3 mol&#x25; yttria stabilized zirconia matrix has been incorporated with 10 wt&#x25;  single crystal <mml:math id="E1" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mi>&#x03B1;</mml:mi></mml:math>-alumina
platelets to enhance the mechanical reliability. The composites have been produced by different forming
techniques, namely, slip casting, tape casting, and injection moulding followed by pressureless
sintering. Relative density <mml:math id="E2" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mo>&#x223C;</mml:mo></mml:math>99&#x25; has been obtained. Alignment of the platelets in the material was
analyzed by processing the images taken from scanning electron microscopy. Strong texture was
formed by the alignment of platelet. Mechanical properties of the composites were evaluated, and
co-related to the alignment of the platelets.

W-Y. Li

O. T. S&#xF8;rensen

Texture Formed by Platelet Alignment in Ceramic Platelet Ceramic Matrix Composites

Gypsum was set on polyethylene foil of different origin and on cellophane foil. Experiments were
also carried out in an electric field (5-25 kV direct-current). In all cases (especially in the electric
field) (010) textures developed on the contact surfaces and were overlapped by a (121) texture. Brinell
hardness tests show a greater hardness of the contact areas than those of the upper sides of the samples.
Those samples set in an electric field yielded, partly, greater differences. The values, however, diverge
greatly.

D. Vogel

H. Jacobi

H. Follner

H. Klein

Texture Development in Gypsum During Crystallisation

Experimental and theoretical studies have been carried out in order to relate elastic anisotropy to optical
anisotropy by means of photoelasticity. The fundamentals of anisotropic photoelasticity have been
described. Specimens of monocrystalline and polycrystalline silver chloride have been submitted to
tensile stress and relative retardation and extinction angles observed in polarized monochromatic light
to show conformity to the theories which quantitatively relate the state of stress and optical phenomena.
Textures of cold-rolled as well as of recrystallized silver chloride specimens were determined with
an X-ray goniometer. Texture determining parameters such as degree of rolling and recrystallisation
time and temperature have been varied. Textures found in silver chloride after various processing have
been characterized.

P. Dietz

H. Giele&#xDF;en

Texture Development and Anisotropic Photoelastic Properties in Rolled Silver Chloride

The regularities of phase changes and texture formation in composite superconductors Ag-HTSC-Ag,
produced by electrophoretical deposition, are studied. Depending on phase composition of the initial
ceramic powder, cyclic treatment of the composites, including pressing and annealing, results in different
development of the basal texture, being necessary for attainment of high critical current density.The basal texture forms primarily in the phase 2212, which prevailed in the initial ceramic powder
and transforms gradually into the phase 2223 during heat treatment. The derivative phase 2223, being
of practical interest, shows either heritage or scattering of the basal texture in accord with the liquid
phase content in the sample under annealing. Mechanisms of texture development in ceramic phases
were proposed.A diagram for composites Ag-HTSC-Ag, connecting their phase composition and texture perfection
with measured critical current density, is constructed.

Yu. Perlovich

M. Isaenkova

A. Shikov

N. Kalinin

T. Gorshkov

Phase Composition, Texture and Current-Carrying Ability of Ag-HTSC-Ag Three-Layer Conductors

