The mechanical properties of metal matrix composites (MMCs) reinforced by discontinuous silicon carbides are governed by the properties of the reinforcing phase, as well as their morphology (whisker vs. particulate), orientation and volume fraction. The morphology of SiC particles and their orientation are major variables affecting the anisotropic properties of these composites. SiC whisker (SiCW) reinforced aluminum MMCs tend to have higher strengths and moduli in the extrusion direction due to the high degree of whisker alignment in that direction, and these values are higher than those for SiC particulate (SiCp) reinforced composites at a given reinforcement level [1]. SiCpreinforced MMCs are known to be more isotropic in the extrusion plane. In situations requiring multidirectional reinforcement, particulate reinforced composites can outperform whisker reinforced composites. Thus, it is important to characterize the mechanical properties of these composites in order to develop the criteria for selecting microstructural design variables

Hsu, David K.

Jeong, H. David

Liaw, P. K.

Shannon, R. E.

English

The mechanical properties of metal matrix composites (MMCs) reinforced by discontinuous silicon carbides are governed by the properties of the reinforcing phase, as well as their morphology (whisker vs. particulate), orientation and volume fraction. The morphology of SiC particles and their orientation are major variables affecting the anisotropic properties of these composites. SiC whisker (SiCW) reinforced aluminum MMCs tend to have higher strengths and moduli in the extrusion direction due to the high degree of whisker alignment in that direction, and these values are higher than those for SiC particulate (SiCp) reinforced composites at a given reinforcement level [1]. SiCpreinforced MMCs are known to be more isotropic in the extrusion plane. In situations requiring multidirectional reinforcement, particulate reinforced composites can outperform whisker reinforced composites. Thus, it is important to characterize the mechanical properties of these composites in order to develop the criteria for selecting microstructural design variables.</p

Hsu, David

Shannon, R.

Digital Repository @ Iowa State University (ISU)

