SCIENTIFIC ABSTRACT GRIBOV, V.N. - GRIBOVA, I.A.

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• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000516710017-3
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: January 3, 2017
• Document Release Date: July 27, 2000
• Sequence Number: 17
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

69698
s/126/60/009/03/021/033
E193/9483
On the Effect of Preliminary Straining at 3009K on the Mechanical
Properties of Technical Iron at 77*K
The relationship between the ductility of the test
pieces at 77*K and the degree of pre-straining at 3000K
is illustrated in Fig 4, where elongation (6, %) and
reduction of area (~, %) are plotted against cy, (kg/mm2)
on the left-hand side diagram and against 60 (%) on the
right-hand side diagraml the experimental.points denoted
by open circles relate to 6 , crosses relate to %P I
and the triangle indicates .6 of test piece Nr 1, which
had not been subjected to preliminary straining; numbers
ascribed to each point denote the number of the test
piece. Fig 5 shows how the yield point as, kg/mm2q
(open circles) and the true tensile strength Ob, kg/mm2
(full circles) at 77*K varied with the degree of pre-
straining at 300*K, given in terms of oo (left-hand graph)
or 60 (right-hand graph), the triangle indicat4ing the true
tensile strength of test piece Nr 1. A characteristic
feature of test pieces which, at 770K, failed in a
ductile manner (test pieces Nr 2 to 6) was twin formation
Card 4/8 and the appearance of mlip bands. It was revealed by

69698
S/126/60/009/03/021/033
E193/E483
On the Effect of Preliminary Straining at 300*K on the Mechanical
Properties of Technical Iron at 779K
metallographic examination of test pieces tested at
770K that the slip bands were formed alreody in the
elastic range long before the yield point was reached.
The microstructure of a test piece, pre-strained at 300OX
under ao = 8.9 kg/MM2 and tested to fracture at 770K,
is illustrated in Fig 6 (x 100) showing (a) twins and
slip bands at the point of fracture and (b) density of
twins at a distance of 1.5 mm from the point of fracture.
The variation of density of twins across the length of the
test piece is illustrated in Fig 7, where N,1N W is
plotted against the distance (mm) from the point of
fracture, curves 1 and 2 relating to specimens which
have failed in the brittle and ductile manner respectivelyl
N9 is the total number of grains in the portion of the
test piece dx = 0.25 mm long and 3 mm wide and N is the
number of grains with twins in that portion. The
relationship between the intensity of twin formation 1, %
(calculated from the formula given at the bottom of p 448
Card 5/8 as Eq (2)) and the magnitude of stress c0 applied azl

69698
S/126/60/009/03/021/033
E193/E483
On the Effect of Preliminary Straining at 3009K on the Mechanical
Properties of Technical Iron at 779K
during preliminary straining, is illustrated by the
graphs reproduced in Fig 8 where the number ascribed to
each point denotes the number of the test piece.
Regarding the slip bands, they are straight when formed
in the initia-_ stages of the formation and curved in the
heavily deformed material. Fig 9 (x 166) shows the
straifht and curved slip bands in specimen Nr 3, deformed
at 77 K to 6 = 4%. Curved slip bands in the region of
local deformation in specimen Nr 3, deformed at 770K to
6 = 8% are shown in Fig 10 (x 360). Finally, Fig 11
shows the local deformation near the grain boundaries
and broadening of the grain boundaries, revealed by
micro-interference meter in test piece Nr 7, pre-strained
at 3000K under a stress equal to the yield point.
Several conclusions were reached. (1) Technical iron
subjected to preliminary straining in the elastic range
at 3000K and then cooled under load to 770K, undergoes a
transition from brittle to ductile condition; this
Card 6/8 transition is accompanied by an increase in the true Vr/

69698
S/126/60/009/03/021/033
E193/E483
On the Effect of Preliminary Straining at 300DK on the J~Iechanical
Properties of Technical Iron at 77*K
tensile strength, as compared with the brittle strength
of technical iron. (2) Technical iron, pre-strained
under optimum conditions (oo =-9 kg/mm2) i,
characterized by elongation - 10-5%, reduction of
area - 23% and tensile strength 20% higher than that of
untreated material. (3) The transition of technical
iron from brittle to ductile condition is due to special
conditions of generation of elementary displacements
brought about by high temperature straining at low rates
of strain and cooling tinder load; those conditions are
favourable for the formation of arrays of dislocations
on various defects and for breaking these arrays without
destroying the continuity of the metal. (4) Technical
iron 0pre-strained at 3000K, begins to deform plastically
at 7~ K under a stress lower than the yield point.
(5) Brittle fracture of technical iron is not caused by
twinning, since it has been found that maximum ductility
corresponded to maximum intensity of the twin formation.
Card 7/8 (6) The critical temperature of cold brittleness of

On the Effect of Preliminary Straining at
Properties of Technical Iron at 770K
.69698
S/126/60/009/03/o2l/033
E193/E483
300*K on the Mechanical
technical iron is not lowered by pre-straining at 300OK-
There are 11 figures, 1. table and 12 references, 8 of
which are Soviet and 4 English.
ASSOCIATION2Khavlkovskly fiz!ko-tekhnicheskiy institut AN USSR
(Kharkov Institute of Physics and Technology AS UkrSSR)
SUBMITTEDi July 15, 1959
Card 8/8

GINDIN, I.A.; IAZAREV, B.G.; STARODUBOV, Ya.D.
Characteristics of the mechanical properties of lithium connected
with low-temperature polymorphic tranBitions. Fiz. met. i metalloved.
10 no-3:472-480 S 160. (MIRA 13:10)
1. Fiziko-tekhnicheskiy institut AN USSR.
(Lithium-Testing) (Metals at low temperatures)

10
24(2), 18(0) S/053/60/070/01/002/007
AUTHORS: Garber, R. I., Gindin, I. A. B006/B017
TITLE. The Physics of,the Strength of Crystal Bodies
PERIODICAL: Uspekhi fizicheskikh nauk, 1960, Vol 70, TTr 1, pp 57-110 (IISSR)
ABSTRACT: Although modern engineering makes over increasing demands on
the strength of materiala 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 possibilites of raising them. Part 1 deals
with the microscopic theory of strength, especially with the
theory by Ya. 1. Frenkell; Pro nkell proved that the critical
shear stress in the case of which the lattice becomes unstable
is equal to G/2n where G-denotes the modulus of rigidit5i this
value is much higher than that for plastic crystals (10- G).
By more accurate investigations other authors obtained a still
theoretical value of G/30 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 otructural 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. Winder, Ya. 1. Frankel', B. Ya. Pines, A. F. loffe,
S. N. Zhurkov A. V. Stepanovi experiments and their results
are mentioned~- Part 4 reporte-on the scale effect and the
strength of t4e thre4d-like crystals (A. P. Alsksandrov, S. N.
Zhurkov - statistiGal theory, R, I, Garber - experiments with
calcite orystalel figures 3-9 show different characteristics
of strength, also Bartonov and Chepkov are mentioned). Part 5
gives a short survey on the statistical theory by N. N. Daviden-
kov, Ya. 1. Frankel' and T. A. Kontorova, and part 6 deals
with the origin of cracks in the crystal nucleus (theory by
A. V. Stepanov and its verification by X. N. Davidenkov, Ye. M.
Shavandin, and M. V. Klassen-Neklyudoval experiments and their
results obtained by S. 0. Toobkallo, Stapanovt S. N, Zhurkov,
T. P. Sanfirova at &I). Part 7 presents the theoretical and
xperimental investigation results of dislocations and micro-
:
racks (Ye. D. Shchukin 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 our-
face defects and adsorption; As F, Ioffe, P. 1. Rebinder,
D. L Shillkrug)o Part 9 deals with the dependence of strength