A dispersed, low-solids-fraction suspension containing <mml:math id="E3" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mrow><mml:mtext>Ce-ZrO</mml:mtext></mml:mrow><mml:mn>2</mml:mn></mml:msub></mml:mrow></mml:math>, fine <mml:math id="E4" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mrow><mml:mtext>Al</mml:mtext></mml:mrow><mml:mn>2</mml:mn></mml:msub><mml:msub><mml:mtext>O</mml:mtext><mml:mn>3</mml:mn></mml:msub></mml:mrow></mml:math> and 5 vol&#x25; <mml:math id="E5" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mrow><mml:mtext>Al</mml:mtext></mml:mrow><mml:mn>2</mml:mn></mml:msub><mml:msub><mml:mtext>O</mml:mtext><mml:mn>3</mml:mn></mml:msub></mml:mrow></mml:math>-platelets
was segregated using centrifugal consolidation to produce functionally gradient laminates (FGLs).
Platelet alignment facilitated efficient packing of highly anisometric platelets to high densities. The
complexity and anisotropy of the microstructure warrants a quantitative analysis of the microstructural
evolution prior to any property evaluation. Quantitative image analysis was used to examine changes
in the volume fraction, dimensional anisotropy, and gradient of pores and platelets with sintering time.
In all cases, special attention was given to the effects of texture during microstructural evolution. Platelet
alignment enhanced densification via anisotropic shrinkage, overcoming constraint that otherwise inhibits
densification in platelet-containing materials. Also, platelet alignment and microstructural design were
used to initiate and control anisotropic grain growth. Platelet growth (at the expense of smaller particles
of the same phase) during annealing promoted further phase segregation and produced higher platelet
content composites consisting of larger platelets, without having to consolidate high contents of large
platelets.

