NDT.net • July 2004 • Vol. 9 No.07 
The Defective Structure of Plastically Deformed Constructional Steel 12X18X10TPaiziev A.A. and Knyazev E.V.Arifov Institute of Electronics, Academy of Sciences of the Republic of Uzbekistan, Tashkent, Uzbekistan Fax: 998711628767, email: paiziev@glb.net Corresponding Author Contact: Email: paiziev@glb.net AbstractThe defective structure of plastically deformed constructional steel 12X18X10X by a method electronpositron annihilation is investigated. The spectra of angular distribution of annihilation photons are measured for steel with a various degree of plastic deformation from 3 % up to 19.5 %. It is shown, that at plastic deformation defects of dislocation type are generated basically. With use capture model of positrons on defects dislocation type dependences of concentration of dislocations on deformation are received. It is shown, that all range of deformations can be divided into three areas where dependence of annihilation parameters on deformation has linear character.Key words: Steel, plastic deformation, defects, dislocation, positron annihilation. 1. INTRODUCTIONThe positron method has already been successfully used to study the structure and dynamics of lattice defects in metals and alloys [1, 2]. Plastic deformation produces dislocations and vacancy. In single crystals the deformation is simple and produces dislocations but in polycrystalline samples the deformation becomes complex due to the various interactions between dislocations and the grain boundaries [ 3 ]. In plastic deformed metals and alloys the positrons are captured mainly by dislocations (with density r_{d}) and by vacancy (with concentration C_{v}). Other imperfections of a crystal lattice, for example, interstitial atom?, packing defects and grain boundaries as capture centers of positrons can be neglected [ 2 ]. During deformation the interaction of dislocations can lead to rise the formation of jogs and point defects [ 4 ]. At increase of deformation the concentration of point defects is increased, which, merging in the area of a defects sink on boundaries of grains and form complexes of vacancies and dislocations .The next increase of deformation results to formation micro pores. The further increase in deformation results to formation of cracks and destruction of a material. An existing quality testing methods of deformed steels are basically limited such methods as radiography [ 5 ] and method of acoustic emission [ 6 ]. However spatial resolution of these methods is limited by the sizes of micro cracks and micro porous. The method of electronpositron annihilation (EPA) is sensitive in respect of defects as dislocations and vacancies at an initial stage of defectiveness development of a material during plastic deformation. Sensitivity of EPA method in respect of vacancy concentration is found out at ~10^{7} vacancies per atom and reaches a maximum at 1.5·10^{5} vacancies per atom and disappears (reaches saturation) at 10^{3} vacancies per atom. Concerning dislocations the sensitivity of EPA method is shown only at their density 10^{8} sm of length per 1 sm^{2}. Approximately at density of 5·10^{11} sm / cm^{3} saturation [ 2 ] is reached. The density of dislocations may be determined with the help of EPA method on mono crystal and also polycrystalline samples with weak or even strongly expressed texture. However, not enough attention was given heterogeneity of distribution of dislocations, for example in coldrolled samples [ 2 ]. In work [ 7 ] monocrystals of copper subjected deformations by a stretching in a direction [100] and received density of dislocations 1·10^{8}6·10^{9} sm/sm^{3}. In [ 8 ] positron life time and Doppler broadening annihilation line shape measurements have been made to study the recovery behavior of Zn deformed at room temperature. In [ 9 ] noted that defects like vacancy clusters and dislocation loops may be created by deformation as well as by irradiation of austenitic stainless steel AISI 316 (specification of the American Iron and Steel Institute) with energetic particles. In work [ 6 ] is shown, that change of crystal structure austenite in thin sheet stainless steel at a stretching occurs in four stages. It is marked, that between a square of amplitude of signals of acoustic emission and change of martensite concentration deformation there is not magnitude relation. In the present work cited the measurement data of angular distribution of annihilation photons (ADAP) in stainless constructional steel samples 12X18X10T (specification of the Russian State Standard Board) is described. 