SCIENTIFIC ABSTRACT GARBER, R.I. - GARBER, R.I.

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• Collection: Scientific Abstracts
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• Release Decision: RIF
• Original Classification: S
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• Document Creation Date: November 2, 2016
• Document Release Date: July 19, 2001
• Sequence Number: 1
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

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R.I. - POLTAKOV, L. M.
ARM-.
Investigating sub-microscopic nonuniformities of rock salt after
p2aatic deformation. 7iz. tyer. tela 2 no.5:974-981 My 160.
(MIRA 13: 10)
1. 7iziko-takhnicheakiy institut AN USSR, rhar'kov.
(Salt) (Deformations (Mechanics))

- 'k- 81616
/' 1 3.yo S/ I 81160100;el Uo/ 04/050
le, 8100 B122/BO63
AUTHORS: Garber, R. I., Zalivadnyy, S. Ya., Mikhaylovskiy, V. M.
TITLE: Change in the Microstructure of Uranium by Cyclic Heat
Treatment 0
PERIODICAL: Pizika tverdogo tela, 1960, Vol. 2, No. 6, pp. 1052-1059
TEXT: When subjected to cyclic heat treatment, uranium exhibits
irreversible growth which has been given different explanations in
publications. In order to clarify this problem, the authors of the
present paper examined the change in the microstructure of uranium,
i.e., the process taking place inside and on the grain boundaries of
polycrystalline uranium during cyclic heat treatment. The metal surface
was examined microscopically and photographed with a camera of the type
M(M-l (MFN-1). Fig. I shows the scheme of the system. The uranium
samples were prepared in such a way that coarse, columnar grains
developed in the center of the sample (Fig. 2). The deformation of the
grains was observed by the changes in etched lines. Sample No. 1 was
Card 113

81616
Change in the Microstructure of Uranium S118116010021061041050
by Cyclic Heat Treatment B122/BO63
heated 200 times from 100 to 6000C, No. 2 300 times, and No. 3 50 times
in the course of 5 min, cooling took 4 min, the peak temperature lasted
1 min. Figs. 3-6 illustrate the changes undergone by the samples
No. 1-3. A curvature in the etched lines and a mutual displacement of the
grains was observed in all samples. In some cases, a distortion of the
grain boundaries was observed in addition to the mutual displacement.
It was further observed that at peak temperature there was a jump in the
lines, which again vanished on cooling. The direction of these jumps
changed after about 10 cycles, and remained the same on a further cyclic
treatment. This thermoelastic deformation is assumed to be related with
the anisotropic thermal expansion of uranium. The disorientation of the
grains in the course of the cyclic treatment is examined roentgeno-
graphically. The greatest possible displacement of grains was determined
from the degree of disorientation and the difference between the thermal
expansion coefficients of touching bodies; the displacement corresponding
to the mechanism of "thermal wedging" is likewise determined and
c,@-_,ared with the displacement observed experimentally. The displacement
observed was found to differ only little from the one determined by the
Card 2/7
Y

81616
Change in the Microstructure of Uranium S/181/60/002/06/04/050
by Cyclic Beat Treatment B122/BO63
mechanism of "thermal wedging", whereas it is two orders smaller 'than the
greatest possible, i.e., only a small part of the thermoelastic
displacements becomes irreversible. It was further established by X-ray
pictures (multiplication of the original spots on the single crystals)
that a splitting of the grain takes place in blocks by cyclic thermal
treatment. The residual displacement of grains, which ultimately causes
the uranium growth, is ascribed to the formation of undersize grains, the
plastic deformation in the boundary zone of weak grains, and the
displacement of grains on their cooling. There are 8 figures, I table,
and 11 references: 7 Soviet and 1 British.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR, Khar1kov
(Physicotechnical Institute of the AS UkrSSR, Khar1kov)
SUBMITTED: February 24, 1958
Card 313

81620
SIIB116010021061061050
4, 9400 B122/BO63
AUTHORS: Garber, R. I., Gindin, I. A., Polyakov, L. M.
TITLE.- Dispersion and Re-establishment of Contacts Between Micro-
blocks DurinK Plastic Deformation*2(0
PERIODICAL Fizika tverdogo tela, 1960, Vol. 2, No. 6, pp. 1089 - 1095
TEXT: The low strength of solid bodies after deformation is ascribed to
dislocations, fractures, and microcracks and the resulting concentratiod
of strains which attain the value:of theoretical strength in microregions.
Furthermore, the formatioY4 splitting, and disorientation of microblockB are
observable. The concentration of strains may be regarded as an increase in
latent energy which is due to the extension of the inner surface brought
about by disorientation. The surface energy of the liberated parts of the
block surfaces would pass over into latent energy. The block dimensions
themselves have a specific value for every material. According to B. M. Ro-
vinskiy and L. M. Rybakova (Ref. 7), this value constitutes a mean value of
split and restored blocks. In this connection, the saturation of the latent
deformaiion energy corresponds to the stabilization of the mean block
Card 1/3 vx/

81620
Dispersion and Re-establishment of Contacts S/18 60/002/06/08/050
Between Microblocks During Plastic Deformation B122XBo63
dimensions. The surface energy is determined by formula;y %- a (1),
3, 7 . S/12@
where (x = V/1 v denotes the volume of the block, 1 its length,
S is the surface, @is the material density, Q is the latent energy of
plastic deformation on saturation referred to the sample mass, and a is
the mean surface tension. As an example, y has the value 0-5 for copper,
i.e., on plastic deformation of copper a considerable part of the block
surfaces is without contact with the neighboring blocks. It is then consi-
dered that a part of the latent deformation energies must be alse ascribed
to other causes, such as lattice defects, dislocations, and residual stres-
ses. The latter are determined in metals roentgenographically, and do not
amount to more than 2 % of Q. Atomic dispersion and imperfections, de-
termined from the change of resistivity as a result of plastic deformation,
correspond to only 5 %'Of the latent energy Q. @hus,alxiost-.the entire latent
energy of the plastic deformation was found to be present as the energy of
the free block surfaces. The process of contact re-establishment was studied
on pressed and high-vacuum heated copper disks, on the change of the flow
ve'--it7 of hydrogen through iron tubes, which were deformed at the temper-
atures of liquid nitrogen, and finally, on the change, caused by anneali
Carc@ 2/)

81620
Dispersion and Re-establishment of Contacts S/181/60/002/06/08/050
Between Mioroblocks During Plastic Deformation B122/BO63
in light dispersion intensity of deformed rock salt samples. The setups
used for the investigation are shown in Figs. I - 5, and respective re-
sults in Figs. 6 - 9. The studies revealed that the activation energy of
contact formation in copper decreases with rising pressure, i.e. the said
formation proceeds very quickly at a certain pressure and also at low
temperatures. In the case of iron, a recrystallization occurs under the
given conditions, which, howeverg does not necessarily give rise to con-
tacts. It is concluded therefrom that at a certain deformation stage there
is a firm inte'rlinkage between the various contact faces of the blocks
besides dispersion and disorientation. There are 9 figures and 15 refer-
encesi 10 Soviet, 3 English, 1 Japanese, I American.
ASSOCIATIONs Fiziko-tekhnicheskiy institut AN USSR, Kharlkov (Physico-
technical Institute of the AS UkrSSR. Khar1kov)
SUBMITTED: August 11, 1959
Card 3/3

81621
S/181/60/002/06/09/050
/.0 82,oo B122/BO63
AUTHORS: Garber, R. 1.9 Qindin, I. A.q Lazarev, B. G., Starodubov, Ya.D.
TITLE: Low-temperature Recrystallization of Copper
PERIODICAL& Fizika tverdogo tela, 1960, Vol. 2, No. 6, pp. !096 1098
TEXT: The authors of the present article studied the rocrystallization of
copper which was first deformed at the temperatures of liquid hydrogen and
nitrogen, and was then subjected to recrystallization at room temperature.
Tubular copper samples (diameters 1-5 mm; wall thicknessa 0.45 mm) were
use.d. The samples were first annealed at 800 0C for 8 hours (at 10-6 torr).
Special care was devoted to the perfect cleanliness of the inner wall of
the tube. The sample was deformed in vacuo at.20 and 4.20K perpendicular to
the tube axis until the inner walls touched, and further, until the plastic
deformation X - 23 %. The sample was then heated at low,'pressure, and kept
at room temperature for 10 - 15 hours. Recrystallization was observed on a
cut -@f the cross section of the tubes after deep etching, by using a metal-
lographical microscope of the type M@M-6 (MIM-6)(Figs. 1 and 2). Small
Card. 1/2 9

GARBER, R.I.; STEFINA, Ta.l.
Etching figures of wedged elastic twins. Kristallografiia 5
no-5:811-813 S-0160. (MIRA 13:10)
1. F12iko-tekhnicheskiy institut AN USSR.
(Urystallograpby) (Calcite)

,2100 s/126/6o/oog/02/019/033
EOAJ/K@
AUTHORS: Garber, R.I., Zalivadnyy, S. a. a l4okhovatskiy,_F.S.
I -tt.0
TITLE- Determination of the Anisotropyl:Ln the Mi-crohardness of
Beryllium Crystals
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vo,l 9, Nr 2,
pp 274 - 278 (USSR)
ABSTRACT: The aim of the present work was to study the anisotropy
in the microhardness of a single crystal of beryllium.
The study was made on 99.4c,113 pure monocrystalline
beryllium. The crystallization was carried out at
10-6 tmn Hg in the apparatus shown schematically in
Figure 1, in which I is a beryllium oxide crucible
which has a hemispherical bottom and conical side walls,
2 is the crucible cover, 3, 4, 5 and 6 are electrical
heaters, 7 is a jacket, 8 and 9 are screens, 10 is
a support, 11, 12, 13 are apertures for thermocoupleb
and 14, 15, 16, 17 and 18 are leads for the electrical
heaters. The temperature of 0the molten materialwas
brought up to 1 400 OC (120 C above the melting point
of beryllium). It was held at that temperature for about
Cardl/3 one hour and then uniformly cooled from the bottom upwards.
LK

6V,30
s/i26/6o/oo9/02/0l9/033
EO
:'_gfi@EA14ss
Determination of the Anisotropy in the Mic r ne of Beryllium
Crystals
The crystallized beryllium was then removed from the
apparatus after being cooled down to room temperature.
The specimens were worked into a spherical form and
suitably polished and the microhardness was determined at
the points indicated in Figure 21 (circles). The specimens
were orientated with the aid of X-ray diffraction photo-
graphs which wore also used to judge the quality of the
specimens. The inicroliardness was then measured using
the PMT-2 microhardness gauge with a load of 100 g.
Typical polar diagrams are shown in Figures 4 and 5 which
refer to the plane containing C6 and the plane
perpendicular to C 6 , respectively. It is concluded that
the microhardness diagram for berylliua-, is close to an
rati
ellLipsoid of revolution about the sixfold axis, the
Card 2/3

U "@i' I- ,
S/l@:6/6o/ooq/o2/olq/o33
EOA2@5@14s
Determination of the Anisotropy in the Micro a es of Beryllium
Crystals
of the axes of the ellipsoid being 0.62 (217 lfg/mm 21 and
350 kg/mm 2 perpendicular and along the C 6 axis).
There are 5 figures, 1 table and 3 references, I of
which is German, I Soviet and 1 English.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR
(Physico-technical Institute of the Ac - Ukrninian-SSR)
SUBMITTED: April 2, 1959
Card 3/3

