In recent years, there has been increasing interest in nanostructured ceramic materials because of their advanced properties. The superplasticity; improved strength and toughness, higher densification rate and low sintering temperature are observed in these materials[1–4]. The sintering speed vsintering of ceramic is related to the grain size d by the expression of vsin ting ∝d-4 [2]. By adding the nano-particles of Al2O3 to conventional Al2O3, the strength, fracture toughness and thermal resistance of Al2O3 ceramic can increase[5]. Up to now, only a few researchers[6,7] have concerned about the specific heat and thermal expansion of nano- ceramics, and no report about thermal diffusivity of nano-composite has been found in literature. However, characterizations of thermal diffusivity of nanocomposite ceramics are very important for designing and preparing this kind of new materials.</p

D Zhang

F Wakai

G Li

IW Chen

J Karch

J Rupp

XR Zhang

Xiao, F.

Zhang, X. R.

Fei, D.

Gan, C. M.

Lei, G. H.

Zhang, D.

Jin, Y. P.

Zhang, G. D.

Digital Repository @ Iowa State University (ISU)

INVESTIGATION OF THERMAL DIFFUSIVITY FOR NANO-PHASE COMPOSITE CERAMICS F. Xiao, X R. Zhang, D. Fei, and C. M. Gan The Lab. of Modem Acoustics and Institute of Acoustics, Nanjing University, Nanjing 210093, China G. H. Lei, D. Zhang Institute of Solid Physics, Chinese Academy of Sciences, Hefei 230031, China Y P. Jin and G. D. Zhang Lab. of Metal-Matrix Composite Materials, Shanghai liaotong University, Shanghai 200030, China. INTRODUCTION In recent years, there has been increasing interest in nanostructured ceramic materials because of their advanced properties. The superplasticity; improved strength and toughness, higher densification rate and low sintering temperature are observed in these materials[I-4]. The sintering speed Vsintering of ceramic is related to the grain size d by the expression of v sinting oc d --4 [2]. By adding the nano-particles of Ah03 to conventional Ah03, the strength, fracture toughness and thermal resistance of Ah03 ceramic can increaser 5]. Up to now, only a few researchers[6,7] have concerned about the specific heat and thermal expansion of nano- ceramics, and no report about thermal diffusivity of nano-composite has been found in literature. However, characterizations of thermal diffusivity ofnano-composite ceramics are very important for designing and preparing this kind of new materials. Using mirage method to measure thermal diffusivity of material begins at the middle of the eighties[8]. Now, several types of mirage measuring methods, such as the zero crossing method or multiply fitting method, have been developed. Detection is made either in skimming way or in bounding way, either at the front or rear surface of the samples. The pump and probe beams are arranged either in parallel or perpendicular to each other. This method has been used to measure the thermal diffusivity of various new materials, including transparent or opaque materials, solid or liquid, in form of bulk or film with single and multiply layers. We have investigated the thermal diffusivities of bulk, thin film and C-fiber/Cu as well as C-fiber/ A1 composites by means of mirage method[9-11]. The Review of Progress in Quantitative Nondestructive Evaluation, Vol. 17 Edited by D.O. Thompson and D.E. Chimenti" Plenwn Press, New York. 1998 1209 investigation results show that the mirage technique has the advantages of the localized measurement and can suffer a non- specula surface, when used in skimming way. The investigation results on thermal diffusivity of nano-composite ceramics obtained by using the mirage effect method are presented in this paper. EXPERIMENTS Five series of samples are used in our experiments. They are: 86 Ah03 with 86 % of conventional (i.e. rough crystal) Ah03, 96 AiZ0 3 with 96 % of conventional Aiz0 3 and 95 AiZ0 3 with 95 % of conventional Aiz0 3 respectively. They are prepared by rough crystal or composite with nano-phase AiZ0 3, and sintering under different temperatures and environments respectively. The nano-powder Ai20 3 was processed by the technique of hydrolysis of pure aluminum sheet (with the purity of 99.99%) after activation. The average diameter of the powders after