2. EXPERIMENTAL PROCEDURE2.1 Objects and technique of researches 2.2 Capture model of positrons on defects. (1) with initial conditions n_{d}(0)=0, n_{P}(0)=1, µ_{d}C_{d} capture rate of positrons on defects. After thermalization the positrons may be annihilate in the area of perfect lattice (p) with rate l_{p} or capture by defects (d) with rate µ_{d}C_{d}. On defects the positrons annihilate with rate l_{p}. Solution of equation (1) is: (2) Decay rate L_{1} (L_{1}=t_{p}^{1}, l_{p}= t_{p}^{1}) and L_{2} = l_{d}=t_{d}^{1} and is characteristic for defect type. Using the equations (2) we can determine capture rate of positrons µ_{d}C_{d} and absolute concentration of defects C_{d}. The positron fraction captured and annihilated on defects is: (3) Measurable parameter F is essentially different for positron annihilation in the perfect (F_{p}) and disturbed (F_{}) areas . Such parameters are mean life time of positrons and parameters of shape ADAP spectra. (H, S, W). Using the equation (3) we can get Fparameter as: (4) As we can see from (4) dependence F on C_{d} have S like shape. 3. RESULTS AND DISCUSSIONThe results of the positron annihilation experiments for annealed sample and deformed for difference stage of plastic deformation are shown in Figure 1. The Full Width at Half Maximum (FWHM) of ADAP spectra showed as up triangle figures. Analysis of ADAP spectra exhibits monotone decreasing of FWHM. Approximation FWHM on the difference areas along deformation axis by straight line let us to pick out three areas of plastic deformations differing by slope ratio:FWHM= As+B (5)
Here s signed as degree of deformation (%). On the first section (0.03.7%) rate of change FWHM for percent elongation ~1% is 0.273 mrad/%. On the next stage (3.7%11.2%) the slope ratio is essentially decreased (0.087 mrad/%). The third stage (>11.2%) characterized
by more smaller falling rate of FWHM parameter (0.01 mrad/%). As we can see the maximal sensitivity of FWHM parameter is observed on the first stage plastic deformation (0.03.7%). The total area of sensitivity for FWHM parameter spread up to 10.0%. In the tabl.I boundary of difference stage of plastic deformation is shown. Simultaneously this boundaries compared with acoustic emission data [ 6 ]. The first stage characterizes the interval of microplastic deformation. Just here relevant data is limited. In particular it is known [ 2 ], that in the area of microplastic deformation the features of single dislocations is showed what may be investigated by electronpositron annihilation method. In initial deformation stage especially visible over patching of acoustic emission parameters is observed and spread this stage is estimated up to 2.0% (see Tabl. I). The second stage is characterized most powerful change of austenite crystalline structure and size this stage is 78% according to ADAP spectra and acoustic emission data (see Tabl.I) . Let's estimate sensitivity of shapeparameters of EPA spectra in respect to defects concentration in researched samples. For this purpose we use capture model of positrons on the centers of dislocation type. In the literature is marked that the primary form of defects in deformed steels are dislocations [9]. In particular to it indicate an invariability of the ratio S and W parameters of ADAP spectra. On the Fig. 2 dependence of Sparameter on deformation in steel 10X18H10T and also the ratio S/W is showed.
Apparently from fig. 2 the Sparameter has the form of a curve with saturation in the area of deformations about 810 %. It indicates that at such deformations all positrons are captured on defects and annihilated on bound states. Other argument for the benefit of dislocation nature of defects is fact, that return of the form of ADAP curve occurs only at temperature intensive primary recrystallization, that in opinion of authors [2] is connected to presence of dislocations. Vacancies which arise during plastic deformation are healed in time Furthermore the bonding energy of a positron with a dislocation is essentially greater the bound energy of positron with vacancy. On Fig. 1 and 2 dependences Sand Hparameters are resulted depending on a degree of deformation according to expression (4). At calculation we shall accept for capture rate of positrons on dislocation cross section s =pr_{o}^{2} with radius of a dislocation core r_{o} which it is accepted equal to average value of a lattice constant of steel a=3.58A [2]. Taking into account that for thermalised positron velocity v_{t}=(3kT/m)^{1/2} =3.45·10^{7}sm/s. Then for life time of positron in a perfect area of sample we have t_{3}=l^{1}=^{1}=187ps [ 2 ]. In result using experimental curve H (s) (Fig.1) and the formula (4) it is possible to determine correlation between density of dislocations r (sm^{2}) and a degree of deformation of a sample s (%). Correlation of deformation with concentration of dislocations (curve 1) and part of positrons captured on defects (curve 2) is shown on Fig.3
As we can see from Fig. 3, a sensitivity limit of annihilation parameters regard to density of dislocations makes 10^{7}10^{8} sm^{2}. The greatest sensitivity of a method is reached at density of dislocations 10^{9}10^{10} sm^{2} when all positrons are trapped on dislocations. 4. CONCLUSION
5. REFERENCES

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