-GARBER, R.I.; POLTAKOV, L.M.
Distribution of residual s%resaes in plastically deformed rock salt
crystals. Piz. met. i metallaved. 10 no.3:462-471 S 16o.
(MIRA 13:10)
1. Fiziko-tekhnicheski7 institut All USSR.
(Rock salt) (Dislocations in crystals)

85044
23t)q, 2109 v_,@,
S/126/60/010/004/014/023
EO21/E4o6
AUTHORS: Garber, R.I., Polyakov, L.M. and Malik, G.N.
4
TITLE.- ki Welding of C-0-p1per by Exposure to-Sonic ViVrations
V
PERIODICAL: Fizika metallov i mltallovedeniye, 196o, Vol.lo, @01P.4'
pp-590-596
TEXT: Investigations were carried out using an oscillator,
a magnetostriction device, an arrangement for loading and a vacuum
chamber. The apparatus is shown in Fig.l. The specimens were
simultaneously loaded with static and dynam3.c_ ressures. The
experimentswere carried out in a vacuum of 10 9 mm mercury. The
influence of the applied pressure, the temperature, the time and
regime of vibrations on the strength of the joint were investigated.
The samples were heated by a molybdenum heater and shields of thin
sheets of stainless steel. The samples were prepared from
oxygen-free copper in the form of a disc, 16 mm in diameter and
10 nun high (Fig.2). The strength of the joints was tested on an
14M-4P (IM-4R) machine. The optimum time of exposure to sonic
vibrations in order to produce the strongest joint is 20 to
30 seconds at 825*C and a.pressure of 1-5 kg/mm2 (curve 1, Fig.3)
and 2 to 3 minutes at 700 C and a pressure of 2.5 kg/mm2 (curve 1,
Card 1/3

85044
S/126/6o/o1o/oo4/o14/023
E021/E4o6
Welding of Copper by Exposure to Sonic Vibrations
Fig.4). The curves were obtained after a ten minute heat
treatment after the sonic treatment at the same temperature.
Curves 2 in Figs.3 and 4 show the strength of joint without the
sonic vibrations. To obtain joints of similar strength to those
obtained with vibrations, the pressure has to be maintained for one
hour at 825*C or three hours at 700*C without the application of
vibrations. Thus the time is considerably reduced by the use of
the vibrations. Fig.6 shows the microstructure of a specimen
after 4 minutes application of vibrations at 6oo*c (the optimum time
for this temperature). The grain size is 3 to 4 times smaller than
that of the original material. The strength of this sample was
19 kglmm2. After 20 minutes vibration, the grain size becomes
coarser and cracks begin to develop (Figs.7,8). The strength fell
to 14 to 15 kg/mm2. Fig.9 shows a sample after 10 minutes
vibration at 8250C. Cracks have developed in the grain boundaries
of the coarse grains. Fig.10 shows the relation between the
strength of the joint and static pressure at 600*C, Curve I is
after 4 minutes vibration treatment, curve 2 after 10 minutes and
curve 3 after 3 minutes treatment without vibrations. It can be
Card 2/3

8
S/126/60/0107040/014/023
E021/E4o6
Welding of Copper by Exposure to Sonic Vibrations
seen that with vibrations the static pressure can be considerably
reduced to obtain the same strength. The use of vibrations also
enables joints to be obtained with low values of plastic deformation
of the samples. There are 11 figures and 8 references: 6 Soviet,
1 German and 1 English.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR
(Physics and Engineering Institute AS UkrSSR)
SUBMITTEDs February 29, 196o
Card 3/3

S/l26/6o/oio/oo6/O2O/O22
E201/E491
AUTHORS: Garber-,w--R,..,j@, and Soloshenko, I,I,
TITLE: The Dependence of the Damping Decrement on the
Amplitude of Elastic VibvationA and the Plastic
Deformation of Overstressed Micro-Regions
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol,10, No,6,
pp-934-937
TEXT: The authors show that changes of the damping decrement (b)
indicate that hardening of crystals by plastic deformation at large
vibration amplitudes (a) does not preclude hardening at small
vibration amplitudes. For each effective stress (a) there is a
set of weak points which can be cured by plastic@ deformation. To
verify these theoretical conclusions, the damping decrement was
measured at various values of N (the total number of vibrations)
and 0 for rocksalt monocrystals and polycrystalline plates of
commercial lead. All measurements were carrted out at I cls at
room temperature. The results for rocksalt (Fig.1 and 2) and
lead (Fig.3), plotted in the form of 6(N) zurves at various values
of a, confirmed the conclusions arrived at theoretically, There
Card 1/2

S/126/60/010/006/020/022
E201/E491
The Dependence of the Damping Decrement on the Amplitude of
Elastic Vibrations and the Plastic Deformation of Overstressed
Micro-Regions
are 3 figures and 6 references: 5 Soviet and I non-Soviet,
ASSOCIATION: Kharlkovskiy gosudarstvennyy pedagogicheskiy Institut
fizicheskogo vospitaniya im. G,S,Skovorody
(Kharlkov State Pedagogical Institute for Physical
Training imeni G.S,Skovoroda)
SUBMITTED: June 7, 1960
Card 2/2
i Tr __ @_M

If
24M, ISO) S/05 60/070/01/002/007
AUTHORS: Garber, R. I., Gindin, 1. A. B006Y3017
TITLE: The Physics of th a Strength of Crystal Bodies
PERIODICAL: Uspekhi fizicheskikh nauk, 1960, Vol 70, Nr 1, PP 57-110 (USSR)
ABSTRICT: Although modern engineering makes ever increasing demands on
the strength of materials there exists no modern physical
theory of strength. The present paper gives a survey on the
up-to-date physical concepts on the strength of crystalline
bodies, the reasons for the low strength of the real materials ,
and the most important poosibilites of raising them. Part 1 deals
with the microscopic theory; of strength, especially with the
theory by Ya. I. Frenkell; Frankel' proved that the critical
shear stress in the case of which the lattice becomes unstable
is equal to G/2n wh ere G denotes the modulug of rigidit ; this
value is much higher than that for plastic crystals (10-@G).
By more accurate investigations other authors obtained a still
theoretical value of G130 which is much higher than that measur-
ed in single metal crystals. The reasons for this discrepancy
are briefly discussed. Part 2 deals with. the atructural defects
,of a real crystal and gives a short survey. Part 3 deals
Card 1/3 somewhat more in detail with the influences of the microcraoks

The Physics of the Strength of Crystal S/053/60/070/01/002/007
Bodies B006/BO17
Card 2/3
(P. 1. Rebinderl Ya. I. Frenkell, B. Ya. Pines, A. F. Ioffe,
S. N. Zhurkov, A* V. Stepan.,v; experiments and their results
are mentioned). Part 4 reports on the scale effect and the
strength of the thread-like crystals (A. P. Aleksandrov, S. N.
Zhurkov - statistical theory, Re I. Garber - experiments vith
calcite crystals; figures 3-9 show different characteria6ics
of strength, also Bartenov and Chepkov are mentioned). Part 5
gives a short survey on the statistical theory by N. N. Daviden-
kov, Ya. I. Frenkell and T. A. Kontorova, and part 6 deals
with the origin of cracks in the crystal nucleus (thaory by
A. V. Stepanov and its verification by He N. Davidenkov, Yee M.
Shevandin, and Me V. Klaason-Hoklyudova; experiments and their
results obtained by S. 0. Tsobkallo, Stepanovj S, N. Zhurkovj
T. P. Sanfirova et al). Part 7 presents the theoretical and
experimental investigation results of dislocations and micro-
crack~ (Yee D. Shohukin and V. I. Likhtman). Part 8 investigates
the influence of the surrounding medium on the mechanical
strength of solids (solution of the body and extension of aur-
face defects and adsorptionj A. F. loffe, P. k. Rebinderp
D. I. Shillkrug). 'Part 9 deals with the dependence of stringth

The PkYsics of the Strength of Crystal Bodies S/053/60/070/01/002/007
B006/BO17
(I.V.
on temperature and time
Obraimov, S. No Zhurkov, Be Ya.
Pines, I. Ya. Dekhtyar, To Po Senfirovs, and K. A. Osipov).
Part 10i destruction on creeping, part 11i cold brittleness
(theory by loffe for rook-salij experiments by No Me Davidankov
and To No Chuohman; miaroviruoture photographs by Garber, Gindin,
Konstantinovskiy, St arodubov). Part 12: discussion of the struo-
ture of high-sirength alloys (Go Vo Kurdyumov, Be Me Rovinakiyj
L. Me Bybakovat Be Me Revinskiy# Parkas, and Khondras, V. A.
Illinal V. X. Kritskaya Grusin Tyutyunik, Entin, V. I.
Startsev, P. N. Aronova@. Part ;3 and 14 are devoted to fatigue
and hardeningl the two types of hardening are briefly discussed
according to R. I. Garber. In conclusion it is then pointed
out that the strong difference between theoretical and experi-
mental strength in due to atruatural defects and that strength
could be increased by a regular stress distribution in thermal
and mechanical processing. There are 38 figures and 223
referenotep 108 of which are Soviet.
Card 3/3

GARBER, R.I.; SOLOSH-ENKO, I.I.
Effect of annealing on the decrease in the damping of an alternating
elastic-plastic flexure. Fiz. met. i metalloved. 12 no.1:153-155
J1 161. (MIRA 14:8)
1. Kharlkovskiy pedagogicheskiv institut imeni G.S.Skovorod -Y*
(Metal crystal@) (Deformations (Mechanics))

S/181/61/003/001/021/042
B006/BO56
AUTHORS: Gar@er, R. I. and Gindin, I. A.
TITLE: Elastic deformation and thermal expansion
PERIODICAL: Fizika tverdogo tela, v- 3, no. 1, 1961, 176-177
TEXT: When investigating deformations with temperature changes, thermal
expansion is usually considered to be independent of deformation; the ex-
planation of certain effects occurring in the temperature change of elasti-
cally deformed specimens, however, requires consideration of the stress
dependence on the coefficient of thermal expansion. This may be done by
taking third-order terms into account in the series expansion of the energy
of elasticity. Whereas this is not possible in general, not only the
required stress dependence of the expansion coefficient may be determined,
but also the coefficients entering into the latter may be estimated for the
special case of uniaxial deformation or uniform expansion in all directions.
This is done in the present work. For a diatomic solid, the stress
G' = -ft +gE2 (1), where E is the relative deformation, and f and g
are constants. If E is considered the sum of shifts due to applied
Card 1/3

S/181/61/003/001/021/042
Elastic deformation and thermal expansion B006/BO56
forces (W and to thermal vibrations then V. Vl+@2gLl-f) 2
(Y' 11 C2+gC2*
Averaging over time gives and L2 = g(21( f-2g@). L 2maybe determined
2 2
from the mean density of the energy of elasticity of thermal vibrations:
T
C
wa= V dT, and TI = -ft 2/2 + gj3/3. By taking into account that L3
V 2 2 r 2
0 sume that jCV
small quantity changing its sign, one may as V dT =- ft'2/2.
T
If E2 oLdT, where OL is the coefficient of thermal expansion,oneobtains
= 2gC,/Vf(2gF_l-f). With 6'1=0, tl=O, -2gCV /Vf2'
L 0 one obtains
C
0(. - Cko (1+PF'j). On the other hand, it follows from the GrUneisen relation
that oko - KC vt/P, where K denotes compressibility, the GrUnelsen
coefficient, V the atomic volume. Thus, one obtains -Kff/3. From (1)
Card 2/3