The Physics of *he Strength of Crystal Bodies S105 60/070/01/002/007
B006YB017
(I.V,
an temperature and time
Obreimov, Be No ZhurkovI Be Yao
Pineet I. Ya. Dekhtyar, To Ps Sanfirova, and K. A. Osipov).
Part 101 destruction on creeping, part 11; cold brittleness
(theory by loffe for rook-saltj experiments by No No Davidenkov
and To We Chuchmanj miorostructure photographs by Garber, Gindin,
Konsianlinovskiy, St Oroduboy). Part 121 diaoussion of the struo-
turt of high-eirength alloys (Go V. Zurdyumovo Be Me Rovinakiyp
Lo Me Bybakovaj Be 11. Rovinskiyt Porkas, and Khondras, V. A.
Illinap Vo Ka Kriiskays, Grusinp Tyutyunik, Entin, V. L
S1ar*~sv# P. No Aronova~. Part 13 and 14 are devoted to fatigue
and hordeningi the two types of hardening are briefly dinoussed
according to Ro I, Garber. In conclusion it in then pointed
out that %he-strong difference between theoretical and experi-
mental strength is due to structural defects and that strength
could be increased by a regular stree4 distribution in thermal
and mechanical processing. There are 38 figures and 223
references, 108 of which are Soviet#
Car4 3/3

S/181/61/003/001/021/042
B006/BO56
AUTHORS: Garber, 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 directiom.
This is done in the present work. For a diatomic solid, the stress
-ft +gt2 (1), where 6 is the relative deformution, and f and g
constants. If 6 is considered the aum of shifts due to applied
Card 1/3

S/181/61/003/-001/021/042
Elastic deformF-tion and thermal expansion B006/BO56
then G' = 'r1+(2gt1-f) 2
forces (6,) and to thermal vibrations (t2)1 72 72' C2+gF2*
Averaging over time gives T = Irl and L, = 9E2 /(f-2g ~). L2 may be detp -mined
from the mean density of the energy of elasticity of thermal vibrations:
T
ce- I_CV dT, and fE2 2 + 3
V '/ 3. By taking into account that &
2/ g72 C 2
0 V 2/2
small quantity changing its sign, one may assume that v dT =-ff-
1 2
T 0
I f -C2 cLdT, where CK is the coefficient of thermal expansion, one obtains
& - 2gCV/Vf (2gEl -f With 6'1.0, t1.0, d,-,L = -2gCV/Vf 2, one obtains
0
0~0 On the other hand, it follows from the GrUneisen relation
that 0k, a KCVt/3V, whare K denotes compressibility, the GrUneisen
coefficient, V the atomic volume. Thus, one obtains -Kf~/3. From (1)
Card 2/3

S1181161100310011021104 2
Elastic deformation and thermal expansion B0061 .0056
it follows that fc---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. d,-Fe 1.9
There are I table and 1 Soviet-bloc Ni 2.1
reference. W 2.1
Co 2.3
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR Khar kov (Institute
of Physics and Technology AS Ukr SSR, Kharlkov)
SUB14ITTED: June 6, 1960
Card 3/3

20798
S11811611002100310241030
2L4 ~Joo 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, 1961, 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 4~8~4, for
example, reach a strength of 1340 kg&m2. When t1he 'irst indications of sliding
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 twinning) 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/181/61/003/003/0211/030
B102/B205
ularly suitable for ouch experiments. Plastic deformation of these crystals
is effected chiefly by sliding in the basal plane (00o1 ) , of! tile faces Of
prisms of first order ~101 01, and by twinning in the planesl j0i2~ . This
was studied with the help of prismatic Be single crystals ( X 1 .5 X 3 mm)
of 99.9vilo purity. The crystals were compressed at 770K by a force perpendic.-
ularly acting on the basal plane (deformation rate; 0. 01 3~('O/s e c) .There
were no indications of plastic doformation up to destruction. Sliding and
twinning were impossible since no components of this foice were ac..L.E2" in
the respective directions. Under these conditions, the Be single '~:rystals
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
already at 34 kg/MM2. At room temperature, the maximum stress is only
210 kg/mm2 (perpendicular to the basal plane). Similar experiments were
carried out with calcite single crystals (6 x4 x1O mm) at 3000K, which are
deformed only by twinning. The orientation of the sin.-le crystals was such
that the twinning plane (110) formed an angle of 450 with the axis of the
specimen and theodirection of displacement 10011 1 opposite to the directio 'n.
in which the tangential stresses acted, which deformed the spenimen at a
Card 2/3

High strength
20798
S/1 BY611 /00~/00;'/024/030
B102 '1 205
rate of 0.004iof/sec. A strength of 23 k-/Mlll2was attained in t1jis case. The
lower bound is 40 9/mn,2. There are 7 rueferences: i1 Sovi,:?t-blcc and 3 n-~n_
Soviet-bloc.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN USSR Khar1kov (Institute of
Physics and Technolo--Y, AS UkrSSR, Kharlkov)
SUBMITTED: August 103 1960
Card 3/3

20799
It'jig S/181/61/003/003/025/030
14-IrOD ijlt4~, 11 co , 2 807, B102[B205
AUTHORS: R~~ ~., Lazarev, B. G., and Starodubov, Ya. D.
TITLE: Discontinuous character of plastic deformation at low
temperatures
PERIODICAL: Fizika tverdogo tela, v. 3, no. 3, 1961, 920-925
TEXT: The discontinuous character of plastic deformation of crystalline
bodies has been known long (A. F. Ioffej Ehrenfeet) M, V. Klassen-
Neklyudova), and the various effects of discontinuous deformation have been
investigated many times. In the authors' view, however, this problem has
not yet been studied in detail, which is the purpose of the present work.
Elongation and compression diagrams of the following metals were recorded
by a machine equipped with a sensitive, rigid dynamometer between 1.4 and
770K and at a deformation rate of 30 p/sec: aluminum, beryllium, bismuth,
tungsten, iron, cadmium, potassium, lithium, magnesium. molvbdenum, 0opper.
sodium, nickel, tin, lead, antimony; silver, mercury, tantalum, titanium,
chromium, cesium, ~,inc, zir-raniur, and uranium. In this connection, it was
necessary to cladaify the deformMlion jumps and to make a detailed study of
Card 1/8