transformation to a ex- AiZ0 3 was 27 nm. The preparing procedure of the series of 96 Aiz0 3 samples is describe as follows. The conventional AiZ0 3 powder with the composition of (mole) 96% AiZ0 3 and other being Si02, MgO and CaO was used as starting material. The average grain size of starting material is 0.211m. Different amounts (0,5, 10,20,30 mole %) ofnano-phase AiZ0 3 powders were added to the conventional Ai20 3 powder and ball-milled in ethanol for 24 h. These powder mixes were calcined at 100°C for 24h after being dried. The powder mixes were firstly uniaxially pressed at 100 MPa then isostatically pressed at 300 MPa. These green compacts were sintered at 1450 °C, 1530 °C or 1600 °C for 4 h in air. The density of the sintered bodies was measured using the Archimedes method with distilled water as the immersion medium. The grain size was obtained by a linear-intercept method. The structure of main phase for 86 AiZ0 3 composite ceramics is Ai20 3 plus mullite of 10%, but that for 96 AiZ0 3 composite ceramics is ex - AiZ0 3 We refer these materials as the nano-phase Ai20 3 composite ceramics. The physical parameters and the prepared conditions of these samples are listed in Table l. The sizes of specimens of 86 and 96 Ah03 nano-phase ceramic composites are 6 x 6 xl mm3. The size of specimens of95 AiZ0 3 nano-phase ceramic composites is 3 cm in diameter and 1 mm in thickness. The surfaces of these specimens are not the mirror surface. We measure the thermal diffusivity of these samples by means of the transverse mirage method, in which the probe beam works in skimming way and is at the front surface of sample. The expression for the tangential (x-direction) deflection of the probe beam ( i. e., the tangential component of mirage signal) is given by[8] (1) where n is the index of refraction of the air, T the temperature, x is the separation between the two laser beams:h is the hight of probe beam from the surface of sample. q and K (with the appropriate subscripts) are the thermal wave number and conductivity of air and samples, Rl and Rz the heating- and probe beam radii, respectively. kg and 1<. are given by (2) The thermal diffusivity of sample is calculated by using following equation 1210 Table 1 The physical properties and the prepared conditions of samples No. of Classical Fract- Sintering Density poro- Environ-Sample of ion of temperature (g/cm3) sity mentof specImen nano- eC), and (%) sintering phase time (h) fl# 86-Al203 0% 1510 2.535 37.79 f2# 86-Al203 1% 1510 2.529 37.79 41# 96- Al203 0% 1450 1.823 50.66 air 42# 96-Al203 5% 1450 1.943 47.25 air 43# 96-AlZ0 3 10% 1450 1.953 47.10 air 44# 96- AlZ03 20% 1450 2.091 43.88 air 45# 96-Al203 100% 1450 2.646 27.68 air 141# 96-AlZ0 3 0% 1530,4 2.475 36.51 air 144# 96-Al203 20% 1530,4 2.693 30.94 air 241# 96-Al203 0% 1600,4 3.051 14.35 air 244# 96-Al20 3 20% 1600,4 3.062 13.10 arr 81# 95-Al20 3 0% 1550, 1 3.259 12.05 in AlZ03 82# 95-Al203 5% 1550, 1 3.303 10.31 in Al203 83# 95-Al203 10% 1550, 1 3.178 14.80 in Al203 84# 95-Al203 15 % 1550, 1 3.100 15.45 in Al203 I (.:\x)2 i Dth = l.4n (A.Jf)-2 = nl.4 (3) where Ax is the difference of zero crossing distances of the CPt, f the frequency, s the value of slope of the curve of Ax versus inverse square root frequency. The experimental system used here, which slightly differs from that used by us previously [9-11], is shown in Fig. 1. A pyroelectric device ofPZT is introduced here for simplification of the measurement procedure and for requirement of practice detection. We use photopyroelectric effect ofPZT to eliminate the influence of original phase resulting from the measurement system, when we carry out our experiment. Since the photopyroelectric response ofPZT to the irradiation of a modulated laser beam is fast enough, we regard the phase of the photopyroelectric signal ofPZT, which results from the absorption of the energy of COz laser beam, as the same as the original phase of experimental system. First, we switch on the photopyroelectric signal from the PZT, to feeding it into the A channel oflock-in amplifier (EG & G-5302) at one fixed frequency. Then we adjust the phase button of amplifier to enable the in-phase signal of CPt to becom maximum. In this case, the influence of original phase