S/18i 61100310011021104 2
X
Elastic deformation and thermal expansion B006
B,056
it follows that f=-E, where E is the modulus of linear elasticity. The
value of P was calculated for several metals:
Metal
Small deformations naturally lead to Pd 1.3
comparatively low changes in the coefficient Ag 1.65
of thermal expansion; in the case of high Pt 1.65
stress gradients, the change may become Cu 1.7
considerable and cause noticeable effects. ck-Fe 1.9
There are 1 table and 1 Soviet-bloc Ni 2.1
reference. W 2.1
Co 2.3
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR Kharlkov (Institute
of Physics and Technology AS Ukr SSR, Khar1kov)
SUBMITTED: June 6, 1960
Card 3/3

GARWER., R.I.; STEPINA, Ye. 1.
Defects on the boundaries of twin interlayers. Fiz. tver. tela. 3
no.2:514-519 F t6l. (MIRA 14:6)
Is Fiziko-tekhnicheskiy institut AN USSR, Kharlkov.
(Crystals-Defects)

20798
s/181./61/003/003/024/030
B102/B205
AUTHORS: Garber,. R. I., Gindin, I. A., and Shubin, Yu. V.
TITLE: High strength of single crystals
PERIODICAL: Fizika tverdogo tela. v. 3, no. 3, 1,161, 918-910
TEXT; Numerous experimental studies of crystals of rock salt and other sub-
stances, performed by A. F. Ioffe and A. V. Stepanov, seem to indicate that
the continuity of the crystals is disturbed in plastic deformation. By
retarding or accelerating the plastic deformation of rock crystal, Stepanov
was able to change their strength by a factor of 30. The highest strength
is displayed by filament crystals if the entire process of deformation up
to destruction is plastic. Iron filaments elastically deformed by 4,8@d, for
example, reach a strength of 1340 k&@jm2. When tbe "irst indications of s I idin a
are noticeable, the resistance of filament crystals to resistance decreases
rapidly. If the orientation of a macroscopic crystal toward the external
force is such that plastic deformation (chiefly sliding and @winninG) is
excluded, increased strength can be expected. Hexagonal. crystals which have
a limited number of slip and twinning planes at low temperatures, are partic-
Card 1/ 3

High strength
26798
s/181/61/003/003/024/030
B102/B205
ularly suitable for such experiments. Plastic deformation of these crystals
is effecte4 chiefly by sliding in the basal plane (0001), Oil tile faces of
prisms of first order @10TOJ, and by twinning in the planes @10i2j . This
was studied with the hell) of prismatic Be single crystals (1 .6 $ 1.5 X 3 mm)
of 99.9;,j' purity. The crystals were compressed at 770K by a force perpendic.-
ularly acting on tile basal plane (deformation rate: 0.01 3i'olsec) . There
were no indications of plastic deformation up to destruction. Sliuing and
twinning were impossible since no components of this foice were act.'.iq; in
the respective direotions. Under these conditions, the Be single crystals
actually showed a very high strength: destruction occurred only under a
pressure of 410 kg/mm2; the crystal suddenly decomposed into very fine
powder. With other positions of the basal plane, destruction occurred
alread at 34 kg/MM2. At room temperature, the maximum. stress is only
210 kg@=2 (perpendicular to the basal plane). Similar experiments were
carried out with calcite single crystals (6 x 4 x 10 mm) at 3000K, which are
deformed only by twinning. The orientation of the sin.-le crystals was such
that the twimning plane (110) formed an angle of 450 with the axis of the
specimen and the direction of displacement 10011 , opposite to the direction
in which the tangential stresses acted, wkich deformed the spenimer. at a
Card 2/3

20798
High strenE;th ...
S/181/6!/CC-,z/003/024/030
B102/B205
rate of 0.004',,)/sec. A strenc,,th of 23 kg/mm2was attained in this case. Th e
L
lower bound is 40 9/mn,2. There are 7 references: ij Soviet-bloc rLrd 3 non-
Soviet-bloc.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR KharIkov (institute of
Physics and TechnoloCy, AS UkrSSR, Kliarlkov)
SUBMITTED; August 10, 1960
Card 3/3

pi -I Soo
22051
S/181//61/003/004/017/030
B102/B214 -
AUTHORS: Garber, R. I., Gindin, I. A., and Shubin, Yu. V.
TITLE: Orientation dependence of the slipping and rupture of
0
single crystals of beryllium on stretching
PERIODICAL: Fizika tverdogo tela, v. 3, no. 4, 1961, 1144-1151
TEXT: The present paper, which is in continuation of earlier investiga-
tions, makes a contribution to the clarification of the structural rules
of beryllium which is highly anisotropic with respect to its mechanical
properties. The single crystals studiea were bred from a 99.98% pure
starting materialq using the method of slow cooling of the melt (crystalliza-
tion rate; 5 mm/hr). Single crystals of 80 mm length and 60 mm diameter
were obtained. The orientation was determined by X-rays. The crystals
were cut in different forms by a special e1ectro-spark device, after
which they were etched, ground, and polished, first chemically and then
mechanically. The tensile tests were made at the followin 9 angles to
the basal plane: a = Ot 5, 10, 15, 20# 016, 459 70, and 90 (see Fig. 2).
The shearing direction 111701 coincided with one of the lateral faces.
Card 1

2205,
s/iai/6i/'003/004/O17/03O
Orientation dependence ... B102/B214
The stretching was done at a conotant rate of 0-005';'of/sec at room
temperature. The crystallographic elements of plasticity and rupture were
studied by crystallographic and microinterference methods. The results
of the investigations are illustrated in Figs. 3 and 4. The curve P9
(Fig. 3) shows the a-dependence of tile ultimate strength. The strongly
non-monotonic behavior of this curve contradicts the law of constancy of
normal stress on brittle rupture. The curve P 26 is drawn according to
this law and does not represent the experimental facts in any way.
The experimental curve P 8 (a) can be described well by the equation
3 -1/2 0 2
P16 @ K(sin acosa) in the an&ular range a 20-70 , where K = 3 k91mm
2
This equation corresponds to the law K. However, the
experimental results do not correspond to this law between 0 and 15
At a > 200 slippin and rupture occur in tile same system of planes, namely,
(0001)9 At a < 20 the crystallographic elements of plasticity and
rupture alter and do not coincide (slipping: @'IOTO@- rupture:
Further, investigations of the st-ructure were made before and a ter the
Card 2/5

22051
S/181/61/003/004/017/030
Orientation dependence ... B102/B214
rupture. The following conclusions are drawn from the results obtained:
Highly pure Be single crystals and commercially pure crystals show marked
anisotropy in their -mechanical properties as well as in the elements of
plasticity and rupture on stretching. There is an orientation limit
which is characterized by the plasticity at room temperature. The peculi-
arity of rupture at this orientation is the absence of ideal cleavability
land a-complicated character of the fracture. Improved plastic properties
of polycrystalline Be are obtained by preparing a definite fine-grained
texture for which, in the process of deformation, the cleavage in the
principal planes of rupture is strongly localized. There are 7 figures
and 14 references: 4 Soviet-bloc.
.ASSOCIATION: Piziko-tekhnicheskiy institut AN USSR Khartkov (Institute
of Physics and Technology, AS UkrSSR, Khar1kov)
SUBMITTED: August 1, 1960
Card-3/5

34h29
S/185/61/006/006/006/030
D299/D304
AUTHORS: ITarberp RoIo, and Kyrylov, V.S.
TITLE: Spectral distribution of optical density of plasti-
cally deformed rock-salt crystals
PERIODICAL: Ukrayinslkyy fizychnyy zhurnall ve 6, no. 6. 1961,
755 - 757
TEXTZ The dependence of the intensity of light scattering on wave-
length in plastically deformed crystals can be determined by opti-
cal-density measurements; thereby the spectrometer C@ -4 (SF-4) was
used. The natural rock-salt crystals were annealed at 650 - 7000C
and tempered. The optical-density distribution was measured on spe-
cimens with a small amount of impurities. Four specimens were mea-
sured simultaneously. One of the specimens (which had highest trans-
mittance), was Aected as a standard and not subjected to deforma-
tion. whereas the other 3 specimens were plastically deformed. Then
the optical density was measured with respect to the standard cry-
Btal. The results of one of the measurement cycles are shown in a
Card 1/3

S/185/61/006/000-/006/070
Spectral distribution of optical D299/D304
figure, where the values of IgD + C (D being the optical density
and C .--- an arbitrary constant) are plotted on the ordinatel and
lgtt(/t beino the wavelength of the incident light) is plotted on
C@
the abscissa. The investigations were carried out for the spectral
region 3800 - 6000 A. The graphs shown are typical for the investi-
gated NaCl crystals. The slope of the straight line 8(lg D)/O(lg;L)
is greater for the deformed crystalsq and depends on the size of
the scattering particles (inhomogeneities). The increase in the
slope is proof of diminishing size of the mosaic blocks. In real
crystalsq although they were especially selected, and annealed and
studied under the same conditions, the development of plastic de-
formation is not entirely similar; thus, in 2 of the investigated
specimens, the slope changed at a stress value of 150 / 2 pro-
/Mj mm ap
ximatelyj whereas in the third specimen - at 350 9 only. Work-
ing formulas for a quantitative estimate of the size of the scatte-
rers and their concentration, as a function of optical density, are
not available as yet. It is emphasized that the chan6e in the slope
starte only at deformation stresses which correspond to the appear-
ance of diffuse scattering (Tyndall's cone) inside the crystal, The
Card 2/3

S/185/61/006/'006/006/030
Spectral distribution of optical ... D299/D304
conducted measurements show that it is possible to study the sub-
microstructure of trans,'@,z_ent. solids in the curly sta,-es of plastic
deforix-tion. There ,-;re 1 -fi,-ure and 5 references: '.' 6ovi_ct-bloc mi@,
2 non-Soviet-bloc. The references to the TE'nt.,-,1ish-1anC;uaL,,-e publica-
tions read as follows: S.P.F. 11umphrys-G-;,w_m, Proc. Phys. Soc., B68,
no- 6, j25, 1955; R. FtIrth, Phil. Mag., 40, 1227, 1949z
ASSOCIATION: Umanslkyy pedahohichnyy instytut (Uznan Peiagogical
Institute)
Card 3/3

