumbersome and easier to build, and, also, that the connections are less bulky with less losses.
The static converters contains power modules which allow the classical energy conversion functions (AC/DC or DC/AC) and which are generally designed based on two main categories of components, namely the MOSFETs (Metal Oxide Semiconductor Field Effect Transistor) for low voltage inverters or IGBTs (Insulated Gate Bipolar Transistor) for high voltage ones. The field of application and the necessary integration of this static converter make it possible to determine the most suitable components according to several parameters such as power and voltage as well as the switching frequency. Figure 11 gives a detailed breakdown of the use of these components.
Use of the different types of switchers depending on the application [
For electric vehicles, the silicon MOSFETs and IGBTs are mainly used. In this field, the battery DC voltage is switched at frequencies ranging from 5 to 20kHz. This switching level is usually achieved by the use of well-adapted control laws. The components required for the DC/AC conversion function are usually packaged in modules. The electric motor of a power train system is three-phase, this implies that the inverter structure must be composed of at least six switches that are bidirectional in current formed by the association of an IGBT with a freewheeling diode or MOSFET in parallel that are naturally bidirectional in current due to their intrinsic integrated diode.
It is also useful to keep in mind that failures can be experienced in a power converter, it is essential that the reliability of this power converter is as high as possible in the case of an electric vehicle for the obvious safety reasons. Several studies show that the power modules can be the most weak part of a converter [9, 10]. The causes of failure are mainly due to temperature (frequent thermal cycling of components and high steady state current), but also to moisture, vibrations and contaminations during the manufacturing process. The Figure 12 shows the results of two studies carried out on the failure modes of power converters.
Distribution of failure sources in a power converter [
The choice of a very low voltage supply, in this case 60 V, allows the use of commercial converters. However, as soon as the required power imposes a current higher than 500 A, it is necessary to design a bespoke power converter or, alternatively, to associate several of them in parallel. The technological constraints and standardisation lead to given silicon chip sizes which are then the building blocks of larger components. The increase in current capacity is thus achieved by combining elementary units in parallel.
Figure 13 shows some examples of power modules used in some conventional electrified vehicles.
Examples of inverters in the realm of electric vehicles [
We can note here that the semiconductors are associated in parallel in order to be able to switch important currents which depends on the power and the supply voltage of the machine and thus on the range of the EV (low range, high range, commercial vehicle...).
For example, the Tesla Model S has 10 IGBT chips per phase (i.e. 30 per module) to provide the 800 kW needed to power this vehicle whereas a Renault Zoé only needs 12 IGBT chips per module to ensure its nominal operation at 400 V/300 A.
The inverter should be compactly designed and should preferably be mounted as close as possible to the motor. The elements that contribute to the performance of the power module and therefore of the inverter are:
well-balanced current in the parallel MOSFETs,
low VDS peak at turn-off,
low Rdson when the MOSFETs are turned on,
low Rth of the heat sink.
In addition to conduction losses, switching losses must also be minimised to ensure optimum efficiency and minimal impact on the vehicle autonomy.
The design of the converter must also take into account the control boards, the drivers and the cooling system. Figure 14 shows the controller and driver circuitry for the Lexus hybrid vehicle.
Examples of controllers and driver circuitry [
Nowadays, new materials are emerging to replace silicon such as: silicon carbide (SiC) and Galium nitride (GaN). These materials allow higher switching frequencies, greatly reduced losses and higher operating temperatures resulting in more compact cooling systems, however, they also require a better control of the EMC and the PCB routing.
Many small electric vehicles (boat, kart, motorcycle, quad, cart, utility tricycle, small urban vehicle, unlicensed vehicle...) are equipped with an electrical motorisation with a power ranging from 10 kW to 30 kW. We present in this section a motor architecture optimised to operate at this power level and at very low voltage.
The winding technique for the electric motor is depicted in Figures 3 and 15, the slot copper bars are connected to each other at the end-windings via bridges bars located in two planes (crook bar and bow bar). In this case the overhangs are extremely compact. This configuration of the bars corresponds to the case number 1 in Tables 1 and 2.
Winding architecture - 20 kW very low voltage motor. (a) Winding layout, (b) 3D CAD view of the wound stator.
To optimise the manufacturing costs, all motors in this power range will use the same stator laminations, the same number of poles; hence, the number of bars is always the same, only the length of the stator stack is likely to evolve in order to comply with the different specifications, we will be giving two examples.
The motors are assembled in square shaped housing (212x212 mm2 CSA), as shown in Figure 16.
A motor portfolio with a power ranging from 10 kW to 30 kW, operating at very low voltage (courtesy of SMVE performance SAS).
The first specification we present is related to a marine outboard motor (electric boat), where the nominal speed of the propeller is 1750 rpm, with a reduction ratio of the transmission angle equal to 2.
The simplified specifications of the motor are as follows:
Rated power: 10 kW
Nominal speed: 3500 rpm
Power supply voltage: 50 VDC
Efficiency: greater than 90%
There is no need here to detail the EMAG sizing of the motor, which is conventional and does not fit the main purpose of this chapter. The following Table 3 summarises all the main characteristics of the motor.
Stator outer diameter | 208 mm |
Stator inner diameter | 172 mm |
Magnetic airgap length | 1,5 mm |
Magnet height | 6 mm |
Stator stack length | 35 mm |
Winding bar dimensions (hxw) | 4x5 mm |
Slot dimensions (hxw) | 4,8x5,8 mm |
Stator corepack | M270-35A |
Magnets | N35UH |
Pole number | 16 |
Slot number | 48 |
Phase rated current | 240A RMS |
Phase resistance (AC, KAC = 1,05), 20°C - 100°C | 1,3 mΩ - 1,7 mΩ |
Torque coefficient kt | 0,113 Nm/A |
Total weight (including mechanics) | 8 kg |
Nominal torque-to-weight ratio | 3.3 Nm/kg |
Joule losses (at 100°C) | 300 W |
Iron losses + mechanical losses | 250 W |
Efficiency | 95% |
Cooling method | Natural convection |
Characteristics of the electric boat motor.
This first case of sizing shows that even with a relatively low nominal operating speed, it is possible to reach high specific performances where, in particular, the power density is higher than 1 kW/kg, without impairing the efficiency. The latter is a key performance in the case of electric boat where the nominal speed corresponds to a permanent operating speed because the vehicle regime is stable during the navigation.
For this second studied case, we use the same motor structure, but considering a much higher power, adapted to the motorisation of a small sport vehicle, a kart for example.
The simplified specifications of the motor are as follows:
Maximum power: 25 kW
Maximum speed: 6000 rpm
Power supply voltage: 60 VDC
Efficiency: greater than 90%
The following Table 4 summarises the characteristics of the motor designed for this specification. The laminations are identical to those of the previous case (electric boat Section 4.1).
Stator stack length | 28 mm |
Pole number | 16 |
Slot number | 48 |
Phase rated current | 490A RMS |
Phase resistance (AC, KAC = 1,35), 20°C - 100°C | 1,3 mΩ - 1,7 mΩ |
Torque coefficient kt | 0,082 Nm/A |
Total weight (including mechanics) | 7 kg |
Nominal torque-to-weight ratio | 5,7 Nm/kg |
Joule losses (at 100 °C) | 1220W |
Iron losses + mechanical losses | 500 W |
Efficiency | 94% |
Cooling method | Natural convection |
Characteristics of the electric kart motor.
This sizing case is extreme, because, given the power, we are at the limit of feasibility at VLV, especially if we consider the phase current reaching 500 A. However, contrary to the previous case, the maximum power is transient because the speed of a small sport car is very variable on a winding track, the thermal steady state depends on the nature of the latter.
Even though the efficiency remains good, the losses at maximum power are high, more than 2 kW, but in this vehicle the motor is located outside and will be naturally cooled by a large amount of air flow (Figure 17). The maximum speed of the vehicle is well above 100 km/h, a natural convection cooling is sufficient. Furthermore, the heat exchange is improved by the very low copper to iron thermal resistance.
Electric kart.
This application illustrates the implementation of the concept for a motor operating at very high electrical frequency for an aeronautical application. It is a laboratory study [1] based on the motorisation specification of one of the first industrial all-electric aircraft, namely the Efan, from AIRBUS (Figure 18). The project was quickly abandoned by AIRBUS, but it was taken up by several other companies, and some versions are now offered for sale to the aero clubs.
Prototype Efan (courtesy of AIRBUS).
The power supply voltage of the Efan motor was equal to 300 V, we think that a VLV version would make sense to facilitate the maintenance operations of the aircraft, if it is particularly used in the aero clubs. This approach is all the more interesting as it also allows the search for very high specific performances thanks to the properties of the winding with only one solid bar per slot. The weight of the motor is, of course, one of the first sizing criteria.
To maximise the power-to-weight ratio, we have designed an electric motor operating at high frequency. The winding structure is special [1, 4, 5, 14], where the phases are arranged in six separate sectors, the electrical phase shift is ensured by introducing an intermediate irregular tooth, as illustrated in Figures 4,19 and 20. This winding design allows, on the one hand, to keep a limited number of slots (36 slots), despite the large number of poles (40 poles), and, on the other hand, to avoid the end-windings overlaps, resulting in very short overhangs.
Structure of the “per group” winding.
High frequency electric motor prototype. (a) Wound stator. (b) Rotor assembly.