Ryan K. Roeder

Keith J. Bowman

Kevin P. Trumble

Texture and Microstructure Development in <svg style="vertical-align:-3.3907pt" height="16.450001" version="1.1" viewBox="0 0 41.587502 16.450001" width="41.587502" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.162)"><path id="x41" d="M673 0h-245v28q47 6 58 16t1 39l-55 154h-213q-31 -87 -36 -129q-16 -47 -5 -61t68 -19v-28h-226v28q50 7 68.5 23.5t43.5 80.5l214 524l24 9l193 -536q23 -63 41.5 -79.5t68.5 -21.5v-28zM418 280l-81 255h-2q-74 -197 -101 -255h184z" /></g><g transform="matrix(.017,-0,0,-.017,11.843,12.162)"><path id="x6C" d="M238 0h-223v26q48 5 60 17t12 61v473q0 50 -10.5 60.5t-58.5 15.5v24q73 8 148 35v-608q0 -49 11.5 -61t60.5 -17v-26z" /></g><g transform="matrix(.012,-0,0,-.012,16.162,16.25)"><path id="x32" d="M412 140l28 -9q0 -2 -35 -131h-373v23q112 112 161 170q59 70 92 127t33 115q0 63 -31 98t-86 35q-75 0 -137 -93l-22 20l57 81q55 59 135 59q69 0 118.5 -46.5t49.5 -122.5q0 -62 -29.5 -114t-102.5 -130l-141 -149h186q42 0 58.5 10.5t38.5 56.5z" /></g><g transform="matrix(.017,-0,0,-.017,22.5,12.162)"><path id="x4F" d="M381 665q131 0 226.5 -93t95.5 -239q0 -158 -96 -253t-238 -95q-137 0 -231 95t-94 238q0 142 92.5 244.5t244.5 102.5zM359 629q-89 0 -151 -74.5t-62 -208.5q0 -141 69 -233t175 -92q90 0 150.5 74t60.5 211q0 152 -69 237.5t-173 85.5z" /></g><g transform="matrix(.012,-0,0,-.012,35.188,16.25)"><path id="x33" d="M285 378v-2q65 -13 102 -54.5t37 -97.5q0 -57 -30.5 -104.5t-74 -75t-85.5 -42t-72 -14.5q-31 0 -59.5 11t-40.5 23q-19 18 -16 36q1 16 23 33q13 10 24 0q58 -51 124 -51q55 0 88 40t33 112q0 64 -39 96.5t-88 32.5q-29 0 -64 -11l-6 29q77 25 118 57.5t41 84.5&#xA;q0 45 -26.5 69.5t-68.5 24.5q-67 0 -120 -79l-20 20l43 63q51 56 127 56h1q66 0 107 -37t41 -95q0 -42 -31 -71q-22 -23 -68 -54z" /></g></svg>-Platelet Reinforced <svg style="vertical-align:-3.3907pt" height="16.450001" version="1.1" viewBox="0 0 109.25 16.450001" width="109.25" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.162)"><path id="x43" d="M614 175l29 -10q-33 -109 -57 -154q-121 -26 -184 -26q-90 0 -160.5 29t-112.5 77t-63.5 105.5t-21.5 119.5q0 157 108 253t277 96q36 0 71.5 -5t69 -13.5t36.5 -8.5q15 -102 20 -150l-29 -8q-20 79 -66.5 114t-128.5 35q-119 0 -187.5 -86t-68.5 -207&#xA;q0 -140 73.5 -227.5t188.5 -87.5q73 0 119.5 37.5t86.5 116.5z" /></g><g transform="matrix(.017,-0,0,-.017,11.605,12.162)"><path id="x65" d="M380 106l15 -22q-42 -52 -87 -74t-76 -22q-89 0 -142 62t-53 151q0 103 66 175q67 73 146 73h1q61 0 105.5 -46.5t44.5 -105.5q0 -16 -4.5 -22.5t-18.5 -9.5q-54 -10 -262 -17q1 -95 46 -143.5t104 -48.5q61 0 115 50zM225 412q-35 0 -64.5 -32.5t-40.5 -90.5q83 0 170 3&#xA;q14 0 19 4.5t5 15.5q1 41 -23.5 70.5t-65.5 29.5z" /></g><g transform="matrix(.017,-0,0,-.017,18.829,12.162)"><path id="x2D" d="M300 253l-14 -55h-229l14 55h229z" /></g><g transform="matrix(.017,-0,0,-.017,24.881,12.162)"><path id="x5A" d="M561 176l29 -6q-25 -130 -36 -170h-517l-8 15l420 599h-173q-77 0 -102 -7t-39 -29q-19 -29 -35 -87l-29 1q9 111 12 183h24q9 -16 19 -20.5t34 -4.5h399l7 -14l-413 -594q48 -6 163 -6q94 0 131.5 7.5t58.5 29.5q28 29 55 103z" /></g><g transform="matrix(.017,-0,0,-.017,35.369,12.162)"><path id="x72" d="M181 342h2q63 107 121 107q24 0 41 -16t17 -34q0 -34 -32 -49q-17 -7 -26 2q-21 20 -43 20q-20 0 -42 -22t-38 -63v-183q0 -50 12.5 -62t69.5 -16v-26h-230v26q47 5 58 17t11 61v207q0 49 -9 60.5t-53 16.5v23q74 12 141 40v-109z" /></g><g transform="matrix(.017,-0,0,-.017,41.675,12.162)"><use xlink:href="#x4F"/></g><g transform="matrix(.012,-0,0,-.012,54.388,16.25)"><use xlink:href="#x32"/></g><g transform="matrix(.017,-0,0,-.017,60.725,12.162)"><path id="x2F" d="M368 703l-264 -866h-60l265 866h59z" /></g><g transform="matrix(.017,-0,0,-.017,67.728,12.162)"><use xlink:href="#x41"/></g><g transform="matrix(.017,-0,0,-.017,79.509,12.162)"><use xlink:href="#x6C"/></g><g transform="matrix(.012,-0,0,-.012,83.825,16.25)"><use xlink:href="#x32"/></g><g transform="matrix(.017,-0,0,-.017,90.162,12.162)"><use xlink:href="#x4F"/></g><g transform="matrix(.012,-0,0,-.012,102.862,16.25)"><use xlink:href="#x33"/></g></svg> Laminates Produced by Centrifugal Consolidation

Glass ceramics of the composition <mml:math id="E2" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mrow><mml:mtext>Li</mml:mtext></mml:mrow><mml:mn>2</mml:mn></mml:msub><mml:mtext>O</mml:mtext><mml:mo>&#x22C5;</mml:mo><mml:msub><mml:mrow><mml:mtext>2SiO</mml:mtext></mml:mrow><mml:mn>2</mml:mn></mml:msub></mml:mrow></mml:math>.were prepared with an oriented microstructure. The
oriented crystalline phase is orthorhombic lithium disilicate. This orientation was achieved by
crystallization of glass fibers and bulk glasses in a temperature gradient and under isothermal conditions.
Both bulk and surface crystallization were achieved. Further, oriented crystalline films were prepared
on glassy and crystalline substrates by a sol-gel method. Scanning electron microscopy and atomic force
microscopy were used to characterize the microstructure. The degree of orientation was investigated
by X-ray pole figure measurements from which orientation distribution functions and inverse pole figures
were calculated. The (002) plane of the surface crystallized material shows a strong fiber texture parallel
to the surface of the sample.

