Whole month was spent on reading scientific literature about my topic. I was focused on the information about morfology and energies of grain boundaries in polycrystalline samples.

In 27-30.09.2011 in Krynica I attended in 39th School in Materials Science.
I presented the presentation (based on the article) during session A (non-ferrous metal alloys).
Below the abstract of mine article:

STRUCTURAL CHANGES IN RECRYSTALLIZATION
OF AA1050 ALUMINIUM ALLOY PROCESSED BY ECAP
J. Poplewska, A. Tarasek, K. Berent, H. Paul
Abstract
This paper describes the development of microstructure after deformation and during recrystallization of AA1050 aluminium processed by equal channel angular pressing (ECAP). The nucleation of new grains and further grain growth were observed in bulk samples after static recrystallization at 270°C. The samples were deformed along route A (no rotation between consecutive passes) through 6 passes, then slightly annealed to obtain the different states of recrystallization. The microstructure was analyzed using high resolution scanning electron microscopy equipped with the local orientation measurements facility. It was observed that the ECAP-processing lead to strong microstructure fragmentation. The as-deformed microstructure was composed of flat (pancake-type) grains with the distance between high angle boundaries in normal direction of about 0.35µm. The low temperature recrystallization led very quickly to microstructure globularization and to their coarsening. After more advanced recrystallization stages the inhomogeneous structure composed of grain classes of different sizes were observed.

Keywords: AA1050 Aluminium alloy; ECAP; Recovery and rekrystallization; Grain growth; EBSD;

One of the goal of this conference was integration PhD students involved in the field of ‘Materials Science’. In this conference about 120 people were attended from seventeen centers in Poland.
There were invited well-known professors who gave lectures on:
- Professor Miroslaw Handke: ‘Silicate materials - from Stone Age to the Present’;
- Professor Marian Szczerka: ‘Tribology - friction and wear in the macro-, micro-and nono-scale’.

In August 2011 I continue the study of stability of homogeneous Zn(II)-Sn(II)-Mo(VI) citrate solutions and the study of electrochemical properties of citrate complexes presented in examinated solutions by cyclic voltammetry method. I conducted research in different hydrodynamic conditions, in the following solutions:
1) 0,65 M Na3HCit; pH=5;
2) 0,65 M Na3HCit; 0,24 M Na2MoO4; pH=5;
3) 0,65 M Na3HCit; 0,08 M SnSO4; pH=5;
4) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,08 M SnSO4; pH=5;
5) 0,65 M Na3HCit; 0,16 M ZnSO4; pH=5;
6) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,16 M ZnSO4; pH=5;
7) 0,65 M Na3HCit; 0,08 M SnSO4; 0,16 M ZnSO4; pH=5;
8) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,08 M SnSO4; 0,16 M ZnSO4; pH=5;
9) 0,65 M Na3HCit; 0,02 M C3H6O; pH=5;
10) 0,65 M Na3HCit; ¬0,12 M Na2SO3; pH=5;
11) 0,65 M Na3HCit; 0,24 M Na2MoO4; ¬0,12 M Na2SO3; pH=5;
12) 0,65 M Na3HCit; 0,08 M SnSO4; ¬0,12 M Na2SO3; pH=5;
13) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,08 M SnSO4; ¬0,12 M Na2SO3; pH=5;
14) 0,65 M Na3HCit; 0,16 M ZnSO4; ¬0,12 M Na2SO3; pH=5;
15) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,16 M ZnSO4; ¬0,12 M Na2SO3; pH=5;
16) 0,65 M Na3HCit; 0,08 M SnSO4; 0,16 M ZnSO4; ¬0,12 M Na2SO3; pH=5;
17) 0,65 M Na3HCit; 0,24 M Na2MoO4; 0,08 M SnSO4; 0,16 M ZnSO4; ¬0,12 M Na2SO3; pH=5;
All the research which I conducted are not completed and I cannot draw out unequivocal conclusions but I’ve got a lot of important information and planned out further investigation.

My research in August:

I used nano-AlN powder to produce third series of composites with 7475 aluminium alloy matrix. As previously, the composites were produced through powder-metallurgy processing. Pre-alloyed 7475 aluminium powders were mixed with ceramic particles and milled in a high energy planetary ball mill.

I also made an literature review concerning heat treatment of composites with aluminium alloy matrix with particular emphasis on precipitation hardening in aging process.

Research in August:

- preparing samples of AA1050 alloy to observations in the scanning electron microscope (EBSD)- grinding, polishing;
- preparing orientation maps of samples of the aluminum alloy after ECAP and recrystallization (in different temperatures and constant time = 1h);
- annealing samples of the aluminum alloy 3004 for 1 h in different temperatures (in the range 100-400°C).

Analysis of obtained results from the scanning electron microscope with used technique EBSD (electron backscattered diffraction) for the alloy AA1050 after different times of annealing in 270°C. In analysis were used tools: TSL OIM Analysis 5 and MS Excel. There were noted the following relationships:

- quantity of low and high angle grain boundaries are decreasing with time of annealing of aluminum alloy at 270°C;
- quantity of low angle grain boundaries calculated to the total number of all boundaries firstly decrease with time of annealing but after 30 min is observed that their number increases;
- the low angle grain boundaries constitute from 18% (for 30min annealing) to 37% (in the deformed state = without annealing), while a high angle constitute from 63% to 82%.