resulting from the system is considered to reach minimum. The adjusting sensitivity of phase oflock-in amplifier is of 0.1 degree. Finally, we switch off the PZT signal and switch on the signal from the position sensor to begin the detection of mirage signal by scanning the pump beam along the surface of a standard specimen. It should be noted that we need to do the elimination of origin phase for each frequency. When the measured result is the same as the standard value, we fix the conditions of system and begin to detect the mirage signals for the specimens. We use Si wafer as a standard specimen, calculate the CPt ofSi and fit the calculated value of C{lt to the measured one. The hight h of probe beam from the surface of sample can be obtained from the fitting, while the radii of probe and pump beams are measured (here are of 50 and 44.5 Ilm respectively). Measurement results show that to get the curves of zero 1211 C0 2 Laser Moving stage Fig. 1 Schematic diagram of the experimental system for the transverse mirage method. crossing distance versus inverse square root frequency only less than six points of frequency are need. Fig. 2 (a) shows the profile of <Jlt signal for Si wafer, when the pump beam scanning from left to right and backwards. Fig. 2(b) shows the curves of in-phase component versus quarters component of <PI From Fig. 2, we can see that a phase difference may be introduced by the difference of screw's distance when the scanning direction is changed. Therefore, it is necessary to fix the scanning direction to get precise measured results during measuring for each fixed frequency. Experimental results show that the nano-phase Ah03 composite ceramics is the kind of material with larger absorption coefficient of CO2 laser beam and is transparent for visible laser light. So the high enough ratio of signal to noise can be obtained in our experiment. Fig. 3 and Fig. 4 show the curves of zero crossing distance dx of the <PI versus inverse square root frequency for some samples. From Figs. 3 and 4, we obtained the slops of these curves by linear regression fitting. Then we calculate the thermal diffusivities according to the equation (3). The values of thermal diffusivities of the samples are listed in table 2. Fig. 5 (a) shows the relations between the thermal diffusivity and the fraction of nano-phase Al20 3 component for 96 Al20 3 Fig. 5 (b) shows the physical properties, such as the density, porosity, slop of 4000 -=-' ~hooo .0 ~ooo ., "0 .E 1000 in phase quadrnlurc phase J 0 L.......L.""""----............. --'--'--'--'-........................... ____ ............. __ 00 0.5 1.0 I 5 2.0 2.5 3.0 3 .5 Scanning distance (mm) (a) fA 2600 {2400 ., = 2200 0; ~ 2000 .. 6-1800 '-~ 1600 +1 .~ 1400 L--'----'_""---..l.._"---L---''--...J....._ Q, 0 1000 2000 3000 4000 ~ Amplitude of in phase sigoal(arb. unit) (b) Fig. 2 (a) The experimental profiles of in-phase and quadrature signal, obtained by scanning the pump beam from left to right (left) and from right to left (right) respectively. (b) The curves of in-phase signal versus quadrature signal, for scanning from left to right 1 and from right to left 2 respectively, for Si wafer. 1212 0.09 10. ~ ;a :a 0.07 'i e006 ... e ~ 0.05 +-....--r--..-r-'----r--"'r"""""1----.---,---r-, 0.04 0.05 0.06 0.07 0.08 0.09 0.10 Inverse root frequency (a) 0.09 E u '-'008 8 ! :6 0.07 QI) c iii e 0.06 u e o 81~ 82# o 83# 0 84# 009 ~ 0.05 +-=:"--,.--,..........,----.-----r--.---r--.---r--o 0.04 0.05 006 007 0.08 Inverse root frequency (b) Fig. 3 Zero crossing distance (cm) versus inverse root square frequency for (a) 86 Ah03 composite ceramic specimens offl# and f2#, (b) for 95 AI20 3 composite ceramics 81# to 84#, respectively. 0.10 o 141 # 0 10.09 '" 241# x 8 Iij 0.08 1;; '6 QI) 0.07 .5 ~ e 0.06 ... o !::l 0.05 ¥;"":"--.-,-..--y-r.--.,.......,,.,..-.-......