20799
S/18 61/003/003/025/030
Discontinuous character ... B102XB205
a new kind of faults which are important at 4.20K and below this tempera-
ture. The principal results of these investigations are published here.
The discontinuity of the low-temperature deformation is essentially caused
by: 1) mechanical twinning, 2) polymori.li)us transitions, 3) peculiarities
of the plastic deformation of high-purity metals (mechanical recrystal-
lization, sliding along the grain faces, twinning), 4) relaxation proces-
ses with a regular increase of jumps. These four cases were investigated
individually. Figs. 1, 2, and 3 show the diagrams of deformations on
mechanical twinning (1), polymorphous transition (2), and of relaxative
JUMPS (3). These diagrams were recorded by the computer machine. Ad 1:
The authors studied the extension elongation of coarse-grained iron of
99.9V* purity at 770K. The jumps are only caused by twinning processes.
The kind of the effect depends largely on the grain size. Fine-grained
material showed no twinning jumps. Jumps of this kind can thus be prevent-
ed by an adequate thermomechanical treatment of the material. Ad 2:
Jumps due to polymorphous transitions occur in the compression of Li or
Na. Fig. 2 shows diagrams obtained for Li (purity of 99.93%) at 20 (1),
4.2 (2), and 1-40K (3). The transition i4to the stable low-temperature
modification takes place after a certafft-degree of deformation has been
Card 2/8

S/18 61/dUY7803/025/03()
Discontinuous character B1 02X3205
reached, and is accompanied by the occurrence of considerable faults. These
jumps occur only if the deformation takes place below the temperature of'the
polymorphoue transition. Ad 3: High-purity metals, such as Al (99-994F/-)
and Fe (99.99016) show mechanical recrystallization within the range of
helium temperatures, i.e., grains are formed, which are larger than the
initial ones. The process is somehow similar to mechanical twinning. Ad 4,
Whereas the effects described above occur only under certain conditions, all
the metals investigated show deformation jumps at sufficiently low tempera-
tures and a corresponding stress strain, which are due to relaxation
processes. These are characterized by a certain rule (Fig. 3 shows it for
Fe (99.9%.' pure) at 4.207~ They are due to the fact that elastic energy
accumulates and is released at a certain value. For some of the metals
examined here, a table contains the temperature and the degree of deforma-
tion at which the elongation process takes place discontinuously and regular-
ly. In some metals, an increased elevated strain stress corresponds to an
elevated temperature (e.g., in the case of Na), but there is still a temperas
ture threshold above which no such jumps will appear any longer, not even at
maximum stressl (for Na, e.g., above 200K). The rules governing the jumps
are observable both during compression and elongation. There are 7 figures,
Card 3/6

20799
S/181/61/003/003/025/030
Discontinuous character ... B102/B205
1 table, and 18 references: 16 Soviet-bloc and 2 non-Boviet-bloo.
ASSOCIATION:-.Fiziko-tekhnicheakiy institut AN USSR Khar 'kov (Institute of
Physics and Technology, AS UkrSSR, Kharlkov)
SUBMITTED: August 10, 1960
.100
0
zoo -
Figs. 2 and 3 0 .4
Card 4/8
-7,
Agg-p- 'g-
V
U
M

24.1 50C)
22051
3/181/61/003/004/017/030
B102/B214
AUTHORS: Garber, R. I., Gindi and Shubin, Yu. V.
TITLE: Orientation dependence of the slipping and rupture of
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 studied were bred from a 99.98~ pure
starting material, 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-rayo. The crystals
were cut in different forms by a special electro-spark device, after
which they were etched, ground, and polished, first chemically and then
mechanically. The tensile tests were made at the followin � angles to
the basal plane: a = 0 '5, 10, 15, 20, 26, 45, 70, and 90 (see Fig. 2).
The shearing direction 111703 coincided with one of the lateral faces.
Card 1/5

22051
s/18i/61/003/004/017/030
Orientation dependence ... B102/B214
The stretching was done at a con0tant rate of 0.005cfolsec 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 Pe
(Pig- 3) shows the a-dependence of the ultimate strength. The strongly
non-monotonic behavior of this curve contradicts the law of constancy of
normal stress on brittle rupture. The curve P26 is drawn according to
this law and does not represent the experimental facts in any way.
The experimental curve P9(a) can be described well by the equation
P16 ~ K(sin3acosa)-l 2 in the angular range a 20-700, where K = 3 kg/mm2
2
This equation corresponds to the law (T")destr K. However, the 0
experimental results do not correspond to this law between 0 and 15
At a > 200 slippin and rupture occur in the same system of planes, namely,
(0001). At a < 20 the crystalloGraphic elements of plasticity and
rupture alter and do not coincide (slipping: OOTC)~; rupture: 1701
Further, investigations of the structure were made before and a&r the
Card 2/5

22051
S/181/61/003/004/017/030
Orientation dependence ... B102/D214
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 elementn 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
.and 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: Fiziko-tekhnicheskiy institut AN USSR Khar1kov (Institute
of Physics and Technology, AS UkrSSR, Kharlkov)
SUBMITTED: August 1, 1960
Card 3/5

S/126/61/oli/ooi/o05/019
Elll/E452
~AUTHORS: Gindin,_I.A Lazarev, B.G. and Starodu~ov, Ya_,D,,
~TITLE: Low-Temperature Metallography of Lithium
'PERIODICAL: Flzika metallov i metallovedeniye, 1961, Vol
.111 No.1,
pp.46-5i
mation is yet available
'TEXT: The authors point'out that no infor
;on microstruct%Aral changes during martensitic transformation of
metalsvUn cooling to low- tempera ture a and heating or after
"Ideformational" polymorphic transformation; or on the mutual effecti
of transformations on microstructure. In their present
'investigation, which in a continuation of their work in this field,
the authors have hylSthe
studied by low-temperature metallograp
microstructure of lithium and its changes in the polymorphic-
transformation temperature region. Polished sections were
prepared as previously described (Ref.1). For preliminary low
'temperature investigations, previously prepared lithium specimens
Z ;(Ref.1) were used; these had been stored in liquid nitrogen and
photomicrographs corresponding to this temperature could then be
mobtained directly. For other temperatures, a special cryostatic I
apparatus~was constructed in which the required specimen to'
mperature~
Card 1/ 3-

........... .s/l26/6i/oii/ooi/005/019_-__
E iai /E 4 5 2
phy of Lithium
~'Low-Temperature Metallogra
*was obtained by suitable selection of thermal resistance between it
n
and a massive copper heat conductor whose other end was immersed i
cooling liquid. The temperature of the 7 x 7 x 2 mm specimen,
which could be microscopically observed, was measured with a
copper-constantan thermocouple or, for below 200K, with an indium
resistance thermometer. The.whole was inside a vacuum jacket
connected to a separate pump and containing activated charcoal.
The optical system was part of a type nMT-3 (PMT-3) apparatus with
a photographic attachment. Microphotos show the original room
.temperature microstructure and also needles of the hexagonal
modification and a chain of martensitic needles with a grain-
boundary fracture. The extent of martensitic transformations does
not exceed 25 to 30% and volume changes produce shear deformation.
further figure shows the, changes from the original microstructure
at a given point on the section during repeated cooling and warming.
Preliminary plastic deformation at 780K was found to impede
formation of the hexagonal modification on subsequent cooling below
the martensitic point;. on the microstructure, wavy slip lines are
visible which represent regions of localized face-centred cubic
Card
I