89543

S/126/61/011/001/010/019 ti
E193/E483
AUTHORS: Garber, R.I., Neklyudov, I.M. and Perunina,--L.M.
TITLE: Vork-Hardenin Bismuth Under Conditions of
Programmed Loading
PERIODICAL: Fizika metallov i metallovedeniye, 1961, @ol.11' No.1,
pp.10-i14
TEXT: Increasing the rate of deformation, or lowering the
temperature, brings about an increase in the work-hardening
exponent; this effect is attributed to the fact that under these
conditions duration of the relaxation process during deforination
decreases. At relatively higher temperatures, the work-hardening
exponent decreases owing to increased intensity of relaxation.
However, it has beer. shown by Bol'shanina (Ref.1) that the yield
PoInt of iwinned calcite increases five times after annealing,
while Garber et al (Ref.3) have found that the yield point of iron,
twinned at the temperature of liquid helium, also rapidly increases.
during.subsequent heating to room temperature. The object of the
present investigation was to elucidate the mechanism of these
effects by studying work-hardening of bismuth. Since twinning in
Car.d.-I/.1.0--

89943
S/126/61/oll/oovoio/oig
7
E193/E483
Work-Hardening of Bismuth Under Conditions-of-Programmed Loading
the predominant mechanism of plastic deformation of this metal,
it was assumed that its mechanicai properties would be similar to
those of twins in calcite and iron. Refined bismuth was used
for the preparation of the experimental test pieces, made by the
Bridgeman method, in the form of rods (180 mm long, 5 mm in
diameter) with spherical ends, and subsequently vacuum-annealed
at 2000C for 3 h. The experiments consisted in straining the test!
pieces in tension at room temperature under controlled conditions.
The tensile force was applied by means of weight, hung at the lower!
end of the specimen, the usual precautions having been taken to
ensure axial loading. The load was increased in a pre-determined
ifashion by means of an automatic dispenser from which small balls
dropped at regular intervals into a container which constituted the!
loading weight. -Each load increment did not exceed
6 x 1.0-3 S/MM2, and.the 'average rate of loading was maintained
constant throughout each experiment, the rates applied varying
between 2 and 10 g/MM2/h. It was found in the course of experiments
that it was possible to select a certain critical rate of loading
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E193/E483
-JWork-Hardening of Bismuth Under Conditions of Programmed Loading
Ok at which the rate of deformation c remained constant within
a wide interval of applied stress. This can be seen in Fig.2, 2
where elongation C (lo3%, left-hand scale) and stress a (g/mm
rigl@t-hand scale) are plotted'againat time t (hours). To make
:sure that the test piece had, in fact, undergone plastic
:deformation, c was measured while the load was graaually removed
The results (broken curves in Fig.2) show that although some elast q
recovery had taken place, more than a half of the elongation,
attained at the end of the loading cycle, was due to plastic
deformation. Fig.3 shows two q(O.curves, constructed for two
"identical specimens, loaded at a < Ok, the upper and lower
;graphs relating to specimens loaded at 2.3 and 4.5 g/MM2/h,
respectively. It will be seen that in both cases, the work-
:hardening exponents
ba/bc remained constant. The results of
the next series of experiments are reproduced in Fig,4, where
elongation c N, left-hand scale) and stress a (g MM2, right- I
hand scale) are plotted against time t -(hours). Graph 1, O(t) I
iand 2, cCt) relate to a specimen tested in the following way:
Card 3/ 10

S/126/61/011/001/010/019'
E.1-93/E483
Work-Hardening of Bismuth*Under Conditions of.Programmed Loading i@
the load was applied at a rate 6 = 8 g/mm2/h until a certain am
,was reached at which the c(t) relationship ceased to be linear;
.beginning from this moment, the load was maintained constant at aml
for 24 h during which time the test piec 'e continued to deform
,owing to creep; the rate of creep during this period remained
constant and was practically the same as the rate of strain during
the preceding period. For comparison, Fig.4 shows a creep curve
(graph 3) of another specimen which has been loaded to 'am in
20 min. It will be seen that in this case the total deformation
was higher than that of the test piuce:: strained tinder slow rate of
loading, and that the rate of creep under this constant stress am
was also considerably higher. The interesting fact is that in
the case of specimens, work-hardened during deformation at slow rate:
of loading and then re-loaded at a fast rate to am, the rate of
creep decreased 2 to 3 times(see right-hand branch of graph 2, FigAL
It was also found that test pieces, work-hardened by deformation at i
slow loading rates, did not lose their strength after ageing (with
the load taken off) at room temperature. The results described
above confirm the hypothesis put forward by Garber (Ref.4),'
.Card 4/10

69943
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E193/E483
Work-Hardening of Bismuth Under Conditions of Programmed Loading
according to whom the observed effects are due to diffusion
strengthening of twins which is brought about by aggregation of
t the twin boundaries.- In cases
vacancies and impurity atoms a
when twins do not traverse the cross-section of the test piece,
diffusion strengthening may inhibit further growth of the twins
even at relatively high loads. It was for this reason that no
traces of twins were observed on the surface of the test pieces
ed in the experiments described above and that deformation took
u
s
place under conditions of equilibrium, as indicated by the absence 1;
of discontinuities on the c(t) curves. 'Different results were
obtained when a test piece in the form of a single crystal, 1.2 mm
in diameter, was used. This is illustrated by grap@s in Fig-5,
Where At (microns, left-hand scale) and a (g, right-hand scale)
are plotted against time t (hours). Sudden jumps on the A&W,
curve for a test piece under load which increased at a constant
t work-hardening, caused by diffusion-induced
rate indicate tha
enrichment of the twin boundaries in vacancies and impurity atoms,
cannot prevent the formation and growth of twins in a specimen of
Card 5/10

89943
s/i26/61/oil/ool/olo/oi9
E193/E483
Work-Hardening of Bismuth Under Conditions of,Programmed Loading
this size. In the case of high quality single crystals of small
cross-section area, a twin nucleus (e.g. an elastic twin) can
rapidly change into a twin intersecting the cross-section of the
speci6ien, as a result of which deformation of the specimen
proceeds in jumps, since the resistance to deformation (by twinning).
at the moment of the formation of a twin decreases several times.
The 6 9(t) and o(t) curves for such a specimen (a single crystal 1
with the gauge length of 150 mm and rectangular cross-section
x 2.5 min) are shown in Fig.6. In spite of very slow rate of
3
loading employed, it was found impossible to obtain gradual
deformation (i.e. smooth 69(t) curves) of the specimens, on the i
surface of which evidence of twins, intersecting the cross-section,
'was found after completion of the loading cycle. That these
.effects were observed in a rectangular.specimen can be attributed
:to non-uniform distribution of stresses over its cross-section and
,to the high quality and homogeneity of its crystal structure.
Finally, in order to elucidate the nature of the processes leading
to work-hardening of specimens deformed at slow and fast rates of
Card 6/10

F
j:
S/l26/6i/on/ooi/oio/ol9
E193/9483
Ifork-flardening of Bisinuth Uncker Conditions of programmed Loading
loading,-X-ray diffraction patterns of test pieces, loaded to the
Isame am (yield point) but at different rates of loading (8 and
1080 g/mm2/h), were obtained. -The pattern obtained for the
slowly loaded specimen hardly differed from that obtained for'an
undeformed material, wl@ereas.a very different pattern was obtained
on the specimen deformed at a fast rate of loading. This
indicated that work-hardening under normal conditions of loading
(within the elastic region) is associated with fragmentation.,of
the crystal, whereas all other factors being equal, deformation
under. conditions of slow rates of loading does not affect the
crystal structure or affects it only in the regions of lowest
strength which constitute a minute fraction of the total volume of
the crystal. Acknowledgments are made to I.M.Fishman and
S.T.Shavlo, who participated in this work. There are 9 figures
and 11 Soviet references.
ASSOCIATION:
Card 7/10
Fiziko-takhnicheskiy institut AN UkrSSR
(The Physicotechnical Institute AS UkrSSR)

89943
S/126/61/011/001/010/0
19
E193/E483
Work-Hardening-of Bismuth Und' ading
or Conditions of Programmed Lo.
SUBMITTED: May 25, 1960
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Fig.2. Fig-3.
:-Card
-7-

S/12 6/61/011/001/010/019
E193/E483
'Ifork-Hardening of Bismuth Under Conditions of Programmed Loading
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69943
s/i26/6i/oii/ooi/oio/oiq
E193/E483
Ifork-Hardening of Bismuth Under Conditions of Programmed Loading
11 7j
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Card 10/10

22964
S/126/61/011/005/009/015
E193/E183
AUTHORS; and Polyakov. L.M.
TITLEt Investigation of the process of sintering metals.
Ii.
PERIODICAL; Fizika metallov i metallovedeniye, Vol.11, No.5, iq6i,
pp. 730-740.
TEXTt Part I of this paper was published in the Ukr.Fiz.Zh.,
1956, Vol.l@ 88.
The process studied by the present authors consisted in butt-
joining two flat, ring-shaped aluminium specimens by simultaneous
application of heat and pressure and constituted, in fact, preasure@
welding. The object of the present investigation was to study the
relationship between the strength of joints, produced by this
method, and the pressure employed, temperature, and duration of the
process. In addition, the variation of the microstructure near the
joint interface was studied, and the temperature dependence of
hardness of aluminium was determined. To minimise the effect of
oxide films and gases absorbed on the metal surface all
experiments were carried out in vacuum of 10-5 to 1;-6 mm Hg.
Card 1/6

22964
S/126/61/011/005/0091'015
E193/E183
Investigation of the process of sintering metals. II.
Immediately before each experiment, the surfaces to be joined were
cleaned with a steel brush after which the surface roughness was
0.5-1.5 4. The two rings were then assembled in a specially
designed press, the whole was placed in the vacuum changer, the
temperature of the aluminium rings was raised to 600 OC and kept
constant for 15-20 minutes, after which they were cooled to the OX
test temperature and the appropriate load applied. The strength
of the joint was determined on a tensile testing machine. The
results are reproduced graphically. In Fig.4, U.T.S. (ap, kg/mm2)
of the joint obtained under 'pressure P c 0.32 kg/mm2, is plotted
against the sintering time (T, minutes), curves .1-4 relating to
sintering at 450, 500, 550 and 600 OC respectively. A similar set
of curves, constructed for joints obtained under p = 2 kg/mm2,
in reproduced in Fig.5. In Fig.6, ap is plotted against p
(kg/mm2), curves 1-6 relating to joints obtained at 300, 400, 450,
500, 550 and 60o OC respectively. It was inferred from these
results that the process studied takes place in two stages. The
first stage consists in the formation of metallic bond between the
Card 2/ 6

2L'964
S/126/61/011/005/009/015
E193/EI83
Investigation pf the process of aintering metals, li.
clean surfaces brought into intimate contact by the action of the
applied pressure. The strength of the resultant joint is deter-
mined mainly by the conditions obtaining during this initial stage,
It is pointed out here that for the joint to be formed, it is not
only necessary to bring the two mating surfaces within a distance
equal to the lattice parameter of the metal, but a re-grouping of
the atoms has also to take place in order to create conditions
favourable for the formation of the metallic bond. The activation
energy for the re-grouping of atoms in aluminium has been found to
be 6.4 kcal/mol. In the second stage of the process, in which
diffusion plays the predominant part, the areas of contact
established during the first stage increase as a result oft
(1) movement of vacancies to the boundaries of the welded regions;
(2) coalescence of the excess vacancies and formation of large
pores due to dissolution of small poresi and (3) dissolution of
large pores. The effect of the second stage of the process on the
strength of the resultant joints becomes significant only at high
temperatures and after a prolonged sintering,
Card 3/ 6

