Modern Engineered Materials and Technologies for Metal Forming Applications
View this Special IssueResearch Article  Open Access
YongShin Lee, SangJun Lee, Sangmok Lee, EungZu Kim, Duck Jae Yoon, "Development of a Master Sintering Curve for AlMg Alloy", Advances in Materials Science and Engineering, vol. 2016, Article ID 5607386, 7 pages, 2016. https://doi.org/10.1155/2016/5607386
Development of a Master Sintering Curve for AlMg Alloy
Abstract
A new master sintering curve (MSC) is proposed for AlMg alloy in order to effectively design the pressureassisted sintering process. In this work, hot pressing experiments of AlMg alloy powders are performed. The changes of relative density during hot pressing are measured for the various heating rates of 5°C/min, 10°C/min, and 20°C/min at the fixed pressure of 50 MPa. A work of sintering, designated as , is introduced and defined as . A work of sintering, , could be interpreted as a measure for the amount of sintering work. The MSC in this work defines the relation between the apparent density and a work of sintering, . Since the measurement of an apparent activation energy, , is very difficult, the correct value of is obtained numerically using a mean residual square method. Then, the master sintering curves for sintering of AlMg alloy powders are proposed for the sintering temperatures of 400°C and 500°C through scaling procedures. It is expected that the master sintering curves proposed in this work could help an engineer to design pressureassisted sintering process for AlMg alloy.
1. Introduction
The demand for more light weight, fuel efficient, and enhanced performance automobiles has stimulated research and development in highstrength and high formability aluminum alloys. The AlMg alloys have medium to high strength, excellent formability, and good corrosion resistance [1]. However, it has been well known that sintering with the powder of AlMg alloys is not easy.
In the conventional design procedure of sintering, the parameters such as time and temperature of the sintering are decided mainly on the “trial and error” basis [2]. If the densification during sintering could be predicted from the sintering data that are really available, it would be helpful for engineers to design a new sintering process. Then, the sintering strategy could be established on that basis, which leads to the production of pellets of good quality and less number of defects. Therefore, there is a need for better understanding of a whole sintering procedure. The theory of master sintering curve (MSC) provides a new insight into the understanding of sintering process [3–5].
The master sintering curve enables engineers to predict the densification behavior under arbitrary timetemperature schedules with the help of a minimum of preliminary experiments. However, this curve has been known as sensitive to the factors such as starting morphology of the powder, fabrication route, dominant diffusion mechanism, and heating condition used for sintering [6]. Thus, one may need a new MSC according to the changes of such factors if any of them is changed when designing a sintering process. A MSC can also be used as an aid to compare the sinterability of different powders and to examine the effects of additives, atmosphere, and fabrication procedure of sintering. Recent study could incorporate the effects of pressure on densification during sintering into one MSC such that the final density at any applied pressure in a pressureassisted sintering can be predicted [2]. The concept of MSC, which was originally developed for the sintering of ceramic powders, has been successfully extended to the sintering with metallic powders such as Al_{2}O_{3}, XnO, rhenium, and nickel powders [2–7]. More recently, pressureassisted sintering of hard metallic powders such as tungsten alloys and WC alloys has been reported [8, 9]. For instance, An [9] constructed the master sintering curves for the mixture of WC, Cu, and Ni powders to understand densification behaviors during the resistance heating. However, the extension of the concept of MSC to sintering with various metallic powders is still in early stage. The motivation for the present study is to extend the concept of the master sintering curve into the realm of hot pressing with metallic powders and to establish the pressureassisted master sintering curve of AlMg alloy.
2. Theory of a Master Sintering Curve
Sintering of particulate materials is a thermally activated process involving the masstransport phenomena that would result in particle bonding [10]. These masstransport phenomena are generally to reduce the free surface area in the compact of particles. On the other hand, the surface transport mechanisms are to only grow the sinter bonding between particles. Thus, it is the bulk transport mechanisms that increase the density of porous body by gathering the particle together in order to reduce the free surface energy. Associated with this sintering densification is a decrease in volume, so the changes of density can be monitored by measuring dimensional changes of a compact during sintering. Hansen et al. [11] developed a combinedstage sintering model with the extensive studies on the masstransport mechanisms during sintering, which is able to predict both the dimensional and density changes that take place during sintering. In their work, the compact densification is related to the dominant diffusional events such as grain boundary and volume diffusion, resulting in the following combinedstage sintering equation:where is a representative dimension of the compact, is time, is the surface energy, is the atomic volume, is Boltzmann’s constant, is the temperature, is a lumped scaling factor, is the diffusivity, is the grain size, and the subscripts and refer to volume diffusion and grain boundary diffusion, respectively.