--, 0.04 0.05 0.06 0.Q7 0.08 0.09 0 .10 0.11 Inverse square root frequency (a) 0.10 gO.09 v 41# 0 43# "" o 42# 0 44# '-' 0.04 0.05 0.06 0.07 0.08 0.09 Inverse square root fu;quenc (b) Fig. 4 Zero crossing distance (cm) versus inverse square root frequency for 96 AI20 3 composite ceramic specimens of (a) 141#,144#,241# and 244#, (b) 41#, 42#, 43#, 44#, and 45# respectively. curves and thermal diffusivity versus the fractions of nanoparticles for 95 AI20 3, where units of density, porosity, slop and thermal diffusivity are of (glcm3 ), (%), (mmJs) and (mrn2/s) respectively. DISCUSSION From the Fig. 3 and Fig. 4, we can see that: For the conventional AI20 3 ceramics, the thermal diffusivity of86 AI20 3(%) ceramic f1 is higher than that of the 96 AI20 3 (%) ceramic 141#. It means that the thermal diffusivities depend on the fractions and the structures of rough crystal AI20 3 ceramics. The structure of main phase for 86 AI20 3 is AI20 3 plus mullite (10%), while that for 96 AI20 3 is (l- AI20 3. The higher the fraction of conventional rough crystal AI20 3, the smaller the thermal diffusivity was. The thermal diffusivity of96 AI20 3 (%) sintering at 1450 °C (sample 41#) is larger than that of96 AI20 3 sintering at 1350 °C (sample 141#), and the thermal diffusivity of 141# is larger than that of sintering at 1600 °C (sample 241#) It means that the thermal diffusivities depend on the 1213 Table 2 The thermal properties ofnano-phase Ah03 composite ceramics Sample Specific pCp Thermal thermal relative heatCp (J/cm3oC) conductivity diffusivi~ change of (JIg 0c) K(w/cm °C Dth (mm Is) ~ (%) ) fl# 0.7509 1.9038 0.16245 8.53* 0 f2# 0.7387 1.8680 0.04502 2.41* -71.75 41# 0.7071 1.2962 0.22658 17.48 0 42# 0.7261 1.4108 0.17818 12.63 -27.75 43# 1.0633 2.0765 0.23734 11.43 -34.61 44# 0.8965 1.8744 0.15670 8.36 -52.17 45# 0.7225 1.9116 0.09539 4.99 -71.45 141# 0.7194 1.7806 0.09562 5.37 0 144# 0.7192 1.9368 0.22331 11.53 +114.7 241# 0.7279 2.2207 0.08705 3.92* 0 244# 0.7165 2.1939 0.08995 4.10* +4.59 81# 5.89 0 82# 4.47 -24.10 83# 3.63 -38.37 84# 5.91 +0.33 ,-.. 18 0 7 ~ M 16 6 ~ 14 .~ 5 '-' 0 .?;> 12 0 8,4 .s: 'fil 10 0 <E 6,3 ~ 8 0 ] 2 1 6 rn 0 £1 ~ 4 ~ E5 0 -Density, --Porosity ---4-Slop, -Thennal diffusivity o 20 40 60 80 100 0 2 4 6 8 10 . The fraction ofnano- Al 203 (%) Fraction ofnano-meter phase (%) (a) (b) Fig. 5 (a) The thermal diffusivity versus the fraction ofnano-phase Ah03 component for 96 Ah03 composite ceramics, (b) The physical properties versus the fractions of95 Ah03 where unit of density, porosity, slop and thermal diffusivity are of (glcm3 ), (%), (mm/ %) and (mmls) respectively. sintering temperatures of ceramics. The higher the sintering temperature, the lower the thermal diffusivity was. From Fig. 5, it is obvious that the thermal diffusivity is related to the fraction ofnano- phase Ah03 component in the composite ceramic. The higher the value of fraction, the lower the thermal diffusivity was, but it is nonlinear. The thermal diffusivities and their variation with the fraction of nano-phase Ah03 for the specimens sintered in air are larger than that in Ah03 powder. By comparing the experimental results of 141 # and 241 # with that of 144# and 244# respectively, we learn that the thermal diffusivity of samples 144# and 244# ( including nano-phase of 20 %) are larger than that of samples 141 # and 241 #( no nano-phase components included) respectively. This phenomenon is contrary to the law of the samples prepared at the lower 1214 sintering temperature of 1450 °C (cf table 1 and 2). Therefore, we can say that the thermal diffusivity of nano-Ah03 composite cer~c is the function of concentration of conventional Ah03, the fraction of nano-phase Ah03 component, the sintering temperature, and the sintering environment. In addition, we measure the specific heats of nano-Ah03 composite ceramics as a function of temperature by using an instrument of Differential Scanning Calorimeter (PE, America). This Calorimeter can only measure the specific heats for the specimens with limited size ofless 6 mm in diameter and less 1 mm in thickness. Its measuring precise for temperature and caloric are ± 0.1 °C and 0.1 % respectively. For comparing between the specific heats and thermal diffusivities for the same specimens, we measure the specific heats of the 96 Ah03 and 86 composite ceramic specimens. The measured results of specific heats versus temperature will be presented in other paper. The values of specific heats at room temperature listed in Table 2 are obtained by linear intercept method from the curves of specific heats versus temperatures. It is shown that the higher the fraction of nano-phase