22964
S/126/6 1/011/005/009/015
Investigation of the process of E193/E-183
There are 10 figures and 16 referencesi 8 Soviet and 8 non-Soviet.
The English language reference readsi
Ref.7j G.J. Finch and R.T. Spurr, Physics of Lubrication,
Supploment, 1951, No.l.
ASSOCIATIONi Fiziko-tekhnicheskiy institut AN USSR g. Khar"kov
(Physlco-technical Institute, AS Ukr.SSR, Kharikov)
SUBMITTED: August 159 196o
Card 4/6

24477
S/126/61/011/006/003/011
2.10 ID E193/E483
AUTHORS. Garber, R.I., Zalivadnyy, S.Ya. and Mikhaylovskiy, V.M.
T1TLE: Variation of the microstructure of uranium during cyclic
thermal treatment. II
PERIODICAL: Fizika metallov i metallovedenive, 1961, Vol.11, No.6,
pp.889-892
TEXT: This is a continuation of earlier published work of the
authors (Ref.l: FTT, 196o, 2, 6, 1052 and Ref.2: M,1, 1959, 8, 9W
relating to the mechanism of distortion of uranium during thermal
cycling on bi-crystal specimens and on coarsely crystalline
material with columnar grains. In this paper the authors
investigate the laws governing the thermal cycling-induced changes
in finely-crystalline technical grade uranium. To ensure uniform
grain-size of the required magnitude, cylindrical uranium specimens
(6C, mm long, 8 mm in diameter) were annealed and then compressed
(in the direction normal to the axis) to approximatelY 50%
reduction in thickness and the resultant blanks were machined to
produce prismatic specimens measuring 60 x 4 x 3 mm. After
recrystallization, these specimens were plastically deformed in
Card 1/5

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Variation of the inicrostructure ... E193/E483
compression (8% reduction in thickness) in the direction normal to
the longitudinal axis and to the direction of the first compressing
operation; this was done to develop texture in the material
studied. The specimens were then cut into several prismatic test
pieces which, after polishing (mechanical and electrolytic) and
recrystallization, measured 6 x 2.5 x 1.5 mm. On 3 faces of each
test piece a set of lines, spaced at 0.1 mm intervals, was
inscribed by making scratches 211 wide and 0.511 deep. Annealing,
recrystallization and the thermal cycling tests were all carried out
in vacuum of 5 x 10-6 mm Hg. Each thermal cycle consisted of the
following: heating to 6000C in 5 minutes; holding at 6000C for
1 minute; cooling to 1000C in 4 minutes. The specimens (whose
original grain size was 2511) were examined after 200, 400, 600,
800, 1300 and 2000 cycles. The dimensional changes of several
test pieces after 600 cycles are tabulated. It will be seen that
the length of the test pieces increased, their width and thickness
decreased. Metallographic examination revealed that thermal
cycling had brought about both the deformation in the interior of
the grains and relative displacement of the grains. The latter
effect was reflected in increased roughness of the
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2hh77
s/i26/6i/oiiAT66/OO3/O11
Variation of the microstructure ... E193/E483
surface of the test pieces. This is illustrated in Fig-3 showing
(x200 and*x200 472 in the horizontal and vertical direction,
respectively) the contour of the surface of a specimen (a)-before
thermal cycling, (6) after 600 cycles and (a) after 2000 cycles.
The average grain-size of the specimens decreased from the initial
25 il - to 18 iL after 2000 cycles -The -rate-of increase in the
length of the -test pieces increased with the increasing number of
the cycles, 41/1 per 1 cycle after 2000 cycles being 2 to 3 times
larger than that after 600 cycles. After 2000 cycles the length
of the test pieces increased on the average by 60%; at the same
time the average increase in length of the grains was 20%. This
discrepancy was attributed to the effect of recrystallization taking
place during thermal cycling on the total elongation of the grains .
There are 5 figures, 1 -table and 4 Soviet references.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN UkrSSR
(Physico-technical Institutb AN UkrSSR)
SUB'MITTED: September 27, 1960
Card 3/5

30456
S/126/61/012/003/016/o2l
E193/E135
AUTHORS: Gindin, I.A., and Shubin, Yu.V.
TITLE: Tensile tests on beryllium single crystals in the
20-500 OC temperature range. V.
PERIODICAL: Fizika metallov i metallovedeniye, vol.12, no-3, 1961,
) 437-446
TEXT: Scarcity of data on the behaviour of beryllium single
crystals under tensile stresses prompted the present authors to
undertake the study of this subject. The experimental specimens
were prepared from 99.98% pure Be by a pulling-out technique.
The orientation of the single crystal tensile test pieces Is shown
in Fig.1, where p indicates the direction of the applied stress.
A strain rate of 0.005%/aec was used in the tensile tests carried
out at 20, 200, 400 and 500 OC, helium being employed as the
protective atmosphere at elevated temperatures. The mechanical
tests were supplemented by metallographic examination. The results
of the mechanical tests are reproduced graphically. In Fig.2, the
UTS and the yield point (Pb and ps, kg/mm2, left-hand scale)
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'Tensile tests on beryllium single ... S/126/61/012/003/Oi6/021
E193/EI35
and elongation and reduction of area (6 and (P , %, right-hand
scale) are plotted against the test temperature (OC). The fifth
curve shows the temperature-dependence of the so-called "diffusion
deformation" factor, X, which is given by X = (1 - y) 100 OC,
where y denotes the deformation localised in the slip on the
basal plane, its magnitude being calculated from
ni asi
where ni is the number of basal slip bands with the absolute slip
displacement of asi, and ( & f )a = &P cos 450 represents the
strain of the specimen in the direction of slip. Fig.2 shows the
true tensile stress/elongation curve for beryllium single crystals
at temperatures indicated by each curve. The effect of temperature
on the mode of slip is illustrated in Fig.4, showing (X 200) slip
lines on the faces of specimens extended (from left to right) at
20, 200 and 400 OC. The variation of the mode of slip with rising
temperature was also studied by determining the magnitude of the
Card 2/ 6,/

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Tensile tests on beryllium single .... S/126/61/012/003/016/021
El93/El35
relative slip, y, and density of the slip bands e, these two
parameters being given by y = b/a. and et= 1@h (for the
meaning of b/a. and h see Fig.1), In he regions of
uniformly distributed slip lines, y increased from 0.4 at 20 OC
@o 2.0 at 500 `C; in the region of macroscopically localised slip,
at 400 OC, y reached 70, The parameter e also initially
increased with temperature, reaching a maximum of 0.12 1/,p at
200 OC after which it decreased again, reaching at 400-500 OC a
value similar to that at room temperature (- 0.3 1/10. Analysis
of the results of mechanical tests, correlated with the
examination of slip bands and microstructure of specimens after
A.racture, led to the following conclusions. 1) Plasticity of Be
single crystals increases monotonically with rising temperature,
s)-towing no peak at 4oo OC which is a characteristic of
polycrystalline beryllium. The increase in plasticity in the
20-200 OC range is caused by the formation of new slip bands with
the material within the bands hardening at a sufficiently fast
rate. The increase in plasticity at higher temperatures is
associated with the onset of localised slip, characterised by a
Card 3/ 4',

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Tensile tests on beryllium single ... S/126/61/012/003/016/021
E193/E135
-large magnitude of y (about 70). Both UTS and the so-called
strain.-hardening_modulus D passed through a maximum at 200 OC;
U is given by D = (pu - p,)b, where pu is the true UTS of
the metal. This effect is a manifestation of the simultaneously
occurring prozesses of strain-hardening and relaxation.
2) Deformation of Be single crystals with an orientation as
illustrated in Fig.1 takes place mainly by slip along the basal
planes (0001) in the IllliO direction. At higher temperatures,
prismatic slip along the jlOlX3 plane in the general [11-i03
direction and diffusion deformation play an increasingly important
part. 3) Brittleness of Be single crystals at room temperature
is caused by non-uniform plastic deformation along the basal plane
which causes the formation and growth of cracks along the main
cleavage plane. At high temperatures, slip becomes more uniform
and deformation takes place partly by prismatic slip.
There are 10 figures, I table and 1 Soviet-bloc reference.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR
(Physicotechnical Institute, AS Ukr.SSR)
SUBMITTED: January 2, 1961
Card 4/@I

S/053/61/074/001/001/003
B11 7 /B212
AUTHORS: Garber, R. I., and Gindin, I. A.
TITLE: Physical properties of high-purity metals
PERIODICAL: Uspekhi fizicheskikh nauk, v. 74, no. 1, 1961, 31 - 6o
TEXT: The present survey deals with papers which have been published in
recent years in the field of high-purity metals. The papers show a trend
to obtain specimens of ever-increasing purity. They also show that the
progress made varies for different metals (appendix). The physical prob-
lems associated with such metals are discussed, for whose analysis the
purity of the specimens is decisive. These problems include the electrical
resistance, the reflectance of the metals, the magnetic permeability, nu-
clear reactions, effects of radioactive irradiation, grain boundaries,
latent energy of plastic deformation, relaxation, recrystallization, inter-
nal friction, moduli of elasticity,and mechanical properties. The latter
include the plasticity, deformation curve, cold-brittleness and creeping.
A .,,lance at the material available shows that great progress has been ma(!e
in the analysis of high-purity metals. The most urgent task at present
Card 1/ 3

S/053/61/074/001/001/003
Physical properties of ... B117/B212
seem to be to develop methods for industrial production of these metals.
So far, it has been impossible to solve the problem concerning the changes
of physical properties of metal effected by small additions. Regarding
the electrical resistance, the joint effect of local distortions by forei&.
atoms and other causes, such as vacancies etc., may be considercdto be
proved. The mechanical properties are very sensitive toward additions,
especially with respect to structural changes occurring during crystalliza-
tion or other thermal processes. Vacancies and local distortions seem to
play a minor role only. The brittleness of various metals can be eliminated
by purifying them from additions. A further development of new methods
for the separation of metals will find new fields of application for high-
purity metals. References to publications on high-purity metals are given
for the following elements: Al, Ba, Be, V, W, Bi, Ga, Ha, Fe, Au, In? CdY
Ka, Ko, Mg, Idn, Cu, h1o, Ni, Nb, Pt, Sn, Pb, Ag, Sr, Sb, Ta, Ti, Th, U, Cr,
Zn, and Zr. The following Soviet authors are mentioned: L. S. Kan, B. G.
Lazarev (Ref.l: DAN SSSR 81, 1027 (1951); V. B. Zernov, Yu. V. Sharvin
(Ref-7: ZhETF 6, 1038 (1T59); B. 11. Aleksandrov, B. I. Verkin (Ref.8:
ZhETF 34, 1655_%58); A. I. Sudovtsov, Ye. Ye. Semenenko (Ref.18: ZhETF
Card 2/ 3