ELASTIC MODULI OF SILICON CARBIDE PARTICULATE REINFORCED ALUMINUM METAL MATRIX COMPOSITES INTRODUCTION H. Jeong and O.K. Hsu Center for NDE Iowa State University Ames, IA 50011 R.E. Shannon and P.K. Liaw Metals Technologies Department Westinghouse Science and Technology Center Pittsburgh, PA 15235 The mechanical properties of metal matrix composites (MMCs) reinforced by discontinuous silicon carbides are governed by the properties of the reinforcing phase, as well as their morphology (whisker vs. particulate), orientation and volume fraction. The morphology of SiC pa~ticles and their orientation are major variables affecting the anisotropic properties of these composites. SiC whisker (SiCw) reinforced aluminum MMCs tend to have higher strengths and moduli in the extrusion direction due to the high degree of whisker alignment in that direction, and these values are higher than those for SiC particulate (SiCp) reinforced composites at a given reinforcement level [1] . SiCp reinforced MMCs are known to be more isotropic in the extrusion plane. In situations requiring multidirectional reinforcement, particulate reinforced composites can outperform whisker reinforced composites. Thus, it is important to characterize the mechanical properties of these composites in order to develop the criteria for selecting microstructural design variables. In this paper, we investigated the effect of metal working (extrusion) on the microstructure and mechanical properties of 2124, 6061 and 7091 Al alloys reinforced by 10-30 v/o(volume percent) SiC particulates. Consequently, we examined the microstructure of these composites using scanning electron microscopy(SEM) [2] and image analysis. Image analysis was conducted on the 7091 Al/SiCp system to assess the SiCp orientation distribution in the three mutually perpendicular planes. Image analysis results showed that SiC particles with aspect ratios of 2 to 4 were slightly aligned in the extrusion direction, making these composites macroscopically orthotropic. By measuring ultrasonic wave velocities using the water immersion method [3], we then determined the nine complete elastic stiffness components from which Young's and shear moduli were obtained for each system of composites. The orientation dependence of the measured moduli agreed with the expectation based on particulate alignment. Elastic anisotropies exhibited a maximum difference of about 10% in Young's modulus for 30 v/o SiC samples. Ultrasonically measured Young's moduli Review of Progress in Quantitative Nondestructive Evaluation, Vol. 9 Edited by D.O. Thompson and D.E. Chimenti Plenum Press, New York, 1990 1395 were also compared with those obtained from tensile tests in which specimens were loaded both longitudinally and transversely with respect to the plate extrusion direction. Finally, ultrasonically measured Young's moduli were compared with a model due to Tandon and Weng [4] which is based on a generalization of the method developed by Mori and Tanaka [5] . MATERIALS Three aluminum base alloys of 2124, 6061, and 7091 reinforced by 0-30 v/o SiCp were investigated . A total of 12 samples were studied. These metal matrix composites were fabricated by DWA Composites Specialities, Inc. using a powder metallurgy technique . The composite materials were received in an extruded-plate form with plate dimensions of approximately 1.27 em in thickness, 12.7 ern in width, and 30 ern to 200 em in length . Following extrusion, the 2124 Al/SiCp were T4 heat treated, while the 6061 Al/SiCp and 7091 Al/SiCp were T6 heat treated. MICROSTRUCTURAL ANALYSIS We examined the SiCp orientation distribution in three mutually perpendicular faces . The composite materials are assumed to be orthotropic, with three material symmetry axes. The three symmetry axes are : x1 in-plane extrusion direction, x2 perpendicular to the extrusion plane, and X3 in-plane perpendicular to extrusion direction (Fig. 1). For metallographic examination, three pieces of specimens were cut from one 20 v/o and two 30 v/o 7091 Al/SiCp system with their faces parallel to the symmetry planes. These pieces were ground, and polished by an usual metallographic method. Optical micrographs were taken on each face and micrographs were then analyzed using an image analysis system. Attention was given to the aspect ratio and orientation distribution of SiC particles. Preliminary results showed that most of the SiC particles had elongated shapes with aspect ratios of about 2 to 4. On x1-x2 plane and x2-x3 plane, SiC particles had preferred orientation in x1 and x3 directions, respectively. On x1-x3 face, most particles were randomly oriented, but they were slightly aligned in x1 direction. Fig. 1 shows the typical micrographs and symmetry axes of the material . Fig. 1. 