For an isotropic shrinkage, the sintering shrinkage rate can be linked to the densification rate by considering the conservation of mass. Then, the following approximate relationship could be obtained:
Combining (1) and (2) provides a link between the densification rate and the diffusional sintering phenomena. However, the lumped scaling factors, and , are arbitrary parameters containing the densitydependent geometric terms. Furthermore, the diffusivities for grain boundary and volume diffusion, , vary significantly between the studies [12]. These are the main reasons why no reliable value can be assigned confidently to a particular material. Thus, determination of the shrinkage and densification rates from the combinedstage sinter model requires experimental characterization of the lumped scaling factors and diffusivities for specific sintering systems. In order to overcome this difficult work, Su and Johnson [3, 6] tried to rearrange the combinedstage sintering equation by grouping all of the densitydependent material parameters on one side, while the known processdependent parameters, with the exception of the apparent activation energy , grouped on the other side:
Here, is the diffusivity preexponent. and depend on the dominant sintering mechanism. The diffusivities as given in (1) follow Arrhenius temperature dependence and have been broken up into their preexponential and exponential terms in (3). Since the grain boundary and volume diffusion have diverse influences on the densification response of a sintering system, they have been lumped together as an apparent diffusivity in (3) to create a master sintering curve. Here, and are determined as and for grain boundary diffusion and and for volume diffusion. The rearranged combinedstage sintering model would be integrated from the initial time to the current time for the righthand side. Similarly, the lefthand side could be evaluated by integrating the function represented in terms of a density from the initial density to the current density which can be obtained at any state of (, , ) during thermal processing. The righthand side of (3) could be interpreted as a measure of the energy supplied to the system during nonisothermal sintering. Correspondingly, the lefthand side might be interpreted as the increase of internal energy due to the changes of density during sintering.
Now, the term (), called a work of sintering in this work, is introduced as follows:
The apparent activation energy for sintering in (4) could be found through a numerical analysis, such as mean square residual method, the detailed procedure of which will be shown in the following section. Now it is clear that there must be an apparent density corresponding to a work of sintering, , at a given time . Once the relationship between the work of sintering and the relative density is established, a master sintering curve describing this relationship could be constructed using a scaling procedure or curve fitting.
3. Numerical Procedure to Construct a MSC
As mentioned previously, the MSC model is derived from the final equation of the combinedstage sintering model which is known as an even earlier attempt at the quantitative prediction of sintering behavior known. However, the MSC model offers a simpler method to predict the final density of a sintered product. The value of apparent activation energy is necessary to evaluate a work of sintering () in (4). But the accurate value of apparent activation energy () is not known for many cases. Su and Johnson introduced the fitting procedure to obtain the proper value of apparent activation energy () using the relationships between a work of sintering and density for at least three different heat rates in sintering [6]. This procedure starts with an initially assumed value of . Then, the values of and the density at the time during sintering are evaluated with the assumed value of and they are plotted on the domain of . When the assumed values of are appropriate, then all the points corresponding to (, ) could be merged onto one curve. In this study, the proper value of apparent sintering activation energy is found out by minimizing the normalized dimensionless mean residual square, defined as the following equation as suggested by Su and Johnson [6]:where is the number of experimental data, is the work of sintering at th experimental measurement, is the average value of all over , and and are the final density and initial density, respectively.