The simplified specifications are as follows:
Maximum power: 26 kW
Maximum speed: 5000 rpm
Power supply voltage: 80 VDC
Weight: less than 7 kg
Efficiency: greater than 92%
The Table 5 shows the main characteristics of the electric motor.
Stator outer diameter | 137 mm |
Stator inner diameter | 120mm |
Magnetic airgap length | 1 mm |
Stator stack length | 92 mm |
Winding bar dimensions (hxw) | 3x5 mm |
Slot dimensions (hxw) | 4x6 mm |
Stator corepack | Iron-Cobalt, 0,2 mm |
Magnets | N35EH |
Pole / slot number | 40 / 36 |
Phase rated current | 400 A RMS |
Phase resistance (AC, KAC = 1,44), 20 °C - 100 °C | 1,85 mΩ - 2,44 mΩ |
Torque coefficient kt | 0,125 Nm/A |
Total weight (including mechanics) | 6 kg |
Nominal torque-to-weight ratio | 8.3 Nm/kg |
Nominal power-to-weight ratio | 4,3 kW/kg |
Joule losses (at 100 °C) | 1200 W |
Iron losses + mechanical losses | 400 W |
Efficiency | 94% |
Cooling method | Natural convection |
Characteristics of the electric aircraft motor.
The structure with large number of poles allows to obtain high specific power, more than 4 kW/kg. The VLV winding contributes to this level of performance without compromising the efficiency. The additional loss coefficient, KAC, remains moderate despite operating at a frequency of 1666 Hz. As the motor is placed behind the propulsion propeller, the 1600Wof total losses will be easily evacuated.
When the required power of the vehicle motorisation exceeds the threshold of 30 kW (approximate), it becomes difficult, if not impossible, to supply the motor with a single controller because the phase currents become prohibitive at VLV. The two examples discussed in this paragraph show how to solve this problem using power partitioning.
The first considered case of high power motorisation is that of a rally type sporty vehicle (Figure 21).
Sporty full electric vehicle.
The simplified specifications of the motor are as follows:
Maximum power: 100 kW
Maximum speed: 5000 t/mn
Power supply voltage: 100 VDC
In order to divide the power supplied to the motor, the winding was designed based on the technique described earlier in Figure 15, and is split into two electrically isolated stars, as depicted in the following Figure 22; each half-winding being fed by a dedicated controller and delivering half of the total required power.
Dual stars winding layout.
Table 6 summarises all the main characteristics of the electric motor. In this case, we are using the solid bar configuration corresponding to case 3 in Table 2.
Stator outer diameter | 204 mm |
Stator inner diameter | 156 mm |
Magnetic airgap length | 2 mm |
Magnet height | 5 mm |
Stator stack length | 175 mm |
Winding bar dimensions (hxw) | 8x4 mm |
Slot dimensions (hxw) | 9x5 mm |
Stator corepack | M270-35A |
Magnets | N35UH |
Pole number | 16 |
Slot number | 48 |
Phase rated current | 650 A RMS |
Phase resistance (AC, KAC = 2,39 - 2 x 3 phase), 20 °C - 100 °C | 1,85 mΩ - 2,4 mΩ |
Torque coefficient kt | 0,46 Nm/A |
Total weight (including mechanics) | 40 kg |
Nominal torque-to-weight ratio | 7,5 Nm/kg |
Joule losses (at 100 °C) | 6000 W |
Iron losses + mechanical losses | 1400 W |
Efficiency | 95% |
Cooling method | Natural convection |
Characteristics of the sporty vehicle electric motor.
The losses at simultaneously maximum power and maximum speed are too high, more than 7 kW, particularly due to a high KAC coefficient, but this is only a transient regime occurring during the acceleration phase. Again, here the steady-state thermal behaviour also depends on the nature of the track which cannot be defined a priori, but in all cases the efficiency is high and greater than 95%. However, at low speed acceleration, the copper losses are halved at constant current because the KAC coefficient tends towards 1, the efficiency, therefore, remains high over a wide speed range. The partition of the power on multiple converters makes it possible to reduce the phase current to 650 A during the transient regime. The bar winding has allowed the design of a very compact motor reaching high power density (4 kW / kg in transient regime).
The second example of power partitioning is that of an utility vehicle, an electric tractor for winegrowers (Figure 23).
This tractor is equipped with four electrified wheels fully independent. The topology of the motors is very similar to that described in section 4. The solid bars configuration corresponds to line 4 of Tables 1 and 2. The four electric motors drive the wheels via a gearbox with a reduction ratio of 1/40.
The simplified specifications of the motors are as follows:
Maximum power: 40 kW
Rated power: 5 kW
Maximum speed: 4000 rpm
Nominal speed: 1000 rpm
Power supply voltage: 80 VDC
The nominal operating condition of the electric tractor corresponds to the ploughing phase, where the displacement speed is low and the total required mechanical power does not exceed 20 kW. The tractive force applied on the plough is approximately 16 kN. The sizing was carried out based on the tractor behaviour with a conventional thermal engine.
The power partition, via the use of four electric motors, enables to have a significant power available for the transient mode, approximately 160 kW, thanks to the capacity of over-torque necessary for obstacles clearing and vehicle overspeed during the road trips. During the latter operating conditions, the motors are running without flux weakening. However, this high power is only used very rarely, and only temporarily, in the case of transporting heavy loads on steeply sloping roads.
The efficiency of each electric motor at the nominal conditions, at low speed and at an output torque of 50 Nm per motor, is about 95% and this because the copper losses in the 24 mm2 solid bars are very low due to the very low electrical frequency (133 Hz).
Electric tractor.
According to the various examples discussed in this chapter, it can be seen that it is possible to design an electric vehicle drive train operating at very low voltage (battery voltage below 120 VDC) and over a wide power range (up to 100 kW). An original, compact and high efficiency motorisation solution using a solid bar winding has been presented. In all the cases, the sizing constraints of the motor controller have been taken into account.
alternating current, alternating voltage direct current, direct voltage skin depth in AC mode Electromagnetic Electromagnetic Compatibility solid bar height slot height Insulated Gate Bipolar Transistor current density additional loss coefficient AC / DC Metal Oxide Semiconductor Field Effect Transistor Joule AC losses in conductors Joule DC losses in conductors Printed Circuit Board MOSFET drain source electrical resistance heat sink thermal resistance copper fill factor solid bar width slot width MOSFET drain source voltage Very Low Voltage
Over the past few decades, functional ceramics have played a significant role in advanced technologies owing to their unique thermal, electrical, magnetic, opto-electrical, superconducting and gas-sensing properties. As such, functional ceramics have become the frontiers for advanced technologies such as information technology, medical technology, energy transformation, storage, supply and manufacture technology. For instance, functional ceramics are widely used for electronic applications as they can operate at high power and high frequencies, at high temperatures and harsh conditions. Their capability to combine properties such as electrical insulation and magnetism, which is not possible with metals, gives them an additive advantage.
Functional ceramics are produced from chemically synthesised powders in the form of oxides, nitrides, carbides and borides mainly through a powder metallurgy route. The properties of functional ceramics are microstructure sensitive, and microstructural features such as grain size, composition, homogeneity and grain boundary constituents are critical to their performance and reliability. The processing route dictates the final microstructural features obtained; thus, the choice/design of a processing route is key in material functionality. For instance, fine grain size has been experimentally proven to amplify functional material properties such as electrical conductivity, thermal conductivity, piezoelectric and ferroelectric properties [1]. It must be mentioned though that the fabrication of dense nanostructured functional ceramics by conventional sintering methods is quite challenging owing to the uncontrollable high grain growth rates [2]. This explains the shift in research focus towards nanostructured functional materials in the past few years.
In recent years, spark plasma sintering (SPS) technology has proven its capability to fabricate fine-grained microstructures possessing superior properties for a wide range of materials [2]. This method is increasingly being applied in the production of functional ceramic materials. It is against this background that the present chapter is aimed at giving an insight on the progress made so far and, furthermore, how the resulting microstructures and properties align with the required functions. It is imperative that a background on the various applications of functional ceramics be given prior to a detailed discussion on the SPS sintering methodologies.
Functional ceramics are materials tailored to possess exceptional properties (electrical, thermal, optical, piezoelectric and magnetic properties) by controlling the composition and microstructures [3]. These materials are being utilised in a broad range of applications owing to the distinct advantages they offer in comparison to metals. The list below is not meant to be exhaustive but to give a qualitative review on the applications of the most popular functional ceramic materials.
Piezoelectric ceramic materials couple electrical and mechanical responses in their functioning and are widely used for electromechanical sensors and actuators. These materials normally produce an electrical response in the form of either a voltage or charge proportional to the applied stress when subjected to a mechanical force. Conversely, an applied voltage can be converted into mechanical energy such as in piezoelectric motors and sound-/ultrasound-generating devices. Piezoelectric materials are widely used in dynamic applications which include mechanical impact, ignition systems, vibration suppression and sensing [4]. Typical examples of piezoelectric materials include crystalline quartz, barium titanate (BaTiO3), vanadium niobate and lead zirconate titanate (PZT) [3]. In recent years, research focus on lead-free piezoelectric materials has been intensified aimed at replacing lead-based materials in electronic devices for the sake of human health and preservation of the natural environment [5].