Katja Engel

G&#xFC;nther Heinz Frischat

Texture Formation in a Glass Ceramic of <svg style="vertical-align:-3.27605pt" height="15.5125" version="1.1" viewBox="0 0 84.087502 15.5125" width="84.087502" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,11.363)"><path id="x4C" d="M495 163l30 -6q-19 -99 -36 -157h-453v28q63 5 77.5 20t14.5 78v400q0 63 -13 77t-75 19v28h261v-28q-61 -5 -74.5 -19t-13.5 -77v-395q0 -41 5 -59t18 -25q24 -13 96 -13q85 0 112 31q30 33 51 98z" /></g><g transform="matrix(.017,-0,0,-.017,9.293,11.363)"><path id="x69" d="M135 536q-20 0 -35 15.5t-15 35.5q0 22 15 37t36 15t35.5 -15t14.5 -37q0 -21 -15 -36t-36 -15zM252 0h-220v26q48 5 59 17t11 63v206q0 47 -9 58t-54 18v24q78 12 142 39v-345q0 -51 11.5 -63t59.5 -17v-26z" /></g><g transform="matrix(.012,-0,0,-.012,13.863,15.45)"><path id="x32" d="M412 140l28 -9q0 -2 -35 -131h-373v23q112 112 161 170q59 70 92 127t33 115q0 63 -31 98t-86 35q-75 0 -137 -93l-22 20l57 81q55 59 135 59q69 0 118.5 -46.5t49.5 -122.5q0 -62 -29.5 -114t-102.5 -130l-141 -149h186q42 0 58.5 10.5t38.5 56.5z" /></g><g transform="matrix(.017,-0,0,-.017,20.2,11.363)"><path id="x4F" d="M381 665q131 0 226.5 -93t95.5 -239q0 -158 -96 -253t-238 -95q-137 0 -231 95t-94 238q0 142 92.5 244.5t244.5 102.5zM359 629q-89 0 -151 -74.5t-62 -208.5q0 -141 69 -233t175 -92q90 0 150.5 74t60.5 211q0 152 -69 237.5t-173 85.5z" /></g><g transform="matrix(.017,-0,0,-.017,36.672,11.363)"><path id="x22C5" d="M170 255q0 -25 -16 -41t-40 -16t-40 16t-16 41t16 41.5t40 16.5t40 -16.5t16 -41.5z" /></g><g transform="matrix(.017,-0,0,-.017,44.321,11.363)"><use xlink:href="#x32"/></g><g transform="matrix(.017,-0,0,-.017,52.481,11.363)"><path id="x53" d="M409 504l-29 -5q-16 60 -44.5 96t-86.5 36q-54 0 -82.5 -32t-28.5 -77q0 -51 30.5 -82.5t96.5 -65.5l35.5 -18t33 -19.5t33.5 -23.5l27 -25.5t24.5 -32t13.5 -36.5t6 -45q0 -80 -62 -134.5t-160 -54.5q-47 0 -98 15q-22 7 -50 21q-8 23 -27 155l30 7q7 -27 18 -52&#xA;t30 -51.5t49 -42.5t67 -16q56 0 88 32.5t32 87.5q0 51 -31.5 82t-98.5 67q-80 44 -110 73q-55 53 -55 124q0 75 56 126.5t150 51.5q53 0 126 -23z" /></g><g transform="matrix(.017,-0,0,-.017,60.453,11.363)"><use xlink:href="#x69"/></g><g transform="matrix(.017,-0,0,-.017,65.009,11.363)"><use xlink:href="#x4F"/></g><g transform="matrix(.012,-0,0,-.012,77.7,15.45)"><use xlink:href="#x32"/></g></svg> Composition

Dry pressing and filtration of a mixture of platelike corundum and rutile powders shows a slight to
sharp texture of the corundum particles. The reaction sintering forming aluminum titanate destroys the
texture of the green compact. When starting with a rutile texture in the green compact there exists a
texture of tielite in the reaction product. Furthermore we developed a process for production of platelike
tielite monocrystalline particles which should be very suited for texturing of the ceramic material.