When the activation energy obtained here would be compared to those reported in the literatures for the activation energies associated with specific diffusional paths, that is, volume, surface, or grain boundary diffusion, the primary diffusional mechanisms in this sintering would be identified as explained in the others [10, 13]. Now, a MSC can be constructed by plotting the relative density, which would be extracted from experimental dilatometry data, against the natural logarithm of the work of sintering represented by (4). Again, all data points of () obtained with the accurate activation energy are merged onto one master curve or a master sintering curve. The sintering activation energy used in this calculation is temperaturedependent. There have been several tries to represent such complicated shape of a MSC with various functions. Su and Johnson invoked a polynomial function to describe the master sintering curve relationship [6]. However, a polynomial function generally requires many coefficients to precisely represent the complicated shape of a MSC. In order to reduce the material constant needed for a given MSC, it is a better way to invoke the function similar to the complicated curve shape. Teng et al. [14] and Blaine et al. [15] developed the new functions which can represent s sigmoidal shape. Teng et al. used three unknown parameters, but Blaine et al. used only two unknown parameters. In this study, we used Teng’s sigmoidal function to better match the complicated master sintering curve of AlMg alloy, defined as the following equation:where , , and are the material constants. It should be mentioned that the material constants and coincide with the point of inflection of the curve while the constant is the slope of the linearized portion. The overall procedure for the construction of master sintering curve is summarized in Figure 1.
4. Hot Pressing Experiments of AlMg Alloy
In order to develop a MSC of AlMg alloy, hot pressing experiments are carried out. The chemical compositions of the AlMg alloy used in experiments are given in Table 1. AlMg alloy powder having an average particle size of 45 μm filled a graphite mold in glove box for a hot pressing. The pellet was preformed at room temperature and under the uniaxial compression of 10 MPa. Its diameter and height are 20 mm and 13.5 mm, respectively. Each sample was pressed using AlMg alloy powders which weighted about 8 grams. The average density of a bulk body was calculated as , where is the mass and is the volume. It must be mentioned that the densities in a bulk body are assumed as distributed uniformly. The experimental schedules for hot pressing experiments are summarized in Table 2. In order to properly construct a MSC, various experimental conditions were considered. The most important parameters in hot pressing are the peak temperature and its holding time. In this work, two schedules are considered: () peak temperature 400°C and holding time 30 min and () peak temperature 500°C and no holding time. Experiments with the above two schedules are performed under the various heating rates and pressures. The constant heating rates considered in this work are 5°C/min, 10°C/min, and 20°C/min. The sintering pressure of 50 MPa is examined. In experiments, the cooling was done in the furnace until the room temperature. The experimental apparatus of hot pressing in this work is newly developed and is schematically shown in Figure 2.

(a) 1st schedule.  
 
(b) 2nd schedule.  

5. Construction of Master Sintering Curves for AlMg Alloy
First, the relative density could be evaluated based on the punch advancement in experiments and would be plotted with respect to time during sintering. The densification curves, which represents the relative density changes during sintering, allow engineers to understand the characteristics of densification during sintering. Figure 3 shows various densification curves for various hot pressing conditions. Those are Case (a) sintering temperature of 400°C, pressure of 50 MPa, and holding time of 30 min and Case (b) sintering temperature of 500°C, pressure of 50 MPa, and no holding time. Three different heating rates of 5, 10, and 20°C/min are examined. As shown in Figure 3, a densification curve may be divided into three sections. In the first section, the initial relative density holds until densification is activated. In the second section, the densification starts with the high rate of densification and this rate holds until the relative reaches about 95%. In the third section, the rate of densification becomes slow. Two intersection points are observed between 1st and 2nd sections and between 2nd and 3rd sections. It is observed that the first intersection point, the temperature for the initiation of visible densification, varies for three heating rates. Although the effect of pressure on the sintering process is not given specifically, sintering pressure of 20 MPa was examined in experiments. As expected, the pressure is shown to facilitate sintering by showing the fast appearance of the above intersection points. In experiments, temperature holding time is used as a parameter since it affects the sintering time. However, it should be noted that the important factor is not a temperature holding time but an exposure time to thermal activation or sintering time, which can induce the densification during sintering process. In high heating rate of 20°C/min, the exposure time without temperature holding time is much shorter than that with temperature holding time. Thereby, the final densification without temperature holding time in Figure 3(b) does not reach that with temperature holding time in Figure 3(a). In slow heating rate of 5°C/min, the sintering time with high peak temperature of 500°C is slightly shorter than that with temperature holding time at the low peak temperature of 400°C. As shown in Figure 3 for heating rate of 5°C/min, their densification behaviors are similar because the difference in the sintering time or exposure time to thermal activation between them is not so long. But the final density with the peak temperature of 500°C is slightly higher than that with the peak temperature 400°C although the exposure time with the peak temperature of 500°C is shorter. Thereby, one may say that the higher peak temperature could result in higher densification rate. Now, it may be concluded that the important factors in pressureassisted sintering of AlMg alloy are the exposure time to thermal activation and the peak temperature.