Piezoelectric materials are produced as multilayered components consisting of electrode-ceramic stacks which can be simple/complex shapes. Various techniques have been developed to fabricate the piezoelectric ceramics without conducting post-processing. These include injection moulding [6, 7], embossing [8] and fused deposition method [9]. The powder injection moulding (PIM) process has received much attention owing to its ability to produce complex-shaped, micro-sized PZT components with minimum damage to the sintered ceramic [10]. The multilayered components are subsequently co-sintered at temperatures less than the melting point of the electrodes typically 1200–1300°C. However, lower sintering temperatures are preferred to avoid damaging the inner electrodes in the stack. It has been observed that the piezoelectric coefficient which directly influences the performance of piezoceramics is strongly influenced by the grain size [11]. Despite the extensive studies carried out over the past decades on the grain size effects on the physical properties of these materials, there are still major controversies on the dependence of piezoelectric and ferroelectric properties on the grain size [12]. There are a number of discrepancies in the existing literature which will be discussed later in this chapter.
Magnetic ceramic materials are extensively used in electronics and information communication fields [13]. They are generally classified as ‘soft’ and ‘hard’ magnets where soft implies large magnetic fields cannot be generated on the outside, whereas in the case of hard magnets, a magnetic field is generated around the magnet itself. Two broad groups of materials are widely used in the industry, i.e. metal magnetic materials and complex oxide containing trivalent iron ion (ferrites) magnetic materials (referred to as ceramic magnets).
Magnetic materials are generally used in the form of multilayer core of rolled thin plates or in the form of dust core [13]. At high frequencies, most metallic magnets tend to lose their magnetic properties (permeability and magnetic flux density) due to low electrical resistivity. On the other hand, ferrites (ceramic magnets) show higher electrical resistivity and smaller eddy current loss at high frequencies; hence, they are more widely used in alternating magnetic fields in comparison to metal magnetic materials. The hard ferrite is used extensively as permanent magnets for speakers and motors. One of the critical magnetic characteristics required for high-frequency materials is high permeability and is defined as the ratio between the magnetic flux density,
Permeability is a structure sensitive characteristic and is strongly affected by the microstructure of the sintered material. There are two general compositions used for oxide magnetic materials, spinel type (MeFe2O3) and garnet type (Me3Fe5O12); typical examples include MnFe2O4 and Y3Fe5O12, respectively. Owing to the complex compositional nature of these oxides, a powder metallurgy route is normally employed for the production of oxide magnets. The microstructure and compositional control are quite critical elements of the magnetic properties of the final products. Further, magnetic properties of materials have been shown to change from those of multidomain to those of single-domain structure as the grain size is reduced below a critical size [14]. The introduction of fine-grained sintered magnetic materials has opened some opportunity for new potential applications as well as complexity on basic research [14].
In the last few decades, the rapid development of modern communication devices such as cellular telephones, antennas and global positioning systems has energised research in microwave dielectric materials [15]. Dielectric ceramics are materials used widely in advanced electronic devices such as capacitors and microwave resonators. They are classified into two broad groups based on their dielectric properties. High-quality factor materials are characterised by linear changes in polarisation with applied electric field. This group is dominated by titanate-based materials which normally sinter at temperatures higher than 1100°C; typical examples include TiO2, MgTiO3, CaTiO3 and SrTiO3 [13]. This group is characterised by a dielectric constant
Ceramic capacitors are widely produced as sintered thin plates in a reducing atmosphere (low
Thermoelectric (TE) ceramic materials can directly convert heat energy to electric energy due to thermoelectric effects [16]. TEs provide an alternative environmentally friendly energy conversion technology which is compact, high reliability, has no pollutants and is feasible over a wide temperature range. The majority of thermoelectric devices operating near room temperature are based on Bismuth telluride (Bi2Te3) and its alloys. These materials have been produced by a variety of methods which include powder metallurgy techniques such as hot pressing (HP), SPS, Bridgman and zone melting and high-pressure sintering methods. Recent studies have shown that grain refinement of Bi2Te3-based alloys can greatly enhance thermoelectric performance [16]. The performance of thermoelectric materials is based on a dimensionless figure of merit (ZT) as follows:
where
Thermal conductivity of TE materials consist of two parts: lattice thermal conductivity (
Over the years, a number of strategies have been adopted to enhance the power factor and reduce thermal conductivity of TEs. This has resulted in the development of three generations of TEs over the 200-year period since their discovery in 1821. The development history has been characterised by achieving high ZTs > 2.0 through new concepts and technologies. The first TE generation devices are characterised by ZT ~ 1.0 operating at power conversion efficiencies of 4–5% [17]. In the 1990s the introduction of nanostructures increased the ZT values by about 70% to ZT ~ 1.7, and the power conversion efficiencies can be expected to be 11–15%. In the third generation, some new concepts such as band structure engineering by doping, reduction in lattice thermal conductivity, nanostructuring and all-scale hierarchical architecturing and quantum confinement effects have been introduced to enhance Seebeck coefficients [16].
It is apparent that the increasing demand for ceramic materials in more advanced technological applications has resulted in greater need for improved properties and reliability of functional materials [2, 13]. The fabrication process plays a critical role in final material characteristics. In other words, the properties of ceramic materials are dictated by the microstructure which is a function of the processing method utilised. Thus microstructures can be tailored through fabrication processes to produce desired properties. In the past few decades, there has been a wide acceptance among powder metallurgists that the quality and reliability of ceramic materials are largely dictated by utilising powders of controlled purity, particle size and size distribution, shape and degree of agglomeration. The characteristics of starting powders are determined by their production method of which a variety of methods are available for the production of ceramic materials. The processing methods are broadly classified into solid-state processing (e.g. mechanical alloying, self-propagating high-temperature synthesis (SHS), laser ablation) and solution chemistry (e.g. sol-gel, polymer pyrolysis, hydrothermal methods) [2]. The chemical processing methods are generally more expensive than solid-state methods but offer more strict control of the powder characteristic [13]. The choice of a powder processing route will therefore largely depend on the production cost and its capability to achieve desired powder characteristics.
Chemical methods involving chemical reactions under carefully controlled conditions normally result in ultrafine nanometric powders (<100 nm) with a narrow particle size distribution [13]. The main attraction in using nanometric powders is their ability to sinter at lower temperatures (typically <0.5 Tm); this is in accordance with Hering’s law discussed in the next section. The diffusion distance during sintering is drastically shortened in nanostructured powders. Moreover, an enhancement of material properties is expected owing to a reduction in the flaw size, and a higher density of highly disordered interfaces is also attained at nanometric particle size range. On the other hand, powders produced by mechanical methods possess a wide particle size distribution which may lead to higher packing density in the green body. However, this advantage is far outweighed by the difficulty in microstructural control during sintering as large grains grow uncontrollably at the expense of the smaller grains, thus making grain size control impossible. However, it is important to underline that as particle size decreases, below ~0.5 μm, particles become more difficult to handle and tend to agglomerate resulting in nonuniform consolidation of powders. Thus the use of nanopowders requires proper control and handling to ensure high-quality properties are attained in the final products.
In 1906, Bloxam filed the first patent on the successful consolidation of powder using the SPS technology [20]. Steady progress was made in the mid-1980s into the 1990s. The SPS technology sinters in a conducting die with a simultaneously applied mechanical pressure and DC pulses which allows for simultaneous densification and sintering process [21]. The SPS set-up consists of a graphite die filled with powder feedstock, uniaxial hydraulic pressing device which achieves 50–250 kN and an electric pulse current of low voltage (<10V) and high currents (1–10 kA) [2]. The system has achieved heating rates of up to 1000°C/min which makes it possible to sinter over very short durations [22]. It can be operated under vacuum or inert gas atmosphere at atmospheric pressure with a maximum temperature of 2400°C.
The sintering mechanisms in SPS are a result of three effects, namely, mechanical, thermal and electrical [2]. The fast heating rates achieved in SPS enables densification while retarding microstructure coarsening owing to the short times required to reach sintering temperature. This allows for the densification of nanopowders with minimal grain coarsening [22]. The SPS system offers a number of advantages over the conventional sintering systems such as hot pressing, hot isostatic pressing (HIP) which include high sintering speeds, high reproducibility, better control of sintering energy and reliability.
The mechanism of sintering is not well understood but several authors have postulated a number of theories. The widely accepted SPS sintering mechanisms involve joule heating, plasma generation and electroplastic effect [2]. The electrical effects are a function of the electrical properties of the powders. For powders that are electrically conducting, current can easily flow through, and heat is generated mainly by joule heating and transferred to the bulk of the powder by conduction (see Figure 1) [23]. In the presence of an applied pressure, the electric current through the particles enhances formation of interparticle bonds through localised welding, vaporisation or cleaning of powder surfaces [22]. This ensures a smoother and more favourable path for the current flow. This also promotes the production of high-quality sintered compacts at lower temperatures in a shorter time than conventional sintering methods. The sintering of nonconducting powders, although not well understood, is thought to occur through grain boundary migration and matter transport at higher input voltages.
Pulse current flow through the spark plasma sintering technology [
Although the SPS has the capability to sinter at high heating and cooling rates, the expectation is that the system can sinter without appreciable grain growth. However in reality this is not always the case; a complete avoidance of the grain growth at the sintering temperatures for most nano-grained materials will always promote grain growth. It is therefore imperative to adopt an approach/methodology that is more effective in minimising grain growth using the SPS system. The
The reliability of ceramic materials is a key function, and it dictates their ultimate performance. A carefully controlled microstructure has a greater impact on the properties and reliability of functional ceramic materials. In the previous section, it has been shown that the development of highly dense nanometric or ultrafine-grain-sized ceramics is not easily achievable through conventional sintering. Although the SPS technology has shown great potential in the production of highly dense nanometric materials, it is difficult to maintain microstructural refinement under the high sintering temperatures. It must be underlined that solid-phase sintering requires high temperatures to facilitate diffusion which promotes material densification. However diffusion processes promote not only densification but also grain growth [24]. To achieve grain refinement during sintering, it is therefore imperative to develop a sintering methodology which promotes only densification without stimulating grain growth. This method has been improved over the years to achieve better microstructural refinement. The so-called two-step sintering (TSS) was subsequently introduced in the 1990s by Chu et al. [25]. In essence, the technique consists of two stages of consolidation process, i.e. a first stage performed at relatively low temperature followed by a higher-temperature stage and subsequent cooling.