S/126/61/011/001/005/019
E11l/E452
Low-Temperature Metallography of Lithium
structure. This effect is similar to that in body-centred cubic
(Ref.11). The work provides some confirmation for the.,
(Ref.1) on the behaviour -of. li.M 'in.
authors' previous conclusions 00,
e low-temperature improvement of the mechanical proper 0
two-phase
this metal is attributable to the fine dispersion of the
structure produced through "deformationallf polymorphous change.
There are 6 figures and 11 references: 8 Soviet and 3 non-Soviet.
ASSOCIATION: Fiziko-telthnicheakiy institut AN UkrSSR
~Physicotechnical Institute AS UkrSSR)
SUBIMITTLD: June 28, 1960

22966
s/126/61/011/005/014/015
E193/E183
AUTHORS: Gindino I.A., Starodubov, Ya.D., and Vasyutinskiy, B.M.
TITLE: Plasticity and brittleness of cast molybdenum at
temperatures between 4.2 and 700 OK. 1.
PERIODICAL: Fizika metallov i metallovedeniye, Vol.11, NO-5, 1961,
PP. 794-8oo
TEXT% The object of the present investigation was to explore
the possibilities of low-temperature application of refractory
metals such as Mo, Cr, W, Nb, etc. To this end, the mechanical
properties of Mo were determined by means of the standard tensile
test at 4.2-700 OK, and the effect of preliminary heat- and
mechanical treatment on the transition temperature from the ductile
to brittle fracture was studied. Mo of 99.95% purity was used in
the experiments, the main impurities consisting of (%)a 0-005 Fes
0.01 Ni; 0-017 Ca' 0.002 Al; 0.002 0; 0.0009 N; o.ooo6 H.
To ensure uniform grain size, the ingots cast in vacuum-are furnace
were hot-rolled at 1000 OC to 50% reduction in thicknessq spark-
machining having been used for the preparation of flat, tensile
test pieces of 7 mm gauge length and 2 mm2 --ross-section.
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Plasticity and brittlanoBs of cast ..... E193/E183
After machining the test pieces were vacuum-annealed at 1280 OC.
This treatment reduced the gaseous impurity content and produced a
coar:ely-crystalline structure with the average grain size of
200- 00 ii. The tensile tests were carried out at 4.2, 20o 77c 18_31!
200, 223, 243, 300o 435 and 700 OKI at two rates of strain, 0.4 and
30 ii/sec. Some of the results obtained at the rate of strain of
0.4 o/sec are reproduced in Fig.3, where the yield point (aa)0
U,T.S. (0b) and the true tensile strength (a ) measured in kg/mm2
are plotted against the test temperature (00. It will be s*an that
all these properties increase with decreasing temperature. The
point of intersittion of the a. and Ob curves determined ths
transition temverature from ductile to brittle fracture, which in
this case was 183 OK. The unusual feature of curves shown in Fig.3
is that they all pass through a maximum at approximately 80 *-K.
since it is generally believed that the tensile strength in the
brittle fractural region does not depend on temperature. With
increasing rate of strain, both a. and Ob increased, and the
temperature of the transition from ductile to brittle fracture was
shifted to 208 OK. The plastic properties of Mo have been found to
decrease with decreasing temperature at a rate which increases with
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Plasticity and brittleness of cast .... E193/E183
increasing rate of strain. This is illustrated in Fig.5, where
elongation (b, %) and reduction of area (4,, Yo) are plotted
against the test temperature (OK) for specimens extended at 0.4
(open circles and squares) and 30 p/sec (black circles and
triangles). In the second stageof the present investigation, the
tensile test pieces were subjected to the following treatment:
(1) loading at room temperature and at a rate of strain of 0.4 P/sec
to attain a stress equal to 0.5 as; (2) slow cooling under
constant load to 77.2 OK and holding at that temperature for 1-1.5
hours. It was found that after this preliminary treatment, the test
pieces tested at 183 OK (i.e. at the critical temperature) exhibited
some degree of ductility (6 MO. Fig.6 shows the actual load (kg)
versus strain (-~i) curves for Mo tested at 183 OK at a rate of
train of 0.4 p/sec for untreated (curve 1) and treated (curve 2)
:
pecimens. In Fig-7 the elongation (6, %) of untreated(curve 1) and
treated (curve 2) test pieces is plotted against the test
temperature. It was found also that no significant improvement in
ductility can be achieved by cooling the metal (during the treatment
described above) to temperatures lower than 77 OK. An increase in
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Plasticity and brittleness of cast ... E193/E183
the low-temperature ductility of iron, subjected to similar
treatment, has been attributed (Ref.13 Gindin, I.A., FMM, 196o, 9,
447) to the formation of twine with dislocation-free boundaries.-
In the case of molybdenum, the present authors postulate, the VX
increased ductility attained by this treatment in associated mainly
with the stress-dependence of the temperature coefficient of linear
expansion and with the changes in the mosaic structure of the metal
,subjected to stresses at low temperatures.
There are 8 figures and 8 references: 6 Soviet and 2 non-Soviet.
The English language reference reads an follows;
Ref.6t J.H. Bechtold, J. Metals, 1953, 5, 1469.
ASSOCIATION: Flziko-tekhnicheskiy institut AN USSR
(Physico-technical Institute, AS Ukr.SSR)
SUBMITTED: August 15, 1960
Card 4/6