1396 Extrusion Direction -Microstructure of 7091 Al/SiCp MMC (20% loading, Billet No. : PE-2712). ULTRASONIC IMMERSION MEASUREMENT We followed the experimental procedure of ultrasonic immersion method [3] to determine the nine stiffness components for orthotropic composites. The stiffnesses Cll• C22 and C33 are determined from the longitudinal (L) wave velocity propagating along the x1 , x2 and x3 axes, respectively while C12, C13 and C23 require measurements of quasilongitudinal (QL) or quasitransverse (QT) waves propagating at an angle to these axes. In principle, C44, ess and ess may be determined from transverse (T) waves along the x1 , x2 and x3 axes, respectively using shear wave transducers. These stiffness components can also be measured using the immersion technique as described below. Anticipating the energy beam deviation from the phase front normal for oblique incidence [6,7], we cut two parallelepipeds of about 4.0 x 1.5 x 1.2 em from each sample with faces parallel to the symmetry planes. Surfaces were prepared by grinding so that opposite faces are flat and parallel to within 5 pm. Throughout the experiment, two 5 MHz broadband transducers of 1/4 inch diameter were used. The transmitting transducer was driven by a spike voltage pulse. Turntable with 0.1° angle resolution was used to control the incidence angle. Measurements of ell• e22 and e33 In order to measure e 11 , a pulse of L-wave is propagated along the x 1 axis in an immersion setup. By measuring the time delay Llt of the L-wave with and without the sample in the path, the longitudinal velocity VL is calculated from VL = (1'V\r- Llt'd)- 1 where d is the sample thickness and V.r is the sound velocity in water which is a function of temperature. The temperature of the water bath was measured with 0.1" accuracy and the sound velocity equation given in [8] was used. e 11 is then calculated from e 11 = pVt where p is density of the material. e22, and C33 were measured in a similar manner. Measurements at oblique incidence In an oblique incidence through-transmission immersion test, the difference in delay time for the QL-wave with and without the sample in place at an incident angle Ri lS given by cos( Rr - Iii) v1.r in which the refraction angle li, is given by _ 1 sin fli fir= tan ( -lltV,,r) coslii- ~ ( 1) ( 2) The longitudinal phase velocity in the direction lir is then calculated from Snell's law by Similar expressions can be written down for the shear wave in which VL and lir are replaced by phase velocity Vs and refraction angle li~ of QT-wave. Hence by measuring Iii and Llt for the QL and QT waves, one can calculate Rr and li~ and then VL and Vs. It should be noted that the time delay measured by this method is due to the group velocity while the equations for calculating stiffnesses use the phase velocity. 1397 Since the refracted QL and QT waves will travel in non-symmetry directions when the incidence of the beam is oblique, the acoustic wave energy propagates at a deviation angle, u·, as shown in Fig. 2. However, using the relation between the phase and group velocity [9], Vp = Vgcosri·, and Snell's law, it can be shown that the time delay taken by the group velocity is equal to the time delay taken by the phase velocity. Thus, the phase velocity can be correctly measured using the time delay experienced by the group velocity. Measurements of C55 and C12 The sample is oriented with the x3-axis vertical. The pulse is then propagated in the x1-x2 plane. Two refracted waves (QL and QT) can be generated as Pi is increased from zero. ~t, and hence Ar and V, can then be measured for QL and QT waves for different incident angles. With the sample mounted as shown in Fig. 3a, refracted waves will propagate along the vector (n 1 • n2. 0) , where n 1 = sin Hr, n2 = cos Hr, and the velocities of QL and QT waves will satisfy the relationship Equation (4) is quadratic in V2 , so that if two values of CRr.V2 ) are known, it can be solved for c12 and c66 using the values of ell and c22 measured earlier. He measured two sets of (H~.V§) at Hi= 6- and 8', and found c66 and c12. Measurements of Css and C13 1398 The sample is oriented with the x2-axis vertical (Fig. 3b). Obliquely Fig. 2. Fig. 3. ______ _!_h_;:~e-velocity propagation direction Group velocity propagation direction Oblique incidence of sound wave in an orthotropic plate. Sample position for measurements (a) C66 and C12 (b) Css and C13 (c) C44 and C23. A pulse is then propagated in the x1 -x3 plane. Refracted waves will propagate along the vector (nl '0 'n3) ' where nl = sin ar' n3 = cos ar' and the velocities of QL and QT waves will satisfy the relationship Measurements of C44 and C23 The sample is oriented with the x1-axis vertical (Fig. 3c). The pulse is then propagated in the x2-x3 plane. Refracted waves will propagate along the vector (0 ,n2 ,n3)' where n2 =cos ar' n3 =sin ar' and velocities of QL and QT waves will satisfy the relationship : RESULTS AND DISCUSSION Young's moduli in x1 , x2 and x3 directions were computed from the relations : Ell = 1 iSll, E22 = 1 S22, E33 = 1 S33, where Sij denote elastic compliances, wh1ch are related to the 6 x 6 elastic stiffness matrix according to _Sij = 'cij - 1 . Shear moduli in the 2-3, 1-3 and 1-2 planes were obtained from the relations : G23 = C44, G13 = Css, G12 = Cs6. Table 1 shows the experimental results of Young's modulus and shear modulus for the Al/SiCp system. In the SiCp reinforced composite samples, the Young's modulus is the highest along the extrusion direction x1, the next highest along the in-plane transverse direction x3, and the lowest along the out-of-plane direction x2. This ordering of the Young's modulus is consistent with the SiC particle orientation distribution observed in the image analysis. The difference between the extrusion direction (x1 ) and the out-of-plane direction(x2) is about 10 % for 30 v/o SiC samples. Shear moduli have the highest values in the x1-x3 plane, and the difference between G13 and G23 is about 9% in 30 v/o SiCp samples. Shear moduli G12, G13 and G23 can be measured by oblique incidence immersion tests described above or by direct shear velocity measurement using a contact transducer. Fig. 4 shows the comparison of shear moduli measured by the immersion method and the direct contact method. The excellent agreement between the two methods proved the validity of the immersion method. Table 1. Ultrasonic measurement results for the Al/SiCp composites Base Alloy Billet No. (SiC ?.) Ell E22 E33 G12 G13 G23 2124 Al PE 2600 ( 0) 74.7 73.3 75.9 28.0 27·. 