However, the higher-temperature stage if not adequately controlled can lead to some grain growth. In 2000, Chen and Wang proposed a modified TSS methodology which effectively suppresses the accelerated grain growth in the second stage [24, 26]. In the modified TSS approach, a high-temperature heating is performed first for a short duration followed by structural freezing and sintering at a lower temperature. The idea of heating to a higher temperature (T1) followed by fast cooling with no sintering holding time (stage 1 in Figure 2) is to eliminate residual porosity at higher temperature and develop a network of grain boundary anchoring at triple points [11].
Schematic illustration of the differences between the two TSS approaches [
These anchored triple points are thought to have higher activation energy for matter migration than the grain boundaries. The second step effectively proceeds in a
The use of the TSS methodology to obtain ceramic materials of controlled microstructure has become standard practice. This section gives a detailed discussion on the effects of processing characteristics on grain density and size as well as their contribution to the improvement of mechanical properties of a number of functional ceramic materials investigated in previous studies.
The pioneering work of Cheng and Wang in 2000 serves as the beginning of a new era in TSS methodology. In one of their successful studies, Chen and Wang obtained a density of 99% and a grain size of 123 nm using a T1 temperature of 1250°C and T2 temperature of 1100°C for a pure Y2O3 ceramic material [24, 26]. After several experimental studies, Chen and Wang concluded that the success of grain growth suppression in their work was mainly attributed to triple-point immobility irrespective of whether doping agents were used or not [11]. In a separate study, Mazaheri et al. [29] obtained dense samples of ZnO with limited grain growth under varying conditions. The starting particle size of the ZnO was 31 nm. The most interesting result was obtained with a T1 of 800°C and T2 of 750°C; a relative density and grain size of 98% and ~68 nm were obtained, respectively [29]. The same authors proved that slightly higher temperatures (850°C and 780°C for T1 and T2, respectively) resulted in grain growth and a lower densification of 86% using ZnO material [29]. A further study done at even higher temperatures, with a starting ZnO powder of grain size of 400 nm (0.4 μm) and a T1 of 1100°C and T2 of 1050°C, resulted in a relative density of 95.1% and a grain size of 3.9 μm, signifying the ineffectiveness of the TSS methodology at higher sintering temperatures and larger particle sizes. Several other TSS studies carried out on the ZnO material proved that the use of dopant agents such as Bi2O3, Sb2O3, CoO and MnO assisted in suppressing grain growth [11].
Yttria-stabilised ZrO2 (YSZ) is one of the most important functional ceramics which find its use in a wide range of applications. Several attempts have been focused on attaining nanometric YSZ materials to improve its functional properties. Mazaheri et al. [30] obtained fully densified 3YSZ with an initial grain size of 75 nm and a pressureless sintering regime of T2 (1150°C) and T1 (1300°C) with an isothermal holding time of 30 h at T2 and 1 min holding time at T1. The final grain size achieved was 110 nm. In a separate study, Suarez compared SPS sintering with pressureless TSS methodologies. The starting material was a three Y2O3-stabilised tetragonal ZrO2 (3YTZ) with an initial average particle size of 65 nm. The TSS methodology used a pressureless sintering regime as T1 at 1350°C without holding time and T2 at 1200°C for 15 h, and a final grain size of 125 nm was obtained. On the other hand, the SPS method was carried out at 1150°C with a heating rate of 300°C/min and an isothermal holding time of 30 mins at a pressure of 150 MPa. The grain size obtained was 115 nm. Several other modifications as summarised in Table 1 were carried out, and an observation that was common to the majority of the studies is that the homogeneity of the green body was very critical to the success of the sintering method in its effectiveness of grain growth control [11].
Sample | Method | Starting grain size (nm) | Pressure (MPa) | T1 profile (°C) | T2 profile (°C) | Relative density (%) | Grain size | Ref |
---|---|---|---|---|---|---|---|---|
Pure Y2O3 | TSS | 10–60 | — | 10°C/min to 1250 | 50°C/min to 1100, 6–30 h dwell | 99 | 123 nm | [24, 26] |
Pure ZnO | TSS | 31 | — | 800 | 750 | 98 | 680 nm | [29] |
Pure ZnO | TSS | 400 | — | 1100 | 1050 | 95.1 | 3.9 μm | [34] |
3YSZ* | TSS | 0.27 μm | — | 1500 (5 min) 10°C/min | 1300, 10 h | — | 0.59 μm | [35] |
3YSZ | TSS | 75 | 150 | 1300, 1 min | 1150, 30 h | Density at T1 (83) | 110 nm | [30] |
3YSZ | SPS | 65 | 150 | — | 1150, 150 MPa, 300°C/min, 30 min | — | 115 nm | [36] |
3YSZ | TSS | 65 | — | 1300 | 1200, 15 h | — | — | [36] |
3YSZ | TSS | 60–120 | — | 1300, 10°C/m | 1175, 20 h | 99.2 | 184 nm | [37] |
3YSZ | H-SPS | 60–120 | 100 at 600°C, 3 min | 300 MPa at 1000, 5 min | 1175, 300 MPa, 30 h | 97.4 | 173 nm | [37] |
8YSZ | SPS | 58 | 50, 15 min | 1150, 200 °C/min, 20 s, 10 MPa | 1050, 50 MPa, 2 h | 99.8 | 190 nm | [38] |
A summary of the two-step methodology used to produce different materials.
3YSZ, 3 mol% Y2O3-stabilised ZrO2.
As mentioned earlier, piezoelectric materials’ performance is strongly influenced by the grain size of the constituent particles making up the ceramics. High-performing piezoceramics have been obtained using the TSS approach. A number of studies have shown that lower sintering temperatures using the TSS methodology can be utilised to obtain ultrafine grain sizes. BaTiO3 is one of the most popular piezoceramics studied, and a number of studies have been carried out to obtain fine-grained microstructures. In their work, Kim and Han [31] used a 1% dysprosium (Dy)-doped BaTiO3 with a particle size of approximately 17 nm which was compacted at 300 MPa at room temperature. The TSS profile used a T1 of 1300°C and a T2 of 1100°C with a 20 h holding time. A grain size close to 1 μm was obtained at a relative density of 95%. In a separate study, Wang et al. [32] studied two different piezoceramic composites, i.e. pure BaTiO3 with a particle size between 10 nm and 30 nm and a nanometric ferrite of composition Ni0.2Cu0.2Zn0.6Fe2O4 with a starting particle size of 10 nm. The two powders were compacted isostatically at 200 MPa. The two piezoceramics were sintered using two different sintering programmes, i.e. a T1 of 950–1250°C for BaTiO3 and at 850–930°C for ferrite; a cooling rate of 10°C/min was used in both cases. The samples were cooled at 30°C/min to a T2 range of 1150–850°C for BaTiO3 and 750–870°C for the ferrite with an isothermal holding time of 20 h. For the BaTiO3, the best result achieved showed a grain size of 35 nm and was sintered at 950°C in T1 and at 900°C in T2 for 2 h. On the other hand, a grain size of 200 nm was achieved for the ferrite sintered at 850°C in T1 and 800°C for 6 h in T2. In comparison to the result of Kim and Han discussed earlier, the use of a lower sintering temperature enabled the formation of BaTiO3 with a finer grain size. To elucidate this point, Karaki et al. [33] obtained a mean grain size of 1.6 μm with a relative density of 98.3% starting with a BaTiO3 of average particle size of 100 nm, cold compacted at 200 MPa. A TSS profile almost similar to that of Kim and Han et al. consists of a heating rate of 10°C/min to T1 (1230–1340°C) held for 1 min and a cooling rate of 30°C/min to T2 (1150–1200°C) held for 2, 4, 5 and 20 h. The best result was obtained with a sintering profile consisting of T1 (1320°C) and T2 (1150°C) with a 15 h holding time. There is a clear indication from the above results that BaTiO3 ceramics with high sintered density are obtainable at lower sintering temperature (≤1000°C) for both T1 and T2. Some of the authors observed that the piezoelectric coefficient is strongly influenced by the grain size [11]. Nanometric BaTiO3 ceramics possess superior piezoelectric coefficients in comparison to their micrometric counterparts.
As mentioned earlier, the current work is not meant to be exhaustive but to give a qualitative insight on the research covered so far. Table 1 gives a summary of some of the successful work carried out and highlights some critical aspects in the TSS methodology as a grain refinement process.
Specific particularities were observed in each of the sintering cycles above. The majority of the authors compared their results with those obtained by conventional sintering and the TSS methodology resulted in superior grain refinement. The initial powder features such as particle size, microstructural homogeneity and green density are quite critical in the success of the TSS process. In the majority of cases, the difference between the T1 and T2 temperatures is <1500°C, and a larger holding time in T2 allowed smaller grain sizes to be obtained. The TSS method has also been shown to improve the material properties (both mechanical and physical).