S/053/61/074/001/001/003
Physical properties of BI 17 /13212
22, 305 (1958); 1. M. LiDshits, M. I. Kaganov (Ref.29: UFN 69, 419 (1959);
B. Leks (Ref-30: UPN 70,)11 (1960); A. S. Zaymovskiy, G. Ya. Sergeyev,
V.-V . Titova, B. M. Levitskiy, Yu. N. Sikurskiy (Ref.34: Atomnaya energiya
5-, 412 (1958); M. Ya. Gallperin, Ye. P. Kostyukova, B. M. Rovinskiy, Izv.
AN SSSR, ser. tekhn. A, 82 (1959); D. Ye. Ovsiyenko, Ye. I. Sosnina, (Ref.
60; Voprosy fiziki metallov i metallovedeniya, sb. no. 9, Kiyov (1959) str.
185); V. A. Pavlov (Ref.64: Fiz. metallov i metallovedeniyeA, 1 (1957);
V. A. Zhuravlev, (Ref-72: Zavodskaya laboratoriya a, 687 (1959); V- S-
Yemellyanov, A. I. Yevstyukhin, D. D. Abonin, V. I. Statsenko, ("Metallurgip
i metallovedeniye chistykh metallov" vyp. 1, 1959, 44). There are 18 fig-
ures, 7 tables, and 144 referencest 61 Soviet-bloc and 83 non-Soviet-bloc.
The six references to English-language publications read as follows: D. J.
Maykut, Prod. Engineering 21, 186 (1953) - (Ref-31); A. N. Holden, Phys.
Metal. of Uranium Massachus., 1958, str. 7 (Ref.33); J. C. Blade, Rev.
metallurgie @J, 769 (1957) (Ref-50); P. Gordon, J. Metals :L, 1043 (1955);
(Ref-51); C. Zener, Phys. Rev. 1j, 639 (1948) (Ref.68); T. R. Barrett,G. G.
Ellis, R. A. Knight, Proc. Sec. Int. Conf. Geneva 5, 319, 320 (1958) (Ref.
100).
Card V.,

KIRILLOV, V.S.
Change in the spectral distribution of optical density caused
by Ught scattering in plastic deformation of rock salt
crystals. I@ristallografiia 7 no.1:142-144 Ja-F 162. (KIRA 15:2)
1. Umanskiy gosudarstvennyy pedagogicheskiy institut.
(Rock salt-Optical properties)
I

GARBER, -R.I.; STEPINA, Ye.I.
DefecLs at stopping places of twins' boundaries. Kristalloprafiia
7 no.2:325-326 Mr-Ao '62. (MIRA 15:4)
1. Fiziko-tekhnicheskiy institut AN USSR.
(Crystals--Defects)

GARBER, R.I.; MOGILINIKOVA, T.T.
Determining the elasticity limit of real solids. Fiz. met. i
metalloved. 13 no.2:314-316 F 162. (MIRA 15-3)
1. Fiziko-tekhnicheskiy institut AN USSR.
(Solids) (Elasticity)

S/126/62/013/005/014/031
r-073/E535
AUTHORS: Garber. R.I. and Mogil I nikova, T.T.
TITJ_E: Internal friction and plastic deformation of over-
loaded micro-regions of a solid body. II
PERIODICAL: Fizika metallov 'i metallovedeniye, v-13, no.5, 1962,
735-737
LX T The effect of increasing stresses during repeated tests
v,as studied on lead and tin at room and at liquid nitrogen
temperatures. In earlier work (DAN SSSR, 1958, 118, No-3) the
authors showed that application of additional, monotonously
increasing, stresses in the case of elastic, freely damped,
oscillations, %,rhich leads to an appreciable increase in the
internal friction, will also lead to the damping decrement showing
a snecific dependence on the stress increase dp/dt = Ot , the
-im
plitude P and the frequency The rate of stress increase
,
from which the damping decrement is satitrated, oL cr, can be -
expressed by the experimentally verified proportionality relation
OLer VP
M
Card 1/2

Internal friction and plastic ... S/126/62/013/005/014/031
E073/E535
To improve the accuracy of relation (I )', the intensity of the
tangential stresses is applied -which, fox7 a tube stressed by
internal pressure (p at) and by a torque causing shear stresses
a12' can be expressed by
J2_ - -2-'i _21 '2 2
Ac)L t- + 30 sin Wt, + Cr0 (2)
2
where A rav (3)
4 h2
CY is the constant component of the tensile stresses occurring under
tRe effec t of the applied load. Analysis of this relation shows
that the intensity of tangential stresses cheCracterizes satisfac-
torily the plastic deformation in over-loaded micro-volumes.
Recrystallization cannot be the cause of the observed effect of
increasing stresses on the damping decrement, which decreases
during repeated tests after short pauses. Very short (30 Sec) Pauses
will nbt re-establish the initial properties of these regions for
which at room temperatur 10 pauses of 1@ min are required for lead and
40 min for tin. There are 4 fi,%ures.
ASSOCIATION: Fiziko-tekPniche.,;1c3_y institut AN UlcrSSR @Ph@sicoT
@TJRMT'r technical Institute A U gSSR
rD: I:ay 22, 19Q1
C A i: -d - 1@ 7 9

S/032/62/028/001/014/017
B116/BIOB
AUTHORS: Garber-,_R. I., Gindin, I. A., Neklyudov, I. M.,
6h-ech6l'nitskiy, G. G., and Stolyarov, V. M.
TITLE: Device for programmed metal hardening
PERIODICAL: Zavodskaya laboratoriya, v. 28, no. 1, 1962, 107 - 109
TEXT: A device has been designed for programming the load on samples.
It permits determining the effect of the gharging rate on the material
properties up to 8000C in a vacuum of 10- mm H or in inert gases.
The charging rate can be increased from 10 g/mm per hr to 3 kg/mm^ Der hr,
Moreover, rates Of UD to 80 kg/mm2 per hr are possible. The maximum-
load is 350 kg. The sample elongation (UP to 4 - 5 mm with an error c'L
0.5 4) is measured with an optical strain gauge. Reduction of the
charging rate to values corresponding to diffusion hardening lowers both
the total deformation and the rate of steady creep. The device (Fig. 1)
operates as follows: Dynamometer spring (6) is compressed by the
reducing gear (7). The charging rate is regulated by varying the
periodic Operation of the motor (8) (PA-09 (RD-09)-type) driving the gear
Card 1/3

3/032/62/028/001/014/017
Device for programmed metal hardening B116/B108
(7). The sample is heated by a tubular furnace with molybdenum coil, and
the temperature is regulated by an 3RA-12 (EPD-12) electronic potentio-
meter. There are 4 figures and 6 Soviet references.
ASSOCIATTON: Piziko-tokhniclieskiy institut Akademii nauk USSR (Physico-
technical Institute of the Academy of Sciences UkrSSR)
Fig. 1. Diagram of device for programmed hardening.
Legend: (1) sample; (2) and (3) fastenings; (4) cross piece; (5) throe
bars; (6) dynam@meter spring; (7) reducing gear; (8) motor; (9) ball-
bearing joint; (10) indicator; (11) mains connection; (12) base Dlate:
(113) vacuum chamber; (14) sylphon; (15) limiter; (16) to pump.
Card 2/3

GARBM, R.I.; GIIIDIII, I.A.; CHIRKIM, L.A.
Twinning and annealing of nonequililn-ium iron-nickel alloy of
the SiYffiote-Alin iron meteorito. IL-teoritika no-2-3:45-55 163.
0 URA 16:9)
(Sildiote-Alin Range-Vateorites)

ACCESSION NR: AR4041609 S/0137/64/000/005/IO49/IO49
SOURCE: Rek, zh. Metallurgiya, Abu. 51289
AUTHOR: Garber, R. I.; Soloahenko, I. I.
TITLE: Accumulation of microdefecta during elaotico-plastic reverse bond
CITED SOURCE: Sb. Relakeats, yavleniya V met. i splayakh. M., Metallurgizdato
1963, 80-84
TOPIC TAGS, microdefect, crystal, elasticoplastic bend, reverse bend
TRANSLATION: On special installation, a diagram and description of which are given,
regularities are studied of accumulation in transparent crystals during eiastico-
plastic bend of the dislocations and defects scattering light, and the influence
of accumulation of defects on internal friction. Werking frequency of forced
oscillations of oamploo amounted to rV1 cps. Integral light. scattering was deter-'
mined on electronic installation with FEU-18A photomultiplier. Intensity of light
scattering was measured with motionless sample during stops of pendulum.
Card 1/2

ACCESSION NR: ARWA1609
Single crystals of NaCl and LIF,_p@eliminarlily annealed at 65* for 40 m-d 25 hours,
respectively were investigated. Aa@plitude of stress imounted to 200 g/M2.
Obtained curves of dependency of damping decrement 6 and magnitude of photocurrent'
.(tmnspu_-_ncy) I from number of bend oscillations of sample N show that with
growth of N magnitude b decreases (which is accompanied by decrease of sag and
increase of number of slip bands), I also decreases, that isintegral scattering
of white light is increased. Saturation in change of given properties in
observed after 104 cycles. During stops and holding of crystal without load there":
occurs partial restoration of transparency-at constant value of 6 . It is as-
sumed that such rest, not removing work hardening, leads to partial restoration
of contacts between fragments formed in process of cyclical deformation. For
crystals of UF values of b and I with growth of N also decrease; besides in aU
cases moment of saturation for 6 sets in somewhat faster than for L Metal-
lographic analysis confirmed that reverse deformation with limited amplitude of
stresses leads to accumulation of defects and increane of dislocations and elip,'@
lbande; with thin saturation of hardening occurs with smal-ler number of cycles
than process of dispersion.
SUB CODE: SS, KH ENCL: 00
Card 212

S/181/63/005/001/032/064
B102/BI66
AUThORS: Carber, R. I., and Stepina, Ye. I.
TITLEj Mechanism of mixing of dislocations during elastic twinning
PERIODICALt Fizika tverdogo tela, v. 5, no. 1, 1963, 211 - 219
TEXT: Formation and variation of elastic twins in calcite crystals was in-
vestigated by photographing and photometrizing the transmission interference
patterns. The elastic twins were created by pressing a steel ball against
a crystal face. Lenrth and thickness of the wedge@-shaped twins were pro-
portional to the load. The creation of the twin and its growth depended
greatly on the stress distribution inside the crystal, i. e. not only on
the load but also on the ball radius. Balls of different dimensions but
impressed with equal loads yielded twins of different length and thickness;
the greater the ball diameter the shorter the twin; twins of equal length
were thinner when produced by a larger ball. When changing from loading
to unloading, or vice versa, the twinning process shows a hysteresis effect
with respect to the twin length. This effect is due to the change in sign
of the dislocation friction forces (Peierls forces) when changing from
Card 1/2

'Mechanism of mixing of ...
5/181/63/005/001/032/064
B102/Bi66
loading to unloading. The kind qf hysteresis depends
Peierls forces and surface tensi8n. In calcite the Peierls
rather weak. The length of the hysteresis reirion,decreases
length and it vanishes at 0.1-0.2 mm twin length. The
shape and growth of elastic twinn depend;uniquely on
tribution along the twin and this distribution is determined
defects and the Peierls forces. There are 7 figures.
SUBMITTEDs July 28, 1962
on the ratio between
forces are
with the twin
rules governing .
the dislocation die-
bY the crystal
Card 212

GARBER, R-I.; GINDIN I.A.; SHUBIN, Yu.V.
Cokpresaion of beryllium sin s@uals along the hexagonal axis
'gle cry
in the tem*ature range 4.2 to 9b6b K. Fiz. tver. tela 5 no- '2:
434,442 F (mu 16 -.5)
(Beryllium crystals) (Strength of materials)

