It　is　quite　different　from　those　low　to　medium　stacking　fault　energy　face-centered　cubic　metals,　Al　and　most　its　alloys　are　not　applicable　to　twin-induced　grain　boundary　engineering　processing　due　to　their　high　stacking　fault　energy.　In　order　to　optimize　the　grain　boundary　character　distribution　so　as　to　remarkably　better　the　properties　of　Al　and　its　alloys,　it　is　necessary　at　first　to　study　the　grain　boundary　plane　distributions.　In　this　work,　two　parallel　high　purity　(99.99%)　Al　specimens,　which　were　prepared　by　multi-directional　forging　followed　by　re　crystallization　annealing　resulting　in　a　homogeneous　microstructure　with　averaged　grain　size　around　20　lam,　were　separately　processed　by　equal　channel　angular　pressing　(ECAP)　and　direct　rolling　(DR)　with　true　strain　epsilon　approximate　to　2　followed　by　a　recrystallization　annealing　at　360　degrees　C　for　8　similar　to　90　min.　Then,　the　grain　boundary　plane　distributions　were　characterized　by　five-parameter　analysis　(FPA)　based　on　stereology　method　and　electron　backscatter　diffraction　(EBSD).　The　results　show　that　the　grain　boundary　planes　of　the　specimens　as　processed　mainly　orient　on　{111},　mostly　corresponding　to　the　＜　111　＞　twist　high　angle　boundaries.　It　is　due　to　the　energy　minimum　of　{111}.　The　primary　difference　of　grain　boundary　plane　distributions　between　ECAP　and　DR　specimens　lies　in　the　behaviors　of　grain　boundary　planes　orienting　onto　{111}.　For　ECAP　specimens,　it　is　slow　the　grain　boundary　planes　orienting　onto　{111}.　However,　for　DR　specimens,　it　is　quite　easy　the　grain　boundary　planes　orienting　onto　{111}.　Discussions　pointed　out,　compared　with　ECAP　deformation,　DR　deformation　is　more　efficient　for　grain　boundary　plane　orienting　onto　{111}　in　the　subsequent　recrystallization　annealing　and　thus　is　more　in　favor　of　the　optimization　of　grain　boundary　character　distribution.　It　could　be　attributed　to　the　development　of　＜　110　＞//ND　textures　during　DR　deformation　which　results　in　the　fast　grain　growth　in　the　subsequent　recrystallization　annealing.