In some cases the use of dopants was effective in inhibiting grain growth. Although the TSS approach has shown great success in effecting grain refinement, the very long isothermal holding times at T2 might not be suitable for commercial purposes. The SPS technology offers an alternative route for grain refinement, and results in Table 1 show that it is more effective for materials such as YSZ ceramics. The SPS process generally can achieve grain refinement over shorter time periods.
SPS technology provides an alternative and more effective route for grain refinement of ceramic materials. As discussed earlier, conventional sintering is ineffective in refinement of ceramic materials owing to the excessive grain growth of fine powders at elevated temperatures [20, 21, 22]. The TSS methodology was developed to mitigate this problem, and it provides a low-cost and effective route for grain refinement. However, this method requires very long isothermal holding times to effect sintering without grain growth. Therefore, it might not be suitable for high production rates (commercial purposes); in addition the prolonged holding times are likely to increase the energy costs. Moreover, there are ceramics that require pressure-assisted sintering to impart the required strength to the component during sintering. The shortcomings above can be minimised with the use of SPS technology which has been briefly discussed in the previous section.
The SPS technology has been successfully used in the production of nanometric functional ceramic materials. The discussion below presents some examples where SPS has been utilised to obtain bulk ceramic nanomaterials. The discussion is not meant to be exhaustive but to impart some critical in-depth knowledge on the synthesis procedures of a few selected case studies.
The magnetic properties of ferrites (magnetic ceramics) are structure sensitive and are affected by a number of factors such as phase composition, crystallite size and shape and the quantity of heterogeneities [39]. It is therefore critical to use a synthesis method capable of producing superior magnetic properties through control of structural homogeneities. The use of SPS technology is thought to promote ordering of spatial positions of magnetic moments of metal ions in the composite crystal lattice through pressure-assisted sintering [40]. The result is the formation of new magnetic phases through a pressure-induced transformation of the nanocrystalline phases [39]. It must be noted however that the mechanism of this transformation in SPS is not well developed for most of the ceramic ferrites.
Papynov and co-workers studied the magnetic properties of nanostructured ferrites using SPS technology (α-Fe2O3 and α-Fe2O3-Fe3O4 composite) [39]. The authors established that the value of magnetisation increases significantly with increasing sintering temperature and reached a value of 10.2 emu/g at 1100°C (equivalent to a tenfold increase). This was attributed to changes in the crystalline phase and to a lesser extent growth of ferrite grains which may affect magnetisation.
In their work Gaudisson et al. [41] consolidated a nanosized magnetic powder into a high-density solid at 750°C for 15 min to a final grain size range of 150 nm. In a separate study, a nanostructured Co-ferrite was shown to be sensitive to heating rate under the same sintering temperatures and times in SPS. A higher heating rate (80°C/min) maintained a finer grain size of 70 nm than a lower heating rate (15°C/min) which produced a grain size of 290 nm for two powders which were processed at the same sintering temperatures and times (2 min at 600°C followed by 5 min at 500°C) [41]. Ultrafine, highly dense yttrium iron garnet (YIG) was produced by SPS treatment at 750°C for 15 min at 100 MPa in wide contrast to the typical parameters used in conventional sintering which requires higher sintering times (typically 1350°C for a few hours) [42].
A SrFe12O19 hexaferrite with a grain size of 400 nm was obtained using SPS at 1100°C for 5 min with a maximum density of 5.15 g/cm3. There was a big contrast with conventional sintering at 1240°C for 2 h which produced a density of 4.83 g/cm3 and a grain size double that of the SPS-produced material [43]. Harder magnetic properties were obtained from the SPS-produced ferrite. In another study, harder magnetic properties were obtained for an SPS-sintered Ba-hexaferrite owing to limited grain growth; grains of 100–150 nm were obtained in comparison to conventional sintering which produced a grain size of 1.5–8 μm [44].
The grain size effect on the macroscopic functional properties of piezoceramics has been widely researched. There are however very few studies that correlate grain size and property stability. It has been shown that improved performance, high permittivity miniaturised devices can be obtained by microstructural control such as grain size and homogeneity [45]. Arlt and co-workers have shown the strong dependency of BaTiO3 functional properties on the microstructure and grain size [46]. Moreover, large grain sizes are detrimental to the mechanical strength of ceramic-based devices. Several studies have been dedicated towards investigating the effect of grain size on the piezoelectric properties of BaTiO3 ceramics down to nanometric scale.
BaTiO3-based piezoceramics is one of the most studied using SPS. It has been demonstrated that SPS technology is effective in stabilising the metastable BaTiO3 cubic phase and reducing the intergranular effects on permittivity and DC resistance [45]. Moreover, SPS samples have shown higher permittivity values typically below the Curie temperature (Tc) [47]. It has been demonstrated that at finer grain sizes, the dielectric constant at the transition temperature decreases and Tc shifts to lower temperatures [45].
Lead-based piezoceramics have dominated the market of piezoelectric ceramics for a long time. However, their continued use is now questionable owing to the associated health risk especially during processing. Another major concern in the sintering of PZT piezoceramics (Pb(Zr,Ti)O3) is the high sintering temperatures which promote the vitalization of lead [48, 49]. Moreover, a number of the proposed alternative piezoceramic materials also contain highly volatile elements such as in (Na,K)NbO3 which makes their sintering ability quite poor. The use of SPS has enabled suppression of lead loss through rapid heating rate, lower sintering temperature and shorter sintering times [50]. In one study, Han et al. demonstrated that the use of SPS can lower the sintering temperature of a Pb (Zr0.52Ti0.42Sn0.02Nb0.04)O3 piezoceramic by a substantial 200–300°C while maintaining a high relative density (>99%) [51]. In a separate study, a (Na0.535K0.485)1−xLix(Nb0.8Ta0.2)O3 (x = 0.02–0.07) ceramic with improved mechanical and electrical properties was produced using SPS method [52].
There is an assumption that the nonlinear response of piezoceramics is grain size dependent; this is understood to be the variation of functional properties under an external stimulus. The two major contributors to nonlinear response of piezoceramics are the intrinsic (i.e. the contribution of composition, crystal structure, etc.) and extrinsic (i.e. grain size, domain wall dynamics, etc.) contributors [53, 54]. This implies that a significant decrease in grain size has the potential to produce a notable modification of nonlinear response in piezoceramics. It therefore means the stability of piezoelectric properties may be improved by controlling the grain size.
The wide application of TEs has not been realised mainly owing to low conversion efficiencies. For instance, commercially available TE materials possess a low ZT of 1 and average conversion efficiency of ~5% [55]. In order to promote the practical applications of TEs, it is critical to synthesise TE materials with ZT values >1; a TE device with ZT = 3 operating between room temperature and 773 K would yield ~ 50% of the Carnot efficiency [56]. It is evident from previous reviews that the key strategy in the improvement of ZT values for TEs has been the increase in the seeback coefficient and reduction in thermal conductivity. However, no significant improvement in ZT values has been reported through the tuning of these properties. Theoretical predictions have shown that nanostructuring can enhance the seeback coefficient through modification of density of states and can reduce the thermal conductivity by selective scattering of phonons, resulting in good ZT values. It should be noted here that the TE properties of nanostructured materials also depend on the size and morphology of microstructural features; thus, microstructural engineering is key in the development of TE materials. In 2005, Yu et al. observed that the seeback coefficient and thermal and electrical conductivities are all significantly dependent on grain size; this was confirmed on CoSb3 TE materials [57].
It has been proven that the main design principle for the future TEs is the use of nanostructured architectures. A number of approaches have been utilised in developing nano-inclusions which are effective in reducing the lattice thermal conductivities [16]. Such methods include in situ dispersion of partially oxidised nanoparticles in matrix [58], endotaxial nanoprecipitates [59, 60] and embedded nano-inclusions [61, 62]. The SPS technology has been utilised in fabricating highly dense and fine-grained TEs [63]. Nanocomposite grains are believed to be effective in scattering phonons with a broad wavelength which enhances the functional properties of TEs [55]. By nanostructuring a wide variation in ZT values ranging from 0.4 to 1.7 has been obtained for nanocomposites with similar composition. A ZT of about 1.5 at 390 K was achieved for a (Bi,Sb)2Te3 nanocomposite produced by a combination of melt spinning of single elements followed by SPS sintering. Another Bi0.52Sb1.48Te3 nanocomposite material had a ZT ~ 1.56 [64, 65]. It has also been proven that by combining mechanical alloying and SPS sintering, one can achieve high ZT of 1.5 at 700 K in AgPbmSbTem+2 nanocomposite [66].
Most of the bulk TE materials with highest ZT values are fabricated through the SPS process. Bi2Te3 compounds have been produced with ZT values ranging from 0.7 to 1.8 in the SPS [67]. The reason for a wide range of ZT values has been attributed to varying initial green densities which is key in determining the inner temperature of the sample. Moreover, powder aggregates can lead to inhomogeneous distribution of temperature.
There is clear evidence that SPS technology and TSS methodology have yielded quite some progressive results in the production of functional nanoceramic materials. Moreover, the use of modified TSS methodology in SPS equipment has shown great potential for yielding nanostructured materials with minimum risk of grain growth. However, what still remains controversial is the consistency of the functional properties and reproducibility of the methodologies used. Thus this area of study still remains highly energised for a broader enquiry. Furthermore, for most functional ceramic materials, nanostructuring has yielded enhanced material properties through various mechanisms. Although there is still room for improvement, it remains a challenge to material scientists and engineers alike to explore further and develop a deeper understanding of the mechanisms involved which may help achieve large increases in critical functional properties. Some of the highlighted problems which might have contributed to the inconsistences in functional properties include variations in the starting green densities and the likelihood of powder agglomeration at these finer sizes. This leads to inhomogeneous temperature distribution in samples and variations in sintered densities which has direct impact on material properties.