component, the lower the specific heat is, for the specimens prepared under the sintering temperature 1450 °C. It is contrary to that for the samples sintered under the temperature higher than 1450 °C (cf for 141#,144#, and 241# with 244#). This phenomenon results from grain size effect. The grain size of the specimen sintered under the temperature of 1450 °C is smaller than that sintered under the temperature 1600 °C. The grain size effect of nano-phase Ah03 will appear when the sintering temperature is lower, and that will disappear when the sintering temperature is higher. According to the theory of thermal dynamics, the specific heat is given by dS C =T-P dT (4) where S, and T are the entropy and temperature of the solid system. From this equation, we can see that the main contribution to the specific heat comes from entropy. As long as the temperature is not so lower, the electronic entropy can be omitted. Therefore, the system entropy results from the vibrational entropy and configurational entropy. They are related to the properties of the interfaces and the defects as well as the dislocations. Previous researches show that, for the nano-metal, the specific heat increase with decreasing of grain size and density, because the interfaces of atoms have more opening structures, that enable the coupling between atoms to become weak. However, our experimental results show that, for Al20 3 nano-composite ceramics, it is different from the nano-metal materials because the thermal diffusivity of Al20 3 is lower than that of air. CONCLUSIONS From this study, the following conclusions can be drawn: The transverse mirage method is an useful method for determination of the thermal diffusivity of Al20 3 nano-composite ceramic materials. A CO2 laser beam is used as a pump beam and irradiates the front surface of specimen. The probe beam works in skimming way. The experimental results show that the thermal diffusivity depends on the component fraction ofnano-phase Ah03, the density (or porosity), the sintering temperature, and the sintering environment of samples. 1215 The difference of thermal diffusivities between conventional rough crystal of 86 and 96 Ah03 (i. e., fl# and 141#) is about 37 %, but the differences of thermal diffusivities between the rough crystal 96 Ah03 and nano-composites Ah03 are about 4% to 71 % even up to 114%, depending on the fractions ofnano-phase Ah03 component and the preparing conditions of samples. The higher the sintering temperature and the lower the fraction of nano-phase Ah03 component, the higher the thermal diffusivity was. Reported here is the first experimental results. The measurement precise is about 7%. More investigations for obtaining the systematic law for such materials are under the way. ACKNOWLEDGMENTS This work is supported by the National Science Foundation of China REFERENCES 1. D. Zhang and 1. M. Mau, Nami CailiaoXue (Liaoning Sciences Press, China, 1994) 2. F. Wakai et. al., Adv. Ceram. Mater. 1 (1986) 259 3. I-W. Chen, C. A. Xue, 1. Am. Ceram. Soc. 73 (1990) 2585 4.1. Karch, R. Birringer, Nature 330 (1987) 536 5. G. Li, A. Jiang and L. Zhang, 1. Mater. Sci. Lett. 15 (1996) 1713 6.1. Rupp, R. Birringer, Phys. Rev. B36 (1987) 7888 7. Z. C. Yuan, Master Thesis, Department of Materials Engineering, University of Science and Technology of China (USTC),(1992) 8. P. K. Kuo, L. D. Favro, and R. L. Thomas, in 'Photothermal Investigations of Solid and Fluids' edit. by Jeffiey A. Sell (Academic Press. Inc, 1988) Chapter 6 9. X. R. Zhang, C. M. Gan et. al., Rev. ofProg QNDE vol. 14 Edit. by D. O. Thompson and D. E Chimenti (plenum Press. N. Y. 1995) 467 10. X. R. Zhang, C. M.Gan et. al., Chinese Phys. Lett. 4 (1987) 213 11. X. R. Zhang C. M.Gan et. al., Springer Series in Optical Sciences, 62 edit. by 1. C. Murphyet. al., (Springer - Verlage, Berlin Heidelberg, 1990) 205 1216 

Investigation of Thermal Diffusivity for Nano-Phase Composite Ceramics

F. Xiao

X. R. Zhang

D. Fei

C. M. Gan

G. H. Lei

D. Zhang

Y. P. Jin

G. D. Zhang

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https://dr.lib.iastate.edu/handle/20.500.12876/61313

Investigation of Thermal Diffusivity for Nano-Phase Composite Ceramics

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