2 27.0 2124 Al PE-2404 (25) 122.4 108.0 118.9 42.3 47.1 41.8 ·2124 Al PE-2229 (25) 122.0 108.6 118.2 42.8 46.6 42.2 2124 Al PE-2488 (30) 129.3 116.0 125.6 45.8 50.1 45.6 6061 Al PE-2045 ( 0) 74.0 71.7 73.7 26.9 25.9 26.7 6061 Al PE-2047 (20) 122.1 110.0 118.2 43.0 46.3 42.1 6061 Al PE-2731 (30) 125.5 113.0 122.4 45.4 48.5 44.8 7091 Al PE 2730 c or--7,f:9 73.6 75.5 27.3 26.5 27.0 7091 Al PE-2711 (10) 90.6 84.4 87.8 31.8 32.4 31.0 7091 Al PE-2712 (20) 111.3 99.8 106.2 38.4 41.7 38.0 7091 Al PE-2713 (30) 124.0 112.3 120.4 44.6 47.6 45.3 7091 Al PE-2665 (30) 127.0 116.3 125.6 46.7 49.7 45.4 1399 Fig. 4. 60 ~ .Q 1-::> c: 50 ,~,' 0 '(;; 05 E ,~--£ 40 > ;:fo' ,D C/) :I "'5 ,rffr:J "'0 30 6 G12 0 ~ r;J, D G13 Co 0 G23 Q) .r= (/) 20 20 30 40 50 60 Shear Modulus by Contact UT (GPa) Comparison of shear moduli measured by ultrasonic immersion method with those measured by direct contact method. The ultrasonically measured Young's moduli were also compared with those obtained in mechanical tensile tests. The comparison, shown in Fig. 5, showed that the agreement were usually good to within a few percent. The agreement between these two methods indicates that the ultrasonic immersion technique is a valid method for determining the anisotropic properties of Al/SiCp MMCs. Fig. 5. 1400 140 .-----------------. 8!. (!) "' -"' 120 ~ 100 u ·c: 0 "' ~ 5 80 60 60 ... E 11 ,2124 AJ/SC • E11 ,6061 AJ/SC • E 11 .7091 AJ/SC 6 E33.2124 AJ/SC D E33,6061 AJ/OC o E33.7091 AVSC 80 100 120 Tensile Tests ( GPa ) 140 Comparison of Young's moduli obtained by ultrasonic immersion method with those measured in tensile tests. COMPARISON WITH A MODEL Ultrasonically measured Young's moduli for 7091 Al/SiCp MMCs were compared with a two phase composite model developed by Tandon and Weng (4] . We considered two different distributions of SiC particle orientation: three dimensional random orientation and unidirectional alignment in the x1 direction. While the 3-D random orientation results in a macroscopically isotropic solid, unidirectional alignment gives a transversely isotropic one. Throughout the calculation we assumed the SiC particles to be prolate spheroids with an aspect ratio of 3, and two isotropic elastic constants, E=458 GPa, G=196 GPa (10]. For 7091-T6-Al, E=76 GPa and G=28 GPa were used. Nominal volume fraction of SiCp was used in the calculation. Fig. 6. 140 ~ I 0?. 120 ~ b/a=3 rJ) :::J :; '0 100 0 ~ rJ) 'o c 3-D Random Model :::J ~ 80 • E11 ,Ultrasonic 0 E22 .Uitrasonic • E33 ,Ultrasonic 60 0 6 10 15 20 25 30 SiC Volume {%) Comparison of Young's moduli for 7091 Al/SiCp MMCs with those computed from a model based on 3-D random orientation distribution of SiC particles with an aspect ratio of 3. The calculated results based on a 3-D random orientation are compared to the measured moduli in Fig. 6. The model curve falls between E11 and E22 and is close to E33 in value. Since this model predicts isotropic properties, it does not explain the anisotropic behavior. Fig. 7 shows the comparison with the transversely isotropic model. E11 and E22 calculated by this model agree well with the measured values. The model therefore may be used to predict the highest and lowest Young's modulus of the Al/SiCP MMCs. However, in order to interpret the complete anisotropic elastic behavior, one must consider the orthotropic distribution of the SiC particle orientation. This requires further analytic model development and quantitative measurement of the microstructure. 1401 Fig. 7. 140 E11 ,Transversely Isotropic E22 ,Transversely Isotropic .... 1 • E11 ,Ultrasonic <0 120 0 E22 ,Ultrasonic / • c... / t? • E33 ,Ultrasonic "' ~::;) "0 100 0 ~ ·"' C3 Ol c: ::;) ~ 80 b/a~3 60 0 5 10 15 20 25 30 SiC Volume (%) Comparison of Young's moduli for 7091 Al/SiCp MMCs with those computed from a model based on SiC particles aligned in x1 (extrusion) direction. ACKNOWLEDGEMENT This work was supported by the Center for NDE at Iowa State University and by Westinghouse Electric Corporation. This work was performed at the Ames Laboratory. Ames Laboratory is operated for the U.S. Department of Energy by Iowa State University under contract No. W-7405-ENG-82. REFERENCES 1. J. L. Cook and R. Mohn, in Composites, ASM Handbook Vol. 1, pp. 896-902, ASM International, Metals Park, Ohio, 1987 2. R. E. Shannon and P. K. Liaw, To appear in Metall. Trans. A 3. A. Woolf, Polymer Testing, 5, 375 (1985) 4. G. P. Tandon and G. J. Weng, Compos. Sci. Tech., 27, 111 (1986) 5. T. Mori and K. Tanaka, Acta Metall., 21, 571 (1973) 6. R. D. Kriz, MS Thesis, Virginia Polytechnic Institute and State University, 1976 7. L. H. Pearson and W. J. Murri, in Review of Progress in Quantitative Nondestructive Evaluation, D. 0. Thompson and D. E. Chimenti eds., Vol. 6B, pp. 1093-1101, Plenum Press, New York (1987) 8. W. Kroebel and K. H. Mahrt, Acoustica, 35, 154 (1976) 9. B. A. Auld, Acoustic Fields and Waves in Solids, John Wiley and Sons, New York (1973) 10. E. Schreiber and N. Soga, J. Ameri. Ceram. Soc., 49, 342 (1966) 1402 

Elastic Moduli of Silicon Carbide Particulate Reinforced Aluminum Metal Matrix Composites

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Elastic Moduli of Silicon Carbide Particulate Reinforced Aluminum Metal Matrix Composites

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