In conclusion, for practical purposes most of these materials have to satisfy certain conditions for this to become a reality: the synthesis route should be scalable, high quality and low cost, materials should have the ability to form dense compact nanostructured materials which are amenable to subsequent processing such as machining/device integration and lastly the nanostructured products should demonstrate enhanced functional properties over their micron-sized counterparts. This points to exciting scientific opportunities for continued research in order to gain more quantitative understanding to allow the design and optimisation of processes in the development of functional ceramic materials.
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\n\nIntechOpen works with award winning print-houses and we hold to the fact that all of our printed products are of the highest quality.
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This response can be blunted with the appropriate mix of biocompatible materials and anticoagulation therapy. The use of anticoagulants, in turn, requires appropriate laboratory testing to determine whether the patient is appropriately anticoagulated. Physicians must balance the risks of bleeding with the risks of thrombosis; the proper interpretation of these tests is often shrouded in mystery. It is the purpose of this chapter to help demystify the coagulation system, anticoagulants, biocompatible surfaces, and coagulation testing so that ECMO practitioners can make informed decisions about their patients and to spur coordinated efforts for future research to improve our understanding of these complex processes.",book:{id:"5202",slug:"extracorporeal-membrane-oxygenation-advances-in-therapy",title:"Extracorporeal Membrane Oxygenation",fullTitle:"Extracorporeal Membrane Oxygenation - Advances in Therapy"},signatures:"Timothy M. Maul, M Patricia Massicotte and Peter D. 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In this chapter we discuss various cannulation techniques used.",book:{id:"5202",slug:"extracorporeal-membrane-oxygenation-advances-in-therapy",title:"Extracorporeal Membrane Oxygenation",fullTitle:"Extracorporeal Membrane Oxygenation - Advances in Therapy"},signatures:"Chand Ramaiah and Ashok Babu",authors:[{id:"183646",title:"Dr.",name:"Chand",middleName:null,surname:"Ramaiah",slug:"chand-ramaiah",fullName:"Chand Ramaiah"},{id:"189073",title:"Dr.",name:"Ashok",middleName:null,surname:"Babu",slug:"ashok-babu",fullName:"Ashok Babu"}]},{id:"27955",title:"Transfusion-Associated Bacterial Sepsis",slug:"transfusion-associated-sepsis",totalDownloads:8260,totalCrossrefCites:1,totalDimensionsCites:2,abstract:null,book:{id:"802",slug:"severe-sepsis-and-septic-shock-understanding-a-serious-killer",title:"Severe Sepsis and Septic Shock",fullTitle:"Severe Sepsis and Septic Shock - Understanding a Serious Killer"},signatures:"Jolanta Korsak",authors:[{id:"72828",title:"Prof.",name:"Jolanta",middleName:null,surname:"Korsak",slug:"jolanta-korsak",fullName:"Jolanta Korsak"}]},{id:"51211",title:"Triple Cannulation ECMO",slug:"triple-cannulation-ecmo",totalDownloads:4782,totalCrossrefCites:3,totalDimensionsCites:8,abstract:"Extracorporeal membrane oxygenation (ECMO) has emerged as an invaluable tool for bridging severe isolated or combined failure of lung and heart. 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Unfortunately, brain death and neurologic injuries are significant causes of morbidity and mortality for patients requiring an ECMO support. Critical to the management of patients requiring ECMO is a broader understanding of neurologic monitoring along with the clinical assessment and management of neurologic events. It is important to evaluate and potentially intervene early in the event of a neurologic problem to minimize its clinical significance. Hopefully, with a better understanding of the pathophysiology, diagnostic and therapeutic tools, and prevention strategies, the true incidence of neurologic complications can be understood and minimized.",book:{id:"5202",slug:"extracorporeal-membrane-oxygenation-advances-in-therapy",title:"Extracorporeal Membrane Oxygenation",fullTitle:"Extracorporeal Membrane Oxygenation - Advances in Therapy"},signatures:"Susana M. Bowling, Joao Gomes and Michael S. 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His research interest focuses on computational chemistry and molecular modeling of diverse systems of pharmacological, food, and alternative energy interests by resorting to DFT and Conceptual DFT. He has authored a coauthored more than 255 peer-reviewed papers, 32 book chapters, and 2 edited books. He has delivered speeches at many international and domestic conferences. He serves as a reviewer for more than eighty international journals, books, and research proposals as well as an editor for special issues of renowned scientific journals.",institutionString:"Centro de Investigación en Materiales Avanzados",institution:{name:"Centro de Investigación en Materiales Avanzados",country:{name:"Mexico"}}},{id:"76477",title:"Prof.",name:"Mirza",middleName:null,surname:"Hasanuzzaman",slug:"mirza-hasanuzzaman",fullName:"Mirza Hasanuzzaman",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/76477/images/system/76477.png",biography:"Dr. Mirza Hasanuzzaman is a Professor of Agronomy at Sher-e-Bangla Agricultural University, Bangladesh. He received his Ph.D. in Plant Stress Physiology and Antioxidant Metabolism from Ehime University, Japan, with a scholarship from the Japanese Government (MEXT). Later, he completed his postdoctoral research at the Center of Molecular Biosciences, University of the Ryukyus, Japan, as a recipient of the Japan Society for the Promotion of Science (JSPS) postdoctoral fellowship. He was also the recipient of the Australian Government Endeavour Research Fellowship for postdoctoral research as an adjunct senior researcher at the University of Tasmania, Australia. Dr. Hasanuzzaman’s current work is focused on the physiological and molecular mechanisms of environmental stress tolerance. Dr. Hasanuzzaman has published more than 150 articles in peer-reviewed journals. He has edited ten books and written more than forty book chapters on important aspects of plant physiology, plant stress tolerance, and crop production. According to Scopus, Dr. Hasanuzzaman’s publications have received more than 10,500 citations with an h-index of 53. He has been named a Highly Cited Researcher by Clarivate. He is an editor and reviewer for more than fifty peer-reviewed international journals and was a recipient of the “Publons Peer Review Award” in 2017, 2018, and 2019. He has been honored by different authorities for his outstanding performance in various fields like research and education, and he has received the World Academy of Science Young Scientist Award (2014) and the University Grants Commission (UGC) Award 2018. He is a fellow of the Bangladesh Academy of Sciences (BAS) and the Royal Society of Biology.",institutionString:"Sher-e-Bangla Agricultural University",institution:{name:"Sher-e-Bangla Agricultural University",country:{name:"Bangladesh"}}},{id:"187859",title:"Prof.",name:"Kusal",middleName:"K.",surname:"Das",slug:"kusal-das",fullName:"Kusal Das",position:null,profilePictureURL:"https://s3.us-east-1.amazonaws.com/intech-files/0030O00002bSBDeQAO/Profile_Picture_1623411145568",biography:"Kusal K. Das is a Distinguished Chair Professor of Physiology, Shri B. M. Patil Medical College and Director, Centre for Advanced Medical Research (CAMR), BLDE (Deemed to be University), Vijayapur, Karnataka, India. Dr. Das did his M.S. and Ph.D. in Human Physiology from the University of Calcutta, Kolkata. His area of research is focused on understanding of molecular mechanisms of heavy metal activated low oxygen sensing pathways in vascular pathophysiology. He has invented a new method of estimation of serum vitamin E. His expertise in critical experimental protocols on vascular functions in experimental animals was well documented by his quality of publications. He was a Visiting Professor of Medicine at University of Leeds, United Kingdom (2014-2016) and Tulane University, New Orleans, USA (2017). For his immense contribution in medical research Ministry of Science and Technology, Government of India conferred him 'G.P. Chatterjee Memorial Research Prize-2019” and he is also the recipient of 'Dr.Raja Ramanna State Scientist Award 2015” by Government of Karnataka. He is a Fellow of the Royal Society of Biology (FRSB), London and Honorary Fellow of Karnataka Science and Technology Academy, Department of Science and Technology, Government of Karnataka.",institutionString:"BLDE (Deemed to be University), India",institution:null},{id:"243660",title:"Dr.",name:"Mallanagouda Shivanagouda",middleName:null,surname:"Biradar",slug:"mallanagouda-shivanagouda-biradar",fullName:"Mallanagouda Shivanagouda Biradar",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/243660/images/system/243660.jpeg",biography:"M. S. Biradar is Vice Chancellor and Professor of Medicine of\nBLDE (Deemed to be University), Vijayapura, Karnataka, India.\nHe obtained his MD with a gold medal in General Medicine and\nhas devoted himself to medical teaching, research, and administrations. He has also immensely contributed to medical research\non vascular medicine, which is reflected by his numerous publications including books and book chapters. Professor Biradar was\nalso Visiting Professor at Tulane University School of Medicine, New Orleans, USA.",institutionString:"BLDE (Deemed to be University)",institution:{name:"BLDE University",country:{name:"India"}}},{id:"289796",title:"Dr.",name:"Swastika",middleName:null,surname:"Das",slug:"swastika-das",fullName:"Swastika Das",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/289796/images/system/289796.jpeg",biography:"Swastika N. Das is Professor of Chemistry at the V. P. Dr. P. G.