C. Schmalzried

J.-W. Kim

H. W. Hennicke

Texture in Aluminum Titanate Ceramic Materials

Texture formation in pure shear deformed rock salt has been studied by neutron diffraction. The
textures developed are comparable to those of rolled face-centered cubic metals with high stacking
fault energy. At room temperature the texture consists of a strong S and copper and a weaker brass
component. It is replaced by static and/or dynamic recrystallization by a strong cube and a subordinate
Goss component. Comparison of the experimental textures with simulations based on different models
shows that the low temperature high strain deformation texture can be qualitatively well explained
by the Taylor model using slip on <mml:math id="E1" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow></mml:mrow></mml:math><mml:math id="E2" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math>, <mml:math id="E3" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>100</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow></mml:mrow></mml:math><mml:math id="E4" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math> and <mml:math id="E5" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>111</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow></mml:mrow></mml:math><mml:math id="E6" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math> systems with equal
critical resolved shear stresses. Relaxation with increasing temperature introduces the cube and Goss
component, which may represent the nuclei for recrystallization. The study shows that texture
simulations on salt without considering recrystallization lead to misleading conclusions.

W. Skrotzki

K. Helming

H.-G. Brokmeier

H.-J. Dornbusch

P. Welch

Textures in Pure Shear Deformed Rock Salt

Several prior investigations have documented deformation-induced rotation of <mml:math id="E3" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mi>&#x03B2;</mml:mi></mml:math>-<mml:math id="E4" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mrow><mml:mtext>Si</mml:mtext></mml:mrow><mml:mn>3</mml:mn></mml:msub><mml:msub><mml:mtext>N</mml:mtext><mml:mn>4</mml:mn></mml:msub></mml:mrow></mml:math> grains resulting
in texture and property anisotropy. As documented previously for axisymmetric textures, Jeffery-based
models correlate well with experimental results for a limited range of strains in plane strain deformation.
Comparison to other experimental results and the implications of these results on texture modeling
are discussed.