~og, 220C, V-119, 111,IG S/126/61/012/001/015/020
25923 E193/E480
AUTHORS: Gindin, I.A., Staradubov, Ya.D., Vasyutinskiy, B.M.
TITLEt Metallographic investigation of molybdenum deformed in
tension at 4.2 to 700*K. II
PERIODICAL: Fizika metallov i metallovedeniye, 1961, Vol.12, No.1,
pp-132-139
TEXT: Many of the metalki_~Iwijth body-centred cubic lattice undergo
a ductile-to-brittle transition.at sub-zero temperatures. It is to
be expected that as the temperature of this transition is approached
changes occur not only in the mechanical properties of the metal
but also in its microstructure. Since no study of molybdenum at
temperatures lower than 770C had been reported, the investigation,
the results of which are described in the present paper, was
undertaken with the object of studying the microstructure of
molybdenum deformed in tension at' 4.2 to 7000K. Both optical and
electron microscopes were used in the examination of the specimens.
No etching was used, the changes in the microstructure on the
preliminarily polished specimen surface having been revealed with X
the aid of a microinterferometer, Qualitative assessment was made
of the density of slip bands, degree of uniformity of deformation
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5/126/61/012/001/015/020
Metallographic investiOMn E193/E480
in different grains, mean magnitude of absolute displacement in
slip, and the dependence of these characteristics on the
temperature and degree of plastic deformation was evaluated. The
results can be summarized as follows. (1) At all temperatures at
which molybdenum remains plastic (that is down to 1830K) it deforms
plastically by the mechanism of slip. As in other body-centred
cubic metals, branched slip lines are formed on molybdenum,
indicating a more complex mechanism of deformation than that
obtaining in face-centred cubic metals. This shape of the slip
lines can be observed already in the early stages of plastic
deformation corresponding to an elongation of 6 = 1- 2%. The
effect becomes more pronounced with increasing degree of
deformation at any given temperature but the effect of heavy
deformation is most pronounced near the ductile-to-brittle
transition temperature. Fig.2 shows (magnified 330-fold) the
microstructure (a) and the interference pattern (b) of the slip
bands formed on molybdenum deformed at 200*K to 6 . 0.8%; the
magnitude of the absolute slip was in this case approx 0.25 P.
In suitably oriented grains (particularly at high temperatures) a,
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Metallographic Investigation ... E193/E48o
system of inter"cting slip lines Is formed, Increasing the
degree of deformation of molybdenum at 240 to 700*K brings about the
appearance of new slip bands and an increase in the displacement
along the slip planes. The development of the process of
deformation, however, is manifested predominantly by growth of the
initially-formed slip bands. Thus, for example, just before the
fracture of a specimen (6 - 38%) at 700*K, the slLp bands may
become 6 to 7 ji wide. The density of the slip lines also changes
with temperature. At 7006KI it is relatively small and slip bands,
spaced at 12 to 15 IL, predominate. At 300'K, the density of slip
bands corresponding to the same degrees of deformation is higher,
the width of the slip bands and the spacing between them decreasing.
With a further decrease in temperature, the density of slip bands
again decreases approaching that obtaining at 700*K.
.(2) In addition to deformation by slip (as revealed by the
formation of slip bands) plastic deformation of molybdenum at room
temperature entails a specific mode of deformation, localized at the
grain boundaries and in the grain-boundary regions, This
mechanism operates at relatively low strains (3 to 5%). With
increasing strain some of the regions of localized deformation grow
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Metallographic investi'VI'Von ... E193/E48o
in size and cracks are formed at the boundaries of these regions
after heavy deformation. The width of these near-boundary regions
can reach 25 to 30 1,1, the relative displacement of adjacent grains
along the grain-boundary being several tenths of a -p. This mode
of plastic deformation which has been observed in pure iron at
sufficiently low temperatures (Ref.4. Glindin I.A. and
Starodubov Ya.D. FTT, 1959, 19 1794) appears to be a property of
pure metals. The m1crostructure and interference pattern of the
grain-boundary and the grain-boundary region of molybdenum,
deformed at 300*K to 6 w. 20%, is shown in Fig.5a and 5b respe-atively
(magnified 440-fold). (3) With decreasing temperature the
character of plastic deformation changes considerably. At
temperatures approaching the ductile-to-brittle transition,
fragmentation and block formation precede the appearance of slip
bands. The formation of blocks (whose size, determined wi h the
aid of an electron microscope, was found to be (2 -3) x 10-h 0m)
increa:4es the resistance of molybdenum to slip and twinningl the
process of deformation becomes less uniform and fracture takes place
at relatively small strains. (4) In contrast to other metals with
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Metallographic investigWon ... E-193/E480
body-centred cubic crystal structure, twinning plays a relatively
insignificant part in the plastic deformation of molybdenum. Thin
twins (1 to 2 1~ thick) appear in specimens deformed below 246*K
but only in isolated grains. An electron mi;:rophotograph
(magnified 11250 times) of a twin (approx 0.5 P thick) in
molybdenum deformed at 200*K to 6 a-2% is shown In Fig.8.
A: specific characterlatic of twins of this type is the presence of
lightly and heavily distorted zones showing, respectively, as dark
and light bands on the microphotograph. It Is postulated that the
highly distorted zone is formed suddenly when a certain stress,
required to initiate the process of twinning, is reached. The
appearance of this zone in accompanied by the formation of a mosaic
structure in the boundary region and by the formation of blocks and
their elastic recovery. As in the case of Iron, growth of a twin
in molybdenum takes place by movement of one of its boundariesi
on reaching the distorted region, the growth of the twin ceases
owing to the strain-hardening of this zone. (5) The specific
character of plastic deformation of molybdenum is reflected in the
manner in which this metal fractures. At 300 and 700*K fracture
takes place along the slip planes and a well-defined ne,~-k is formed
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Metallographic investigation ... E193/E480
in a tensile test piece. Cracks along the slip planes appear
also in molybd:enum, tested at 240'K, but in this case they are
accompanied by cracks along the cleavage planes, the number of
these cracks increasing with decreasing temperature, This is
illustrated in Pig.9 (magnified 440-fold) showing a portion of a-
test piece deformed at 243*K to 6 ,.18% In which the parallel slip
lines end at a crack along the cleavage plane. Or. approaching the
ductile-to-brittle-tranaition temperature, and particularly below
it, cracks along the grain- and block-boundaries are formed. Side
by side with the main crack a number of cracks parallel to it but
not traversing the entire cross-section of the test piece can be
observed. Fracture below the critical temperature Is both trans-
and inter-crystalline, although the latter is relatively less
pronounced. The decrease in strength of molybdenum below 27*K
has been attributed to the formation of a large number of surface
cracks which cause premature fracture. The formation of the
surface cracks is, in turn, associated with a high concentration of
oxygen in the surface layer. It was concluded from the results of
the present investigation that the character of plastic
aeformation of 99.95% molybdenum in the temperature interval
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25923 S/126/6'1/ol2/001/015/020
Metallographic investigation E193/E48O-
,studied changes considerably with decreasing temperature. In the'i
plastic range deformation trans-crystalline slip predominates; at
room temperat ure this mode of deformation is accompanied by.
localized deformation in the grain-boundary regions. On
approaching the ductile-to-brittle transition temperature, block-
formation plays an increasingly important part and is ma.inly.
responsible for the absence of twinning at low temperature.
Ductile fracture at 240 to 700*K takes place along.the slip 15IAnes
At lower temperatures, cohasion of the metal is destroyed in the
early stages of the deformation and the main crack develops along-
the block boundarles. There are-10 f1gures and 9 references.
5 Soviet and 4 non-poviet. The four references to English
language publications read as follows: Chen N.K., Maddin R.-
Trans. AIME, 1951,,igi, 461; Andrade E.N., Chow J.S. Proc.Roy.
Soc., 1940, 175A,.2'90; Cahn R.W. J.Inst. Metals, 1954-55,
a3, 49j; Rendall ~.H., Johnstone'S.T.M.., Carrington W.E.
J.Inst.Metals, 1953*-54, 82, 345.
ASSOCIATION: Fiziko-tekhnicheskiy institut AN UkrSSR
(Physicotechnical Institute AS UkrSSR)
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30h56
S/126/61/012/003/016/021
E193/El35
AUTHORS: Garber, R.I., Gindin, I.A., and Shubin, Yu.V.
TITLE: Tensile tests on beryllium single crystals in the
20-500 OC temperature range. V.
PERIODICALS 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 text pieces in shown
in Fig.1, where p indicates the direction of the applied stress.
A strain rate of 0.005%/sec 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 p., kg/mm2, left-hand scale)
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Tensile tests on beryllium single ... S/126/61/012/003/016/021
E193/EI35
and elongation and reduction of area (b and q), %, 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 = (I - y) 100 OC,
where y denotes the deformation localised in the 5lip 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)s = Lecos 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
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E-193/EI35
relative slip, y, and density of the slip bands theme two
parameters being given by y = b/as and e I~he'(for the
meaning of b/a. and h see Fig.1). in t~e regions of
uniformly distributed slip lines, y increased from 0.4 at 20 OC
to 2.0 at 500 OC; 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 11-g at
200 OC after which it decreased again, reaching at 400-500 OC a
value similar to that at room temperature (- 0.3 1/0- Analysis
of the results of mechanical tests, correlated with the
examination of slip bands and microstructure of specimens after
fracture, led to the following conclus�ons. 1) Plasticity of Be
single crystals increases monotonically with rising temperature,
showing no peak at 400 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
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Tensile tests on beryllium single ... S/126/61/012/003/016/021
E19YE1315
large magnitude of y (about 70). Both UTS and the so-called
strain-hardening_modulus 15 passed through a maximum at 200 OC;
U is given by D = (pu - ps)6, where pu is the true UTS of
the metal. This effect is a manifestation of the simultaneously
occurring processes 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 [11-i03 direction. At higher temperatures,
prismatic slip alorg the 1101X3 plane in the general Cllk3
direction and diffusion deformation play an increasingly important
part. 3) Brittleness of Be single crystals at room temperature
~Ls 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 temperatiires, slip becomes more uniform
and deformation takes place partly by prismatic slip.
There are 10 figures, 1 table and 1 Soviet-bloc reference.
ASSOCIATION: Fiziko-tekhnicheakiy institut AN USSR
(Physicotechnical Institute, AS Ukr.SSR)
SUBMITTED: January 2, 1961
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S/i26/61/012/oo6/007/023
E193/E383
AUTHORS: Gindin, I.A., Lazarev, B.G., Starodubov, Ya.D. and
__L~azareva, M.B.
TITLE: Mechanical properties of sodium in the range of low-
temperature polymorphic trans(formations
PERIODICAL: Fizika metallov I metallovedeniye. v. 12, no. 6,
1961, 846 - 852
TEXT: As is the case with Li, the body-centred cubic
crystal structure of Na undergoes a partial change to close-
packed hexagonal on cooling below 35 0K. A so-called
"deformation" modification of this metal can be obtained by
straining it plastically at temperatures below 80 0K and the
object of the present investigation was to check whether the
effect of low-temperature polymorphism of Na on its mechanical
properties is similar to that observed earlier by the authors
(Ref. 1: Fmm, 196o, 10, 472) in Li. 0 To this end, tensile
t-ests were carried out at 1.6 - 290 K on polished and etched
test pieces of 99.8% pure Na and the following properties were
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Mechanical properties of .... E193/E383
determined: 0.2% proof stress-, UTS; true tensile strength-
elongation; reduction in area and the strain-hardening
coefficient. In addition, the microhardness of each fractured
specimen was measured at 77 0K, side-by-side with that of a
pilot (i.e. untested) specimen. Typical results are reproduced
graphically. In Fig. 2, the elongation (6, % - lefthand scale)
and reduction in area (Y , % 0righthand scale) are plotted
against the test temperature K). The temperature-dependence
of 0.2% proof stress (d'. ), UTS and tru. tensile
0 2
strength (ce Is reproduced in Fig. 3. Finally, in Fig.
u 2 0
the microhardness ~H, kg/mm ) measured at 77 K is plotted
against the temperature ( 0K) to which the test piece had been
cooled prior to hardness test,, the lower curve relates to
pilot specimens, the upper curve representing results obtained
near the neck of fractured tensile-test pieces. Several
conclu'sions were reached.
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Mechanical properties of ... E193/E383
1) Anomalous variation of mechanical properties of Na in the
sub-zero temperature range is associated with polymorphic
transformations taking place at these temperatures.
2) The martensitic transformation which on cooling takes place
in Na at about 350K is reflected in a sharp increase in its
yield strength, UTS and microhardness.
3) A minimum in the elongation versus tempevatuve eux-ve is
situated in the temperature range within which the deformation-
induced polymorphic transformation takes place. The rapid
increase in elongation on cooling from 70 to 1.6 OK can be
attributed to the deformation-induced change from body-centred
cubic to close-packed hexagonal crystal structure.
4) The low-temperature polymorphic transformations
(particularly the martensitic transformation) bring about an
increase in the degree of strain-hardening and,uniformity of
the plastic flow of Na. There are 4 figures.,
I table and
12 referqnces. 6 Soviet-bloc and 6 non-Soviet-bloc. The
four latest English-language references mentioned are:
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S/126/61/012/oo6/007/023
Mechanical properties of .... EJ93/E383
Ref. 2- C.S. Barrett - Phys.Rev.; 1947, 72, 245; Acta
crystallog., 1956, 9, 671z Ref. 8: D. Hull, H.M. Roserbergs
Phys.Rev.Let., 1959, 2, 5-, Ref. 1.0.- D. Hull, H.M. Rosenberg
Phil.Mag., 1959, 4, 303; Ref. 12- D. Gugan, J.S. Dugdall,
J. Can, Phys. Rev., 1958,-36, 1248.
ASSOCIATION.
SUBMITTED-
Fiziko-tekhnicheskiy institut AN UkrSSR
(Phys:icqtechnical Institute of the AS UkrSSR)
May 3, ig6i
Card 44 (f//