\nHalakatti College of Engineering and Technology, BLDE (Deemed\nto be University), Vijayapura, Karnataka, India. She obtained an\nMSc, MPhil, and PhD in Chemistry from Sambalpur University,\nOdisha, India. Her areas of research interest are medicinal chemistry, chemical kinetics, and free radical chemistry. She is a member\nof the investigators who invented a new modified method of estimation of serum vitamin E. She has authored numerous publications including book\nchapters and is a mentor of doctoral curriculum at her university.",institutionString:"BLDEA’s V.P.Dr.P.G.Halakatti College of Engineering & Technology",institution:{name:"BLDE University",country:{name:"India"}}},{id:"248459",title:"Dr.",name:"Akikazu",middleName:null,surname:"Takada",slug:"akikazu-takada",fullName:"Akikazu Takada",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/248459/images/system/248459.png",biography:"Akikazu Takada was born in Japan, 1935. After graduation from\nKeio University School of Medicine and finishing his post-graduate studies, he worked at Roswell Park Memorial Institute NY,\nUSA. He then took a professorship at Hamamatsu University\nSchool of Medicine. In thrombosis studies, he found the SK\npotentiator that enhances plasminogen activation by streptokinase. He is very much interested in simultaneous measurements\nof fatty acids, amino acids, and tryptophan degradation products. By using fatty\nacid analyses, he indicated that plasma levels of trans-fatty acids of old men were\nfar higher in the US than Japanese men. . He also showed that eicosapentaenoic acid\n(EPA) and docosahexaenoic acid (DHA) levels are higher, and arachidonic acid\nlevels are lower in Japanese than US people. By using simultaneous LC/MS analyses\nof plasma levels of tryptophan metabolites, he recently found that plasma levels of\nserotonin, kynurenine, or 5-HIAA were higher in patients of mono- and bipolar\ndepression, which are significantly different from observations reported before. In\nview of recent reports that plasma tryptophan metabolites are mainly produced by\nmicrobiota. He is now working on the relationships between microbiota and depression or autism.",institutionString:"Hamamatsu University School of Medicine",institution:{name:"Hamamatsu University School of Medicine",country:{name:"Japan"}}},{id:"137240",title:"Prof.",name:"Mohammed",middleName:null,surname:"Khalid",slug:"mohammed-khalid",fullName:"Mohammed Khalid",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/137240/images/system/137240.png",biography:"Mohammed Khalid received his B.S. degree in chemistry in 2000 and Ph.D. degree in physical chemistry in 2007 from the University of Khartoum, Sudan. He moved to School of Chemistry, Faculty of Science, University of Sydney, Australia in 2009 and joined Dr. Ron Clarke as a postdoctoral fellow where he worked on the interaction of ATP with the phosphoenzyme of the Na+/K+-ATPase and dual mechanisms of allosteric acceleration of the Na+/K+-ATPase by ATP; then he went back to Department of Chemistry, University of Khartoum as an assistant professor, and in 2014 he was promoted as an associate professor. In 2011, he joined the staff of Department of Chemistry at Taif University, Saudi Arabia, where he is currently an assistant professor. His research interests include the following: P-Type ATPase enzyme kinetics and mechanisms, kinetics and mechanisms of redox reactions, autocatalytic reactions, computational enzyme kinetics, allosteric acceleration of P-type ATPases by ATP, exploring of allosteric sites of ATPases, and interaction of ATP with ATPases located in cell membranes.",institutionString:"Taif University",institution:{name:"Taif University",country:{name:"Saudi Arabia"}}},{id:"63810",title:"Prof.",name:"Jorge",middleName:null,surname:"Morales-Montor",slug:"jorge-morales-montor",fullName:"Jorge Morales-Montor",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/63810/images/system/63810.png",biography:"Dr. Jorge Morales-Montor was recognized with the Lola and Igo Flisser PUIS Award for best graduate thesis at the national level in the field of parasitology. He received a fellowship from the Fogarty Foundation to perform postdoctoral research stay at the University of Georgia. He has 153 journal articles to his credit. He has also edited several books and published more than fifty-five book chapters. He is a member of the Mexican Academy of Sciences, Latin American Academy of Sciences, and the National Academy of Medicine. He has received more than thirty-five awards and has supervised numerous bachelor’s, master’s, and Ph.D. students. Dr. Morales-Montor is the past president of the Mexican Society of Parasitology.",institutionString:"National Autonomous University of Mexico",institution:{name:"National Autonomous University of Mexico",country:{name:"Mexico"}}},{id:"217215",title:"Dr.",name:"Palash",middleName:null,surname:"Mandal",slug:"palash-mandal",fullName:"Palash Mandal",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/217215/images/system/217215.jpeg",biography:null,institutionString:"Charusat University",institution:null},{id:"49739",title:"Dr.",name:"Leszek",middleName:null,surname:"Szablewski",slug:"leszek-szablewski",fullName:"Leszek Szablewski",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/49739/images/system/49739.jpg",biography:"Leszek Szablewski is a professor of medical sciences. He received his M.S. in the Faculty of Biology from the University of Warsaw and his PhD degree from the Institute of Experimental Biology Polish Academy of Sciences. He habilitated in the Medical University of Warsaw, and he obtained his degree of Professor from the President of Poland. Professor Szablewski is the Head of Chair and Department of General Biology and Parasitology, Medical University of Warsaw. Professor Szablewski has published over 80 peer-reviewed papers in journals such as Journal of Alzheimer’s Disease, Biochim. Biophys. Acta Reviews of Cancer, Biol. Chem., J. Biomed. Sci., and Diabetes/Metabol. Res. Rev, Endocrine. He is the author of two books and four book chapters. He has edited four books, written 15 scripts for students, is the ad hoc reviewer of over 30 peer-reviewed journals, and editorial member of peer-reviewed journals. Prof. Szablewski’s research focuses on cell physiology, genetics, and pathophysiology. He works on the damage caused by lack of glucose homeostasis and changes in the expression and/or function of glucose transporters due to various diseases. He has given lectures, seminars, and exercises for students at the Medical University.",institutionString:"Medical University of Warsaw",institution:{name:"Medical University of Warsaw",country:{name:"Poland"}}},{id:"173123",title:"Dr.",name:"Maitham",middleName:null,surname:"Khajah",slug:"maitham-khajah",fullName:"Maitham Khajah",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/173123/images/system/173123.jpeg",biography:"Dr. Maitham A. Khajah received his degree in Pharmacy from Faculty of Pharmacy, Kuwait University, in 2003 and obtained his PhD degree in December 2009 from the University of Calgary, Canada (Gastrointestinal Science and Immunology). Since January 2010 he has been assistant professor in Kuwait University, Faculty of Pharmacy, Department of Pharmacology and Therapeutics. His research interest are molecular targets for the treatment of inflammatory bowel disease (IBD) and the mechanisms responsible for immune cell chemotaxis. He cosupervised many students for the MSc Molecular Biology Program, College of Graduate Studies, Kuwait University. Ever since joining Kuwait University in 2010, he got various grants as PI and Co-I. He was awarded the Best Young Researcher Award by Kuwait University, Research Sector, for the Year 2013–2014. He was a member in the organizing committee for three conferences organized by Kuwait University, Faculty of Pharmacy, as cochair and a member in the scientific committee (the 3rd, 4th, and 5th Kuwait International Pharmacy Conference).",institutionString:"Kuwait University",institution:{name:"Kuwait University",country:{name:"Kuwait"}}},{id:"195136",title:"Dr.",name:"Aya",middleName:null,surname:"Adel",slug:"aya-adel",fullName:"Aya Adel",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/195136/images/system/195136.jpg",biography:"Dr. Adel works as an Assistant Lecturer in the unit of Phoniatrics, Department of Otolaryngology, Ain Shams University in Cairo, Egypt. Dr. Adel is especially interested in joint attention and its impairment in autism spectrum disorder",institutionString:"Ain Shams University",institution:{name:"Ain Shams University",country:{name:"Egypt"}}},{id:"94911",title:"Dr.",name:"Boulenouar",middleName:null,surname:"Mesraoua",slug:"boulenouar-mesraoua",fullName:"Boulenouar Mesraoua",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/94911/images/system/94911.png",biography:"Dr Boulenouar Mesraoua is the Associate Professor of Clinical Neurology at Weill Cornell Medical College-Qatar and a Consultant Neurologist at Hamad Medical Corporation at the Neuroscience Department; He graduated as a Medical Doctor from the University of Oran, Algeria; he then moved to Belgium, the City of Liege, for a Residency in Internal Medicine and Neurology at Liege University; after getting the Belgian Board of Neurology (with high marks), he went to the National Hospital for Nervous Diseases, Queen Square, London, United Kingdom for a fellowship in Clinical Neurophysiology, under Pr Willison ; Dr Mesraoua had also further training in Epilepsy and Continuous EEG Monitoring for two years (from 2001-2003) in the Neurophysiology department of Zurich University, Switzerland, under late Pr Hans Gregor Wieser ,an internationally known epileptologist expert. \n\nDr B. Mesraoua is the Director of the Neurology Fellowship Program at the Neurology Section and an active member of the newly created Comprehensive Epilepsy Program at Hamad General Hospital, Doha, Qatar; he is also Assistant Director of the Residency Program at the Qatar Medical School. \nDr B. Mesraoua's main interests are Epilepsy, Multiple Sclerosis, and Clinical Neurology; He is the Chairman and the Organizer of the well known Qatar Epilepsy Symposium, he is running yearly for the past 14 years and which is considered a landmark in the Gulf region; He has also started last year , together with other epileptologists from Qatar, the region and elsewhere, a yearly International Epilepsy School Course, which was attended by many neurologists from the Area.