(a)
(b)
In order to find a correct activation energy , an initial estimate for must be made. In this work, 500 KJ/mol is used as initial guess, which is much bigger than the correct values given in the literatures. Then, the work of sintering () at the time, when the relative density was measured in experiments, can be computed using (4) for three heating rates of 5, 10, and 20°C/min. This procedure is repeated with the new value of activation energy , smaller than the current one, until reaches the value, close to zero such as 1. In this work, more than 50 values of are examined. The mean square residuals corresponding to those values of are calculated according to (5). Then, the variations of mean square residual corresponding to are plotted as given in Figures 4(a) and 4(b). It should be mentioned that the correct value of is obtained at the minimum of the mean square residual.
(a)
(b)
Once the correct value of is given, then a master curve could be obtained that represents the relationship between the relative density at any time during sintering and the work of sintering until that time, defined by (4). When the relative density during sintering is plotted against the logarithm of a sintering work or ln(), it appears in a form of sigmoidal function given in (6).
As for Case (a) with three heating rates of 5, 10, and 20°C/min, the minimum of is found out as 28 KJ/mol as shown in Figure 4(a). Now, the other densification curve shown in Figure 3(a) could be merged into one master curve as shown in Figure 5(a). As shown in Figure 4(b), the minimum of is 36.4 KJ/mol for Case (b). The corresponding master sintering curve is given in Figure 5(b). The maximum errors between the predicted relative density by a master sintering curve and the measured density in experiments are less than 1% as shown in Figure 5. This implies that the concept of a master sintering curve can be successfully extended into the realm of hot pressing of AlMg alloy.
(a)
(b)
It should be noted that the values of activation energy obtained in this study are slightly bigger than that ( KJ/mol) by Witkin et al. [16], although those values are generally below the activation energies of aluminum lattice with the main grain boundary selfdiffusion mechanism reported in the literatures [17, 18]. In fact, the activation energy is very sensitive to the sintering conditions such as the preparing procedure of green compacts, the sintering procedure, applied pressure, peak temperature, and its holding time, even for the same material.
Now, the coefficients of the master sintering curves as represented in (6) are summarized in Table 3. The individual sintering points converged reasonably close to single curve. This indicates that there should have been a general curve, master sintering curve, which is independent of the sintering path or heating rates. It suggests that integration of a proposed sintering timetemperature profile yields a point on the master sintering curve. The expected density can be obtained by finding the ordinate value at that point. On the other hand, if the final desired density is known, it is possible to obtain the corresponding value from the abscissa of the master sintering curve and therefore to design the sintering schedule.

6. Conclusions
This study is concerned with the development of master sintering curves for AlMg alloy, which can provide a useful method to quantify the densification behavior during sintering. Hot pressing of AlMg alloy powders is performed under the constant heating rate at 5, 10, and 20°C/min for two schedules: (1st schedule) peak temperature 400°C and holding time 30 min; (2nd schedule) peak temperature 500°C and no holding time. The activation energy, Q, is obtained as 28.0 KJ/mol for the 1st schedule, while = 36.4 KJ/mol for the 2nd schedule. It is shown that the concept of master sintering curve could be successfully extended into the realm of hot pressing of AlMg alloy by constructing a master sintering curve for AlMg alloy. The constructed master sintering curves according to = 28.0 and 36.4 KJ/mol for the sintering temperatures of 400°C and 500°C, respectively, show the maximum error of less than 1%. Finally, it is concluded that the master sintering curves presented in this work would be helpful for engineers to design a new sintering process of AlMg alloy.
Competing Interests
The authors declare that they have no competing interests.