@;AitjLAP R.I.; STEPINA, Ye.I.
Strengthening of calcite following multiple twii.ning. Fiz. tver
tela 5 no.9:2656-2662 S 163. (MIRA 16:10)

GARBER, R.I.; STEFINA, Ye.j.
Defects dua to the fusJon of tho! lnterlqyprs of' a polysynthetic twin.
Fiz. tvar. tela 5 no.12:3489-3495 D 163. (MIRA 17:2)

R.I;- GINDIN I.A.; STOLTAROV, V.M.; CHECHELINITSKIY, G.G.;
_-GMkIkA, L.A'.
Apparatus for studying the damping of low-frequency torsional
oscillations. Prib. i tekh. eksn. 8 no.3tl72-174 MY-Je 163.
(K[RA 16:9)
1. Fiaiko-tekhnicheskiy institut AN UkrSSR.
(Oscillations-Electromechanical analogies)

S/126/63/015/003/022ofO25
E073/E320
AUTHORSs Garber, R.X., Gindin, I.A. and Neklyudov, X.M.
TXTLEs Xnfluence of "programmed strdngthening" on the creep
and recrystallization-of iron*at elevated temperatuxes
PERXODXCAL: Fizika metallov i metallovedeniye. v. 15, no. 3.,
1.9631 473- 475
TEXT: Xn earlier investigations on calcite, bismuth and
iron, the.authors found that in addition to ordinary strengthening
caused by lattice distortions during the process of plastic
deformation under a continuous load, there is also "programmed
strengthening 11.due to diffusion-blocking and strengthening of weak
and overloaded lattice nodds. This produces an increase in the
yield point. plasticity at low temperatures and an increased creep
resistance. So far, an improvement in the mechanical-properties
@.has been observed only attemperatures lower than or equal-to the
temperature of the programmed treatment. In the work described
here, specimens of Fe (0-03% C)o were polished and chemically
etched, vacuum-annealed at 88o C for 3 hours and 2then slowly
cooled. After' "programmed loading" up to 8 kg/mm at 300 OC at
Card 16

5/126/63/015/003/022/025
Influence of .... E073/E320
a rate of 90 g1mm 2@h the specimens were s@bjected to a 100-hour
creep test at 400 C with a load of 7 kg/mm . The creep rate of
previously progr4m-loaded specimens was significantly lower
.(about 5.6 x 101"-'@%/h) both'in.the initial and An the steady-state
stages) than'that of specig!ns to which the final load had been
applied quickly (1.3 X_ _10,:_- )J/h,in' the steady-state section).
-This indicates thit,.qverf ja@,Ing.does -not eliminate -the, off ect of
-incroaied -'resistance., to I-xetp'@ of,@@program-4trengthene,d'@ specimie''n"s - -----
A-61 oth- ypes-'of s@eci ens after
Microstructu'res -,are -repi(i&ii:@e m
0
Annealing at 830 Oc for-3-hours: 2f specimens loaded at 400 C.
with a load increasin@;'to 16 @S/mm . whereby the rate.of increase
varied between 22U and 6 x 10 S/mm ./h; of specimens loaded
quickly. The residua@l'deformations were 1.3 and 1.6%. respective4
-The microstructure of-specimens which were-subjected directly to
the final load showed sign 's'of selective recrystallization,
whil-st the microstructure iof the program-loaded specimens was
almost the same as prior to annealing. The author',consider the
results as a further proof that*program-loading leads to a more
Card 2/3

S/126/63/015/003/022/025
Influence of E073/E320
equilibriated, stable structure in that the strengthening does not
seem to be accompanied by an increase in the free energy of the
crystal. There are 3 figurea.
SUBMITTED: 'August 15, 1962'
Card 3/3

L ift4q_63 EWP(q)/B1dT.(mi)/BDS AFFTC/ASD 'JD
ACCFMICN NRt AP1002850 S/0126/63/0-15/0061tgC-8/0913
AUTHORSt Garber R. Oindin, Is A*; Neklyudov, 1, M. 4/,
TITLE: Programmei.1virdening of commercial iron
'SOUP
WES risdka.metallov i metallovedenlye, vo 15, ho., 6, 1963P 9M-913
TOPT 0 TAM i prograumted hardening, iron, mechanical property
1ABSTRAM One@of the possible methods for improving mechanical f solid
!bodies consi-sts o' diffusive blocking and strengtheriDO of weak or over-stressed
iparts of a specim)n. Such parts may develop shearindr, sliding surfaces, twinning
ibnnds, or dialocahlon sources. This method was called "the programming of
!@hirde-dng. " The 4evice used in the progravvdng procedure is described, rt'-a3 Iowa
!the stretching of a specimen at high temperatures and at very amall rntes of load
lincrease. The co-uercial iron aamplea thnt underwent a proEamed hardeni 1@.t
;'100C were studied. The tensile test was,condiiated -it the temperature of liquid
nitrogen.snd also at room temperature. The creep tist was also conducted at tOOC'
Trell.rdnary deforiation at high temperatures -nd lo-Y rates of loading reaultel int
.1
1) increase of fl-3w limit and harderdir roftl-s-, 2) increase In plasticity at,the
if emporature of R juid nitrogen; 3) a -nibrtnnf.*- -il de ireeae in c!-eep velocityl
_2

1 18049-63
iAGGESSICK NHI AP3002850
fl.) eliruination of creep at 3000., It is concluded thnt the obsorved effects are due
i t4n a diffusive hardeTdng of weak and overstressed rogions in the samples.. Tht
authors express Visir appreciAtion to V, M, Stolyaror and Go G. Cheabellnitakiy-for
their help In the construction of,tbis device,: Orig, art# has-..-6.f1gwes,
ASSOCTAWOUS Fiziko-tekboicheady institat AN USS
R (rnstitute.of Physics and_
Tachnolop-T. Aorsde:r of Sciences, Mcr@SR)
SUBIETTEDs -26jun62, DATE ACQ: 23jul63 EV0111. '00
SUB CODEt )AL NO RE? SOVt 008 OMRs 001
!
Caro _2/2

F@IISMAL, MikhAl Aronovich; FIGUZOV, Yueiy Vasillyevich; GOLOVIN
Stanislav Alakseyevich; GARDEP, it.I., prof., retgenzent
[Internal friction in metals and alloys] Vnutrennee trenie
v metallakh i splavakh. Moskva, Izd-vo Motallurgiia, 1964.
245 1). (MIRA 17:6)

GOBERS R.I.; S-TEFINA, Ye.l.
Secondary cleavage in calcite crYstals. KrAstallograflia 9
no.2:255-2159 Pfr-Ap164. (M-TRA -L-(- 5)
1. Fiziko-tekhnicheskly institut All UkrSSP,.

GiNDIN, I.A.; 1140GILINIKOVA, T.T.; NE*,U,,'UDGV, 1.M.
Internal friction of iron hardened by programmin.g. Fiz. mat. i
matalloved. 18 no.3;443-".7 S 164. (',,',IRA 17.11)
1. Fizlko-tekhnichsskly institut All UkrSSR.

IVA (d:)/ F ?.
36625-65 EvTrWAwPWA T/_WPW/MY*P(k)/EVWP(b)A A( -P( A LW
@E @ @Sl 0 NNR: AP5002348 S/0126/64/018/006/0904/09
0
AUTHOR: Garber ikhgylov kiy'-
R. - 1. G indin, 1. A.; ZaUvadnyy, S. Ya,; M
s
MIN
V. M. At I M
judo
TITLE: Effect of pr
ogrammed hardening on ep o lycrystalline zinc and
stability.during cyclic heat treatment
SOURCE: Fizika trietallov i metallovedeniye, v. 16, no. 6, 19648 90441081
T
-OPIC TAG& polyaryst9line-zinc, creep, programmed hardening, beat treat-
ment, cyclic heat treatment
ABSTRACT: The effect of P12115iramme'd hardening (hardening by controll, d appli-_
cation of stress at slow ratek) on the creep of polycrystalline zinc at room tem-
d:
"pL
@,rati e an on its i@esistance to forming during cyclic heat treatment was stud-
ied. The linear deformation of -annealed polycrystalline zinc and of sarn es sub-!
Pi
2/
@j jected to loading (I_t5xI0-4 kg/mm min) and to loading beyond the yield point,
(2.6 kg/mm2/min) *as compared. The elongation of the programmed samples
Card 1/2

36625-65
ACCESSION NR: A] 5 @OO 2 ---------
p
ioly-
wa less than in the annealed and. was redue'd t @U,
rap stressed samples; e wo
x 10"4 kg/
times as the,programmed rate was decreased from 5 to 1. 5 mm
Samples subjected to normal treatment were less resistant to heating-cooling cy-!
cles than programmed samples. The hardening increased as the maximum
temperature'of the cyv e was reduced. -,- The
maximum temperature -approached-tW-
melting temperature (0. OTM K)@ The creep in progra harden6d*samples was
-lesa -than -in-those-otherwise deformed.- Metalloaraphic-talysis showed slip
'i bands and the fornliation of substi@uctures in a small nU ffiber_df-tke-grains-
migration of the bOundaries occurred in samples after programmed and after or
dinary hardening prior to thermal cycling; after that the migration in the program-.,
J med samples was'much less noticeable. Thus prograrnmed hardening of polyery-,,
4
stalline -zinc- increased its creep strength and Its resistance to forming during
cyclic heat treatment, Orig. art, has: 3 figures and I table
ic
ASSOICITTION: Fizikd-tekhnicheskiy institui AN tkrssR (P@Xsical-teclui al Inst
11--tute AN blaOSO,
OlAug63 ENCL: 00 SUB CODE: MM
SUBMITTED.
NR REF SOV: 009 OTHEA'. 001
Card 2/2

ACCESSION NR: AP4043667 S/0053/64/083/003/0385/0432
AUTHORS: Garber, R. I.; Fedorenko, A. I.
TITLE: Focusing of atomic collisions in crystals
SOURCE: Uspekhi fizicheskikh nauk, v. 83, no. 3, 1964, 385-432
TOPIC TAGS: crystal lattice structure, fast particle, radiation
damage, particle collision, cathode sputtering, ion bombardment
ABSTRACT: The authors have systematized and explained as far as
possible the theoretical treatments of the mechanism of atom focusing
occurring in a crystal lattice when solid materials are bombarded
by fast particles, and bring together the main experimental results.
reported in the literature. Each of the theories recently developed
for the formation of radiation.damage in,solid materials (cascade
displacement of atoms, th6rmal spikes, displacement zones, and others)
is analyzed briefly,and its advantages and shortcomings compared.
Card 1/5

ACCESSION NR: AP4043067
The study ot atomic collision focusing, whereby bombardment of a
crystal by a charged or neutral particle results in preferential
propagation of a wave of atomic collisions along the most closely
packed directions, under the influence of the regular location of
the atoms in the lattice to various branches in physics is odtlined.
It is shown to be important not only to investigations of radiation
damage, but also in connection with studies of cathode sputtering,
the sputtering of surfaces of artificial earth satellites and space
ships, destruction of metal by ion bombardment in plasma and ion
engines, and the contaminations of plasmas in thermonuclear devices.
The section headings are: 1. Introduction. 2. Theory of radiation
damage. 2.1. Cascade displacements of atoms. 2.2. Thermal spikes.
2.3. Displacement zones. 2.4. Replacement collisions. 2.5. Crowdi-
ons. 2.6. Depleted zones. 3. Focusing of atomic collisions. 3.1.
Propagation of collisions along a linear chain of atoms. 3.2. Focus-
ing and crowdion collisions. 4. Formation of focusons in phase-
centered cubic metals. 4.1. Focusing of atomic collisions in the
Card 2/5 0