S/05 61/074/001/001/003
B117YB212
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 aSBOCiated 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-
oiear 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 glance at the material available shows that great progress has been made
in the analysis of high-purity metals. The most urgent task at present
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Physical properties of ... B117/B212
veem 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 considerEdto be
proved. The mechanical properties are very sensitive toward additions,
especially with respect to structural changes occurring during cryotalliza-
tion or other thermal proccesea. Vacancieo 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: Alt Bat Bet Vt W, Bit Ga, Hat Pe, Au, In, Cd,
Ka, Ko, Mg, Mn, Cut Mot Nit Nb, Pt, Sn, Pb, Ag, Sr, Sb, Ta, Tit Th, U, Cr,
Zn' and Z.r- The following Soviet authors are mentioned: L. S. Kan, B. G.
Lazarev rRef-1: DAN SSSR 81, 1027 (1951); V. B. Zernov, Yu. V. Sharvin
(Ref-7: ZhETF 36, 1038 (lT5_~); B. N. Aleksandrov, B. I. Verkin (Ref.S:
ZhETF 34, 1655 T1956); A. I. Sudovtsov, Ye. Ye. Semenenko (Ref.18: ZhETP
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S/05 3/61 /C)74/()01/()01/003
Physical properties of .4 B117/B212
.35-, 305 (1958); 1. M. LifLhits, M. Kaganov (Ref.29: UFN 69, 419 (1959);
B. Leks (Ref-30-- UFN _70,:111 (1960); A. S. Zaymovskiy, G. Ya. Sergeyev,
V_V . Titova, B. M. Levitakiy, Yu. N. Sikurskiy (Ref-341 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.
6o, Voprosy fiziki metallov i metallovedeniya, sb. no. 9, Kiyev (1959) str.
185); V. A. Pavlov (Ref.64: Piz. metallov i metallovedeniye A, 1 (1957);
V. A. Zhuravlev, (Ref.72: Zavodskaya laboratoriya a, 687 (1959); V- S-
Yemellyanov, A. I. Yevstyukhin, D. D. Abonin, V. I. Statsenko, ("Metallurgi~a
i metallovedeniye chistykh metallov" vyp. 1, 1959, 44). There are 18 fig-
ures, 7 tables, and 144 references: 61 Soviet-bloc and 83 non-Soviet-bloc.
The six references to English-language publications read as follows: D. J.
Maykut, Prod. Engineering 24, 186 (1953) - Ref-31); A. N. Holden, Phys.
Metal. of Uranium Massachus.~ 19581 str. 7 tf.33); J. C. Blade, Rev.
metallurgie.~A, 769 (1957) (Ref.50); P. Gordon, J. Metals 1, 1043 (1955);
(Ref-51); C. Zenert Phys. Rev. JA, 639 (1948) (Ref.6a); T. R. Barrett,G. G.
Ellis, R. A. Knight, Proc. See. Int. Conf. Geneva 5-, 319, 320 (1958) (Ref.
100).
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S/181/62/004/002/027/051
B101/B102
AUTHORSt Gindin, I. A,, Kozinets, V. V,., and Starodubov, Ya. D,
TITLE& Comparison of structural changes in nickel causedhy
deformation at 4.2 and 300 0K and by subsequent creeping
PERIODICAM Fizika tverdogo tela, v. 4, no. 2, 1962, 465-469
TUT i Experiments with high-purity nickel (99.994%) tempered at 8000C and
3,10 _6 mm Hg and subsequently deformed by 3.5% at 4.2 or 3000K by stretching
are reported. Some of the specimens were subsequently kept at room
temperature for 80 - 100 hrs and subjected to creep tests at 7000C and
constant pressure (2.8 kg/mm 2), while others were heated from 4.20K to
7000C within 1.5 - 2 min and likewise subjected to creep tests. Both
stretching and creeping were carried out with machines described in M;
794, 1959~ A sharply focused X-ray tube, designed by B. Ya. Pines
Olstrofokusnyye rentgenovskiye trubki i prikladnoy rentgenostrukturnyy
~
analiz (Sharply Focused X-ray Tubes and Applied X-ray Analysis) GITTL,
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Comparison of structural changes in B101/B102
1955) was used to examine the X-ray structure of the specimens. The
disorientation waa calculated according to P. B. Hirsch (see below).
Resultsi The original specimens possessed large subgrains (80/t), the
lattice was not distorted, and the disorientation was less than 10.
Disorientation reached 8 0 at 4.20K, but was less at 3000K. Specimens
deformed at 4..20K underwent relaxation when heated to room temperature.
The distortion of the lattice decreased as e result of polygonization of
the subgrain fragments. Microdistortions diminished further on heating to
creep temperature. The specimen deformed at 4.20K and subsequently kept
at room temperature had a more uniform and more disperse structure than
the specimen heated directly from 4.20K to 7000C. The removal of
microdistortions of the specimens, especially of that deformed at 4.20K,
and the increase in disorientation during the creeping process, indicate
that the substructure depends on the temperature at which deformation has
taken place. There are 2 figures and 9 referencest 8 Soviet and 1 ncn-
Soviet. The reference to the English-language publication reads as
followst P. B. Hirsch, J. N. Kellar, Acts, Crystal., 5, 162, 1952~
Card 2/3