References
 L. Zhen and S. B. Kang, “The effect of preaging on microstructure and tensile properties of AlMgSi alloys,” Scripta Materialia, vol. 36, no. 10, pp. 1089–1094, 1997. View at: Publisher Site  Google Scholar
 D. L. Johnson and H. Su, “A practical approach to sintering,” American Ceramic Society Bulletin Journal, vol. 76, p. 72, 1997. View at: Google Scholar
 D. L. Johnson and H. Su, “The master sintering curve,” Advances in Powder Metallurgy and Particulate Materials, vol. 2, p. 115, 1997. View at: Google Scholar
 D. L. Johnson, M. Henrichsen, J. Hwang, and V. P. Dravid, “Ultra rapid phase conversion in ${\beta}^{\text{'}\text{'}}$alumina tubes,” Journal of the American Ceramic Society, vol. 83, no. 11, pp. 2861–2862, 2000. View at: Publisher Site  Google Scholar
 M. Stöcker, “From rapid prototyping to rapid manufacturing,” Auto Technology, vol. 2, p. 38, 2002. View at: Google Scholar
 H. Su and D. L. Johnson, “Master sintering curve: a practical approach to sintering,” Journal of the American Ceramic Society, vol. 79, no. 12, pp. 3211–3217, 1996. View at: Publisher Site  Google Scholar
 W. Q. Shao, S. O. Chen, D. Li, H. S. Cao, T. C. Zhang, and S. S. Zhang, “Prediction and control of microstructure evolution for submicroscale αAl_{2}O_{3} during lowheatingrate sintering based on the master sintering curve theory,” Journal of the European Ceramic Society, vol. 29, no. 1, pp. 201–204, 2009. View at: Publisher Site  Google Scholar
 S. J. Park, J. L. Johnson, Y. Wu, Y.S. Kwon, S. Lee, and R. M. German, “Analysis of the effect of solubility on the densification behavior of tungsten heavy alloys using the master sintering curve approach,” International Journal of Refractory Metals and Hard Materials, vol. 37, pp. 52–59, 2013. View at: Publisher Site  Google Scholar
 K. J. An, “Application of the pressureassisted master sintering surface,” Metals and Materials International, vol. 20, no. 1, pp. 113–118, 2014. View at: Publisher Site  Google Scholar
 R. M. German, Sintering Theory and Practice, John Wiley & Sons, New York, NY, USA, 1996.
 J. D. Hansen, R. P. Rusin, M. H. Teng, and D. L. Johnson, “Combinedstage sintering model,” Journal of the American Ceramic Society, vol. 75, no. 5, pp. 1129–1135, 1992. View at: Publisher Site  Google Scholar
 I. Kaur, W. Gust, and L. Kozma, Handbook of Grain and Interphase Boundary Diffusion Data, 1, University of Stuttgart, 1996.
 J. Wang and R. Raj, “Estimate of the activation energies for boundary diffusion from ratecontrolled sintering of pure alumina, and alumina doped with zirconia or titania,” Journal of the American Ceramic Society, vol. 73, no. 5, pp. 1172–1175, 1990. View at: Publisher Site  Google Scholar
 M. H. Teng, Y. C. Lai, and Y. T. Chen, “A computer program of master sintering curve model to accurately predict sintering results,” Western Pacific Earth Sciences, vol. 2, no. 2, pp. 171–180, 2002. View at: Google Scholar
 D. C. Blaine, S. Park, and R. M. German, “Master sintering curve for a twophase material,” in Proceedings of the 4th International Conference on Science, Technology and Applications of Sintering, Grenoble, France, August 2005. View at: Google Scholar
 D. Witkin, B. Q. Han, and E. J. Lavernia, “Mechanical behavior of ultrafinegrained cryomilled Al 5083 at elevated temperature,” Journal of Materials Engineering and Performance, vol. 14, no. 4, pp. 519–527, 2005. View at: Publisher Site  Google Scholar
 Y. Sohn, “Diffusion in metals,” in Smithells Metals Reference Book, W. F. Gale and T. C. Totemeier, Eds., chapter 13, Elsevier ButterworthHeinemann, Oxford, UK, 8th edition, 2004. View at: Google Scholar
 H. J. Frost and M. F. Ashby, DeformationMechanism Maps, vol. 1, Pergamon Press, New York, NY, USA, 1982.
Copyright
Copyright © 2016 YongShin Lee et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.