ACCESSION NR: AP4043067
direction. 4.2. Replacement with focusing in the direc-
tion. 4.3. Replacement with focusing in the direction.
4.4. Dependence of the number of focusons on the total number of
displacements. 4.5. Interaction of focusons with lattice defects.
5. Formation of focusons in body-centered cubic metals. 5.1. Focus-
ing of atomic collisions in the direction. 5.2. Focusing of
atomic collisions in the direction. 5.3. Focusing of colli-
sions in the direction. 6. Formation and propagation of
focusons in other crystal structures. 7. Study of atomic collision
focusing of high-speed electronic computers. 8. Experimental con-
firmation of the existence of atomic collision focusing by the
crystal lattice. 8.1. Cathode sputtering of face-centered cubic
metals. 8.2. Cathode sputtering of polycrystalline face-centered
cubic metals. 8.3. Cathode sputtering of body-centered cubic me-
tals. 13.;'4. cathode sputtering of diamond structure metals. 6654,
Cathode sputtering of hexagonal metals. B.G. Effect of nuclear
cbarges of moving an,d stationary particles on cathode sputtering,
Card 3/5

ACCESSION NR: AP4043067
8.7. Effect of specimen temperature on cathode sputtering. 8.8.
Study of angular distribution of sputtered particles in the bom-
bardment of metals by ion beams. 9. Experimental confirmation of
the part played by focusing processes in radiation damage in metals.
9.1. Electron-microscope observation of radiation damage. 9.2. Di-
rect observation of radiation damage. 10. Explanation of th@ changes
in the properties of metals under irradiation, in terms of atomic
collision focusing. 11. Experimental methods of studying atomic
collision focusing. 11.1. investigation of cathode sputtering in
a glow discharge. 11.2. Study of cathode sputtering by means of
ion guns. 11.3. Study of cathode sputtering with an electron
microscope. 11.4. Observ7ation of focusons with the ion projector,
11-5. The preparation of thin single crystal and polycrystalline
metallic targets. Orig. art. has: 49 figures and 49 formulas.
ASSOCIATION: None
Card 4/5

ACCESSI6N MR: AP4043067
SUBMITI!ED: 00
SUB CODE: SS NR-REF SOV: -031
ENCL: 00
OTHER: 095
Card 5/5

142040-65 E'dT(M)/'Bfll(4)/Wk(d)/T/EWP(t)/EWP(b) JD
1ACCESSICS M-@ AP5010939 IUR/02"/65/000/007/0 0i
IMHORS; Garbert R.- 1. 4.; Polyakovo L. U.
TITUE: A method for dete
rmining inherent plasticity. Class 42t No. 16948
SOURCE: Byulleten' izobreteWv I tovaraykh znakovp no- 79 1965# 122
TOPIC TAGS i plasticityl,/deformation. rate 9 density determination
ABSTRACT: Thia-Author ortificate presents amethod for determining the inherent
plasticity of metals$ alloys, and nommetallic solid materials. To increalao the
accuracy of eistimating the inherdnt plastioity, the-maoroscopio density or the.
specimen is,3heasured during pleatio.deformation, while the deformation$ during
.,Iwhose unifott increase there occurs a sharp:decrease of plasticityp is taken as the
characteristic of the inherent plasticity,
ASSOCIBION: Pisiko-takhrAchasklyIns-bitut AN UkrSSR (Pbysico-teebaical Institute
a UkrSSR)
SUMITTED: 25jid63 ENPL: 00 SUB 001MI @IE
'NO REP SOY: 000 OTIMS -000
M2

L z5o75-65 -EWT(l))FEEC(b)-@2/T IJP(c)
ACCESSION NR,- Ap$m4o -
AUTHOR: Garbeg. ".tggina.'Ye, I*
TITLE:, Speed of vanishing of 01astic twins in calcite
SOURCE: Pizika tverdogo te is 196 141-166
V. 7, no
lat 59
TOPIC TAGS: calcite
twinningLmlastic twin, twin velocity, dislocatign motion,-:
temperature dependence'
AWTVACT: The vanishin
gof elastic twins incalcite followinga rapid;: removal of,
the load was me-asured.by high speed motion picture photog ap
r by. A diagram of the
equipment is shown in Fig. 1 of the enclosure, and an FP-22 camer@@,was used for
the photography. An additional lens in front of the camera made it-possible to
take pictures in natural size on 8 mn film ati
100,000 frames per second. The re-.@,
sults have shown that the speeds of the twins',reach tens of meters per secondp
which is much higher than the value obtained @y F. P. Bowden and R. E.-Cooper
(Nature v. 19% lo9l,, 1962)o An analysis of V4e kinetics of stress removal in -a
crystal leads to the assumption that the speed of the twinning dislocations in
tard 1/3

T _1 25074-65 EW(1)/T/MC(b)_2/EWP(J) UP(a)
ACCESSION NRI AP5003431 s/0181/65/w/001/0167/017i
AMOM GEberx R. I&; Pojyg@oys Le H
TITLE: Change in densLty'und'e@r plastic compression of ionic-crystalq,,N
SOUCH: Fizika tverdogo telat V.- 7s no. 19 1965t 167-176
rear.
TOPIC TAGS: 'density change at Measurementl.strain measurementy rupture
stieneuh, ionic crystal
ABSTRACT: Thepurpose of the inveatiSaUon was.to study further the processes
articipating in failure under plastic deformation, by determining the cbnnection'
p
between the strzsb, strainjand the residual changes In the density. To this endj
sampler. of natmxal rack salt, end of potassium chloride-grown-from the melt were
-subjected to uniaxial compreasionj -and-the stressj strain., and relative change in
volume were meabured. The sampleavere parallelepipeds measuring 5-6 i= in cross-
sect3 on and 14-716 mm-in length. -Thechinge in volume was measured with the'aid,
of equiliment similar to that described by Bridgman (J. Appl, Phys. v. 20p 1241p
49). The results show that plastic compression of the crystals leads to a re
the competing influence of the diaper-'
sidual change in densitri which in 'due to
@ard

'L 25074@61
ACCESSION NR: AP5003431
-Sion and renewal:of the contacts. During the initial stages, the density in.
creases, after which it decreases and remains constant within a certain strain
interval. Further deformation leads-to an abrupt decrease in the densityj which
I;. continues up to the instant when the crystal fails* In a region of relatively
small change in density, the main process is the subdivision of a crystal into
blocks, with formation of ultramicroscopic defects. The abrupt decrease in den-
sity is connected with the formation-of large defectas the growth of which leads
to failure of the crystal. Almost the entire plastic part of the deformation oc-
c
s icith the average sample density changing by approximately lo-5 whereas
ur
to ,,o@4.
local changes in the density nearthe,slip bands amount 'The authors
N. 1.@Bashmgh= for help with,the measur
thank JC. K. _SLC@gX and ements." Orig.
art. has: 11figures and.2 forwilas.@
ASSOCIATIONI Fiziko-tekbaicheskiy institut AN_1JkxG8A) Khar kov (P1mrs1cotechW&L___@
AN
UkrSSB
Institute,
SUWMD1 OaTtd64 ML t _.'OO $013 =9 it SSI146
IM REE, Mir! 010 Omit 066
Card
2/2

L 38528-65 EEC(b)_2/E`oU(1)/NV M)/Ef t)
4A c)/T/14P( P 4 P(c) GGIJD
8/0181/6
:ACCESSION HRt 050052W@ 5/007/062/0459/0443
@AUTHOR: Carber R, Is; Stepina, Y*4J, 5 2-i
TITLE: Poseible.mechanismfor~multiplication of twinning dislocations
SOURCE: Fizika tverdogo telai v@ L-no,129 1965, 459-463
,TOPIC TAGS: twinning, dialocation,loop, dislocation motion, crystal imperfeicti@nd
cryttal inclusion
ABSTRAM The authors propose@&-new,mechanism for multiplication-of tvi.nning,dis-
locations, which may be effective in.the-case of crystals with a_limited.number@ !of
sources* -The mechanism is similar to that1which gives rise to slip dislocationi;
near inclusions * in a perfect crystal'at sufficiently low general stresslevel. its
observed by is J. GLImen (J. App.10- Phya. v. 30, 1584, 1959), differing from the
latter only in that the elastic field-of the twinning dislocations moving in the
neighboring layer may also Tarticipate In the production of the loop and may-ali;o
be concentrated on the Inclusions The newly produced loops expand under the in-"@
-fluence of applied stresses and give rise to new loops on concentrator inclusions
which they.encounter, This possibilitr of dislocation-loop nucleation on the con-
Card 1/2

L 38528-65
ACCESSION MR: AP5005282
0'
centrator, in conjunction with the low...energy of formation of a tv -dimension&i
nucleus on the boundary between the twin and the parent crystal, may make posa,;Lble
transverse growth of a tvin layer.due@tcl the formation of plain nuclei on the
-boundary in the presence of random Inclu3ions near the boundary. Such a mechadism
A.agrees vith the features -of -tvinnlng. in'-calcite. -The concentrators may,:-be of dif_
t er . e- ti ated
ferent sizes and may concentrate the.stresses in differen mann 6 Th - ea gi..
critical dimensions of the created.atable loops, assuming the stress on the bovmd-@
ary between the twin and the.,parent crystal to be in the range from 40 to 400"
g/MM21, is from 0-3 x 1(@-3 to 0*3 x 10-4 cmi - 'Art is pointed out in the conclusion
that the described mechani= is sultab2a for any'cr7stal, being Independent of,
tte structure, and does not pertain to twin formation in perfect crystals. ft1he
authors thank A. M. Kosevich, L .-Gindin, and V, L. Indenbom for a discussion or
the vor O@_ig. art* bast 2 figuress
ASSOCIATIONt Fisiko-tekhnIcheskly,-Institut AN Uxr66R$ Khw1kov (Pbyslcotechnl cal
!-Institute.AN UkrSSI.R)
SUBMITTEM 22Jul(A EKCL1 00 SWOODSt as
WREF 9DVv 005
Cud 212p@s

TOPIC TAGS: tungste T,'recrystallization# microblock dispersiou, crack evolution,
autoionic microscope
ABSTRACT: This investigation was ained at further confirmation of a hMthedio
iv, 2
advanced by one of.the authors'.previounly (Carber, UFZh Y. 1 88, 1956; Fwol-
1089, 196o) tbat,plastic deformation can be regarded, starting vith a certain . .
stage, as simultaneous dispersion.of microt1coks and restoration of contact te-
tween fragments. Using an autc-iontq microscope, the suthors observed the
tion of a crack iu a single cljstal@olf tungsten at liquid-nitrogen temperature,
under the influence Z? the quenching stressea and of the force produced by an
electric field. The evolution of the crack during the ecurse of evaporation of a
1/2