\n\nInternationally, Dr Mesraoua is an active and elected member of the Commission on Eastern Mediterranean Region (EMR ) , a regional branch of the International League Against Epilepsy (ILAE), where he represents the Middle East and North Africa(MENA ) and where he holds the position of chief of the Epilepsy Epidemiology Section; Dr Mesraoua is a member of the American Academy of Neurology, the Europeen Academy of Neurology and the American Epilepsy Society.\n\nDr Mesraoua's main objectives are to encourage frequent gathering of the epileptologists/neurologists from the MENA region and the rest of the world, promote Epilepsy Teaching in the MENA Region, and encourage multicenter studies involving neurologists and epileptologists in the MENA region, particularly epilepsy epidemiological studies. \n\nDr. Mesraoua is the recipient of two research Grants, as the Lead Principal Investigator (750.000 USD and 250.000 USD) from the Qatar National Research Fund (QNRF) and the Hamad Hospital Internal Research Grant (IRGC), on the following topics : “Continuous EEG Monitoring in the ICU “ and on “Alpha-lactoalbumin , proof of concept in the treatment of epilepsy” .Dr Mesraoua is a reviewer for the journal \"seizures\" (Europeen Epilepsy Journal ) as well as dove journals ; Dr Mesraoua is the author and co-author of many peer reviewed publications and four book chapters in the field of Epilepsy and Clinical Neurology",institutionString:"Weill Cornell Medical College in Qatar",institution:{name:"Weill Cornell Medical College in Qatar",country:{name:"Qatar"}}},{id:"282429",title:"Prof.",name:"Covanis",middleName:null,surname:"Athanasios",slug:"covanis-athanasios",fullName:"Covanis Athanasios",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/282429/images/system/282429.jpg",biography:null,institutionString:"Neurology-Neurophysiology Department of the Children Hospital Agia Sophia",institution:null},{id:"190980",title:"Prof.",name:"Marwa",middleName:null,surname:"Mahmoud Saleh",slug:"marwa-mahmoud-saleh",fullName:"Marwa Mahmoud Saleh",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/190980/images/system/190980.jpg",biography:"Professor Marwa Mahmoud Saleh is a doctor of medicine and currently works in the unit of Phoniatrics, Department of Otolaryngology, Ain Shams University in Cairo, Egypt. She got her doctoral degree in 1991 and her doctoral thesis was accomplished in the University of Iowa, United States. Her publications covered a multitude of topics as videokymography, cochlear implants, stuttering, and dysphagia. She has lectured Egyptian phonology for many years. Her recent research interest is joint attention in autism.",institutionString:"Ain Shams University",institution:{name:"Ain Shams University",country:{name:"Egypt"}}},{id:"259190",title:"Dr.",name:"Syed Ali Raza",middleName:null,surname:"Naqvi",slug:"syed-ali-raza-naqvi",fullName:"Syed Ali Raza Naqvi",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/259190/images/system/259190.png",biography:"Dr. Naqvi is a radioanalytical chemist and is working as an associate professor of analytical chemistry in the Department of Chemistry, Government College University, Faisalabad, Pakistan. Advance separation techniques, nuclear analytical techniques and radiopharmaceutical analysis are the main courses that he is teaching to graduate and post-graduate students. In the research area, he is focusing on the development of organic- and biomolecule-based radiopharmaceuticals for diagnosis and therapy of infectious and cancerous diseases. Under the supervision of Dr. Naqvi, three students have completed their Ph.D. degrees and 41 students have completed their MS degrees. He has completed three research projects and is currently working on 2 projects entitled “Radiolabeling of fluoroquinolone derivatives for the diagnosis of deep-seated bacterial infections” and “Radiolabeled minigastrin peptides for diagnosis and therapy of NETs”. He has published about 100 research articles in international reputed journals and 7 book chapters. Pakistan Institute of Nuclear Science & Technology (PINSTECH) Islamabad, Punjab Institute of Nuclear Medicine (PINM), Faisalabad and Institute of Nuclear Medicine and Radiology (INOR) Abbottabad are the main collaborating institutes.",institutionString:"Government College University",institution:{name:"Government College University, Faisalabad",country:{name:"Pakistan"}}},{id:"58390",title:"Dr.",name:"Gyula",middleName:null,surname:"Mozsik",slug:"gyula-mozsik",fullName:"Gyula Mozsik",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/58390/images/system/58390.png",biography:"Gyula Mózsik MD, Ph.D., ScD (med), is an emeritus professor of Medicine at the First Department of Medicine, Univesity of Pécs, Hungary. He was head of this department from 1993 to 2003. His specializations are medicine, gastroenterology, clinical pharmacology, clinical nutrition, and dietetics. His research fields are biochemical pharmacological examinations in the human gastrointestinal (GI) mucosa, mechanisms of retinoids, drugs, capsaicin-sensitive afferent nerves, and innovative pharmacological, pharmaceutical, and nutritional (dietary) research in humans. He has published about 360 peer-reviewed papers, 197 book chapters, 692 abstracts, 19 monographs, and has edited 37 books. He has given about 1120 regular and review lectures. He has organized thirty-eight national and international congresses and symposia. He is the founder of the International Conference on Ulcer Research (ICUR); International Union of Pharmacology, Gastrointestinal Section (IUPHAR-GI); Brain-Gut Society symposiums, and gastrointestinal cytoprotective symposiums. He received the Andre Robert Award from IUPHAR-GI in 2014. Fifteen of his students have been appointed as full professors in Egypt, Cuba, and Hungary.",institutionString:"University of Pécs",institution:{name:"University of Pecs",country:{name:"Hungary"}}},{id:"277367",title:"M.Sc.",name:"Daniel",middleName:"Martin",surname:"Márquez López",slug:"daniel-marquez-lopez",fullName:"Daniel Márquez López",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/277367/images/7909_n.jpg",biography:"Msc Daniel Martin Márquez López has a bachelor degree in Industrial Chemical Engineering, a Master of science degree in the same área and he is a PhD candidate for the Instituto Politécnico Nacional. His Works are realted to the Green chemistry field, biolubricants, biodiesel, transesterification reactions for biodiesel production and the manipulation of oils for therapeutic purposes.",institutionString:null,institution:{name:"Instituto Politécnico Nacional",country:{name:"Mexico"}}},{id:"196544",title:"Prof.",name:"Angel",middleName:null,surname:"Catala",slug:"angel-catala",fullName:"Angel Catala",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/196544/images/system/196544.jpg",biography:"Angel Catalá studied chemistry at Universidad Nacional de La Plata, Argentina, where he received a Ph.D. in Chemistry (Biological Branch) in 1965. From 1964 to 1974, he worked as an Assistant in Biochemistry at the School of Medicine at the same university. From 1974 to 1976, he was a fellow of the National Institutes of Health (NIH) at the University of Connecticut, Health Center, USA. From 1985 to 2004, he served as a Full Professor of Biochemistry at the Universidad Nacional de La Plata. He is a member of the National Research Council (CONICET), Argentina, and the Argentine Society for Biochemistry and Molecular Biology (SAIB). His laboratory has been interested for many years in the lipid peroxidation of biological membranes from various tissues and different species. Dr. Catalá has directed twelve doctoral theses, published more than 100 papers in peer-reviewed journals, several chapters in books, and edited twelve books. He received awards at the 40th International Conference Biochemistry of Lipids 1999 in Dijon, France. He is the winner of the Bimbo Pan-American Nutrition, Food Science and Technology Award 2006 and 2012, South America, Human Nutrition, Professional Category. In 2006, he won the Bernardo Houssay award in pharmacology, in recognition of his meritorious works of research. Dr. Catalá belongs to the editorial board of several journals including Journal of Lipids; International Review of Biophysical Chemistry; Frontiers in Membrane Physiology and Biophysics; World Journal of Experimental Medicine and Biochemistry Research International; World Journal of Biological Chemistry, Diabetes, and the Pancreas; International Journal of Chronic Diseases & Therapy; and International Journal of Nutrition. He is the co-editor of The Open Biology Journal and associate editor for Oxidative Medicine and Cellular Longevity.",institutionString:"Universidad Nacional de La Plata",institution:{name:"National University of La Plata",country:{name:"Argentina"}}},{id:"186585",title:"Dr.",name:"Francisco Javier",middleName:null,surname:"Martin-Romero",slug:"francisco-javier-martin-romero",fullName:"Francisco Javier Martin-Romero",position:null,profilePictureURL:"https://s3.us-east-1.amazonaws.com/intech-files/0030O00002bSB3HQAW/Profile_Picture_1631258137641",biography:"Francisco Javier Martín-Romero (Javier) is a Professor of Biochemistry and Molecular Biology at the University of Extremadura, Spain. He is also a group leader at the Biomarkers Institute of Molecular Pathology. Javier received his Ph.D. in 1998 in Biochemistry and Biophysics. At the National Cancer Institute (National Institute of Health, Bethesda, MD) he worked as a research associate on the molecular biology of selenium and its role in health and disease. After postdoctoral collaborations with Carlos Gutierrez-Merino (University of Extremadura, Spain) and Dario Alessi (University of Dundee, UK), he established his own laboratory in 2008. 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