S/181/62/004/002/027/051
Comparison of structural changes in B101/B102
ASSOCIATIONt Fiz'Lko-tekhnicheskiy institut AN USSR, Khar1kov
(Physicotechnical Institute, AS UkrSSR, Kharlkov)
SUBMITTEDs September 22, 1961
z
-1
Card 3/3

GINDIN. I.A.j KOZINETSO V.V.1 STARODUBOV, Ya.D.; IWOTKEVICH, V.I.
Structural changes in copper depending on low-texperature
deformation and subsequent annealing. Fiz.met.i metalloved,, 14
no.6s864-873 D 162. (MIU 16#2)
1. Fiziko-tekhnicheskiy institut AN Ukr6SR i Kharikovskiy
gostdirstvennyy universitet. I
(C-opper-Metallography)
(Metal, Effect of temperature on)

S/032/62/028/001/014/017
B116/B108
AUTHORS: Garber, R. T-A., Neklyudov, I. M.,
Chechellnitskiy, 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 peogramming the load on samples.
It permits determining the effect of the gharging rate on the material.
properties up to 800 0C in a vacuum of 10- mm H or in inert gases2
The charging rate can be increased from 10 g1mm per hr to 3 kg/mM per 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 of
0.5 0 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 follo%s: Dynamometer spring (6) is compressed by the
reducing gear (7). The charging rate is regulated by varying the
periodic operation of the motor (a) (PA-09 (RD-0g)-type) driving the gear
Card 1/3

S/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 )HA-12 (EPD-12) electronic potentio-
meter. There are 4 figures and 6 Soviet references.
ASSOCIATION: Fiziko-tokhnicheskiy institut Akademii nauk USSR (Physico-
technical Institute of the Academy of Sciences UkrSSR)
Fig. 1. Diagram of device for programmed hardening.
Legend: (1) samole; (2) and (3) fastenings; (4) cross piece; (5) three
bars; (6) dynamometer spring; (7) reducing gear; (8) motor; (9) ball-
bearing joint; (10) indicator; (11) mains connection; (12) base plate;
(13) vacuum chamber; (14) sylphon; (15) limiter; (16) to pump.
Card 2/3

. ; I .. . . . . -. S/O~, 62/6~/6611014/dif
Devibe for programmed metal .hardening B11 ~,IbS
---I
1.

GARBERP R.I.; GINDIN I A - 14ALIK N.I.; STARODUBOV Ya.D.
.1 J,
Machine for testing materials for tension and compression at the
temperatures from 1p/+ to 1500 K. Zav.1ab. 28no.7:865-868 162.
(MIRA 15:6)
1. Fiziko-tokhnichoskiy inatitut AN USSR.
(Testing machines)

37382
S/02 62/143/006/011/024
A 2A6 0 B164YB101
AUTHORSt Gindin, I. A.,__Starodubov, Ya. D., and Azhazha, V. M.
TITLE: Increase of the creep resistance of nickel by prior
deformation at 4.20K
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 143, no. 6, 1962,
1325-1327
TEXT: The effect of small deformations of nickel at 4.20K on its creep
resistance at higher temperatures was examined by tempering small
specimens of high-purity nickel (99-994%) in vacuo at 6000C and then
drawing them at 4.20K, the rate of drawing being 0.03 mm/sec and the
degree of deformation 1.7 or 3.50/16, afterward establishing the creep
curves under a constant stress of 2.6 kg/MM2 in vacuo at 7000C. For
comparison, tempered specimens which had been deformed at room temperature
were used as standards. An increase in creep endurance from 40 to 106 hra
(after 3. Vo deformation) and a 4-5-fold ircrease in creep strength were
obtained. Specimens prestrained at 3000 C gave much lower values
amounting to 51.5 hra and to a 1.37-fold increase, respectively.
Card 1/2

S/020
,/62/143/006/011/024
Increase of the creep resistance, B164/B101
Microphotographs of the specimens show that those deformed at 4.2 0K
present greater homogeneity of fine structure than the others. There
are 2 figures and 1 table.
ASSOCIATION: Fiziko-tekhnicheskiy institut Akademii nauk USSR
(Pbysicotechnical Institute of the Academy of Sciences
UkrSSR)
PRESENTED: January 26, 1962, by 0. V. Kurdyumov, Academician
SUBIMITTED: September 22, 1961
Card 2/2