Peter Miller

David Collins

Inna Golinkin

Keith Bowman

Plane Strain Deformation Textures of <svg style="vertical-align:-3.56265pt" height="16.6625" version="1.1" viewBox="0 0 10 16.6625" width="10" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.162)"><path id="x1D6FD" d="M558 587q0 -32 -14 -61t-40 -53.5t-48.5 -41t-54.5 -36.5q144 -51 144 -174q0 -55 -43.5 -108t-104.5 -87q-77 -42 -131 -42q-31 0 -54 20t-31 47l11 18q48 -29 108 -29q79 0 119.5 43t40.5 109t-44.5 107.5t-119.5 50.5l22 47q34 1 65 21q96 61 96 157q0 42 -24 67.5&#xA;t-62 25.5q-24 0 -43.5 -9t-35 -29.5t-27 -44t-22.5 -63t-19.5 -75.5t-18.5 -91q-57 -294 -68 -380q-26 -190 -35 -200q-26 -31 -97 -37l-4 26q19 9 48 170l77 413q23 121 52.5 187.5t83.5 114.5q70 62 148 62q51 0 88.5 -34t37.5 -91z" /></g></svg>-<svg style="vertical-align:-3.3907pt" height="15.65" version="1.1" viewBox="0 0 37.9375 15.65" width="37.9375" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,11.362)"><path id="x53" d="M409 504l-29 -5q-16 60 -44.5 96t-86.5 36q-54 0 -82.5 -32t-28.5 -77q0 -51 30.5 -82.5t96.5 -65.5l35.5 -18t33 -19.5t33.5 -23.5l27 -25.5t24.5 -32t13.5 -36.5t6 -45q0 -80 -62 -134.5t-160 -54.5q-47 0 -98 15q-22 7 -50 21q-8 23 -27 155l30 7q7 -27 18 -52&#xA;t30 -51.5t49 -42.5t67 -16q56 0 88 32.5t32 87.5q0 51 -31.5 82t-98.5 67q-80 44 -110 73q-55 53 -55 124q0 75 56 126.5t150 51.5q53 0 126 -23z" /></g><g transform="matrix(.017,-0,0,-.017,8.018,11.362)"><path id="x69" d="M135 536q-20 0 -35 15.5t-15 35.5q0 22 15 37t36 15t35.5 -15t14.5 -37q0 -21 -15 -36t-36 -15zM252 0h-220v26q48 5 59 17t11 63v206q0 47 -9 58t-54 18v24q78 12 142 39v-345q0 -51 11.5 -63t59.5 -17v-26z" /></g><g transform="matrix(.012,-0,0,-.012,12.575,15.45)"><path id="x33" d="M285 378v-2q65 -13 102 -54.5t37 -97.5q0 -57 -30.5 -104.5t-74 -75t-85.5 -42t-72 -14.5q-31 0 -59.5 11t-40.5 23q-19 18 -16 36q1 16 23 33q13 10 24 0q58 -51 124 -51q55 0 88 40t33 112q0 64 -39 96.5t-88 32.5q-29 0 -64 -11l-6 29q77 25 118 57.5t41 84.5&#xA;q0 45 -26.5 69.5t-68.5 24.5q-67 0 -120 -79l-20 20l43 63q51 56 127 56h1q66 0 107 -37t41 -95q0 -42 -31 -71q-22 -23 -68 -54z" /></g><g transform="matrix(.017,-0,0,-.017,18.912,11.362)"><path id="x4E" d="M719 650v-28q-43 -2 -62 -15t-22 -44q-6 -47 -6 -169v-403h-31l-426 524h-2v-251q0 -111 6 -169q4 -37 24 -50.5t72 -16.5v-28h-237v28q45 2 64.5 16t23.5 49q6 62 6 171v220q0 54 -3 68.5t-17 32.5q-16 19 -34.5 26.5t-54.5 10.5v28h147l418 -502h3v246q0 117 -7 166&#xA;q-4 34 -24.5 47t-73.5 15v28h236z" /></g><g transform="matrix(.012,-0,0,-.012,31.537,15.45)"><path id="x34" d="M456 178h-96v-72q0 -51 12.5 -62.5t72.5 -16.5v-27h-256v27q65 5 78 17t13 62v72h-260v28q182 271 300 426h40v-407h96v-47zM280 225v295h-2q-107 -148 -196 -295h198z" /></g></svg> 

The occurrence of axisymmetric textures prevails over a wide range of processing approaches for
alumina-based materials. Mechanisms ranging from dislocation slip, recrystallization, anisometric grain
rotation and grain growth all can contribute to the development of textures with similar characteristics.
This paper documents neutron texture measurements of axisymmetric textures in hot-pressed, hot-forged
and tape-cast alumina. Strong basal textures were introduced in the tape-cast samples during long term
annealing in finer, non-tabular aluminas if glass and dopant additions are introduced. The implications
of these results versus prior reports of textures in alumina and alumina matrix composites are discussed.

Nicholas W. Medendorp, Jr.

Keith L. Kruger

Dorte Juul Jensen

O. Toft S&#xF8;rensen

Axisymmetric Textures in Alumina

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Special Issues

Texture, Stress, and Microstructure | Hindawi

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Texture, Stress, and Microstructure

<p>This Issue is now open for submissions.</p>
<p>Papers are published upon acceptance, regardless of the Special Issue publication date.</p>


Call for papers