ACCESSION NR: AT40~3981 6/3070/63/000/000/0116/0118
AUTHOR: Gindin, 1. A.; Starodubov, Ya. D.
- Device for metallographic and radiographic investigations of the structure of solid
TITLE.
bodies during deformation at low temperatures
SOURCE: Novy*ye mashiny*i pribory*dlya ispy*tanlya metallov.6bornik statey. Moscow,
Metallurgizdat, 1963, 116-118
TOPIC TAGS. low temperature metallography, low temperature radiography, micro-
photography, deformation, metal deformation
ABSTRACT: Devices described'in the literature are intended either for determination of
mechanical properties of solid bodies at low temperatures, or for loW-temperature metal-
lography. However, these devices do not permit direct observation'of changes in structure
of a specimen during the process of Its stressing at low temperature& Metallographic and
usually radiographic investigations of structure of deformed specimens are performed after
the specimens have regained room temperature, despite Irreversible changes In them. A
device has been developed by the authors permitting observation, photographing and taldng
of motion pictures of changes on the surface of a specimen during cooling, deformation at
C ard 1/7

ACCESSION NR: AT4013981
0,
low temperature, and subsequent heating. The device in also suitable for radiographic
investigations of structure in solid bodies during cooling, low-temperature deformation, and
heating. The design of the device permits cooling a specimen down to approximately 10K,
measuring this temperature, deforming a specimen in tension or compression, and simul-
taneously recording values for the "load-deformation" diagram. A schematic illustration of
the device is given in Fig. 1 of the Enclosure. The test specimen 1, in the form of flat
plate enlarged at Its ends, is gripped by jaws 2 located In a depression' of the mounting table.
One of the jaws is fixed to the table; the other is connected to rod 3 of the loading mechanism
and is guided by grooves in the table. The cooling of the specimen to the required tempera-
ture is provided through a copper conductor 4 (25 mm in diameter), the low6r part of which
is immersed in a liquid coolant contained in the -acuum-bottle 5. In order to increase the
cooling rate and to reduce the temperature difference between test specimen and coolant,
circulation of the coolant is provided through an axial bore in the conductor 4 and tubes 6
and 7. For regulation of the specimen temperature and of the- cooling rate, a resista ' e
8 is provided and a heater 9 in the lower part of the mounting table. The specimen t(
perature is measured by a thermocouple or a pick-up resistor. The wire connections
the -temperature pick-up pass through vacuum insulators 10. The mounting table with ~fe
Card 2,N.

ACCESSION NR: AT4013981
specimen and part of the cooling conductor are located in a vacuum test chamber 11. The
upper part of the chamber is flanged for connection with cover 12. Observation and photo-
grapli ng of the specimen microstructure during the test are conducted through a window in
the cover. For observation and photographing of specimen surface changes, the optical part
of the device PMT-3 with & photographic attachment are used; and for taking motion pictures,
the "Kiyev"-type camera. To avoid condensation of moisture on the specimen, high vacuum
is applied to the test chamber 11 by an adsorption-type pump through the hose connection 14.
The vacuum is maintained by a thin layer of activated charcoal 15. A copper s6ield is pro-
vided for heat protection of the specimen. The loading device consists of a worm gear re-
ducer 1G, driven by the electro-motor 17. The worm gear is mounted on a threaded spindle
rotating freely in bushing 18. The bushing is fixed in body 19 of the loading deviceand
takes the thrust during loading of the specimen. The thrust from the spindle is transmitted
to a moving cylinder 20, closedfrom one side and con4dning the calibrated loading spring 0
er 20 and from the other side on a flange
21, acting from one side on the bottom of the cylirr
connected to the rod 3 of the movable jaw 2. , To a thicker part in the central portion 9f the
rod 3, a bellows 22, having a working stroke of 12 mm, is soldered. The working pins of
two'dial gages 23 tie to rod-3. The left gap (see Fig. 1 of the Enclosure) is fixed to ~he
body 19 of the device and serves for measuring the absolute elongation (or shortening) of
the specimen. The right gap in fastened to the movable cylinder 20 through a plate 24, 'and
Card 3P

ACCESSION NR: AT4013981
measures the deflection of spring 2 1, 1. e. , the load applied to the specimen. A yoke with
three ribs 25 provides greater bending stiffness to conductor 4. The specimen is subjected
to a constant-speed axial deformation of 0. 03 mm/sec, and a maximum load of 200 kg can
be applied. For X-ray investigations at low temperatures, a small chamber. for Aotograph-
ing by reflection has been devised (see Fig. 2 of the Enclosure), which can be flanged to the
test chamber and scaled by a rubber gasket A beryllium window 2, 12 mm in diameter and
0. 3 mm thick, is used to introduce the X-ray beam Into the test chamber. Inside the cham-
ber, a magazine-with film 3 is mounted and a sector-screen 4 of lead underneath the magazine.
The screen permits taking four X-ray pictures without disturbing the vacuum in the cbamber,
and consequently without heating the specimen. The screen has to be rotated 90" after each
exposure. The height of the film magazine location over the sample is adjustable. For
making of radiograms, A sharp-focus~ed X-ray tube designed by B. Ya. Pines is u&ed. A
photographic camera can be installed to take microphotographs and radiograms of the same
spot of the sample. The residual pressure in the vacuum chamber is 10-6 to 10-6 mm Hg.
The temperature of the specimen dependis an the coolant used and is 78K with liquid nitrogen,
,26K with liquid h'drogen, and 10K with liquid helium. Orig, art, has , 2 figures, -
ASSOCIATIOM *IZIko-tekbs1chox* JrAl4tut AN \tMR (bodwo of ftyste's nit Tooko
nology AN USSR)\
Card 4/7

ACCESSION NR: AT4013981
SUBMITTED. 00 DATE AM 20F~b64 ENCL: 02
SUB CODE: MM NO REr BOVt 010 OTHER: 000
Card 5/7
~'- 7-W
_4
mll
Ep
Rpm

ACCESSION NR:. AT4oiaaal
UOUP.E. 01
Fig. 1. Devic~-~ for inechankal tooW, mown pf and X-ri ms at
low tomperabum
Card 6/7

ENCLOSURE: 02
:'ACCESSION NR: AT4023981
00,
Fig. 2. Chamber for X-ray investlPHOR Of struchm of solids under deformation at klm,
temperatures. 1 - body of duurJ*r, 2- berYlihnn window, 3 - magazine
X-ray tulm, 7 - jaw for I g of
4 - sector screen (leac%. G test specimm4 6 -
specimen, 8 i.- shield
Card-
7P

BPF(~)--2 .1p. )'/FY~T(m) __AFPTC/ASD/
PM(l
55D Pu-4 -tM ......
ACCESSION NRS AP3002746 6/6-126/ ~~1000iod~10169' -
10 71
AUTHOR% Gindin, L A.a Kraychenko, S. F. �tarodubov, Ya. D.t Godzhaev, V. M.
TITLEr Outfit for studying metal oreop at low temperatures
SOURCEt Pribory* i'tekhnika eksperimela, no. 3, 1963, 169-171
TOPIG TAGSt metal creep, low-temperature creep
~p
ABSTRAM A now djesign of the outfit forstudying metal cree within 300-4.QZ
iat a 100-kg maximum load is described. The outfit comprises: 1) a mechanism for
loading the specimen,,(2) a high-sensitivity mechano-optical primary detec
program
tor of small deformations (3) an optical device with a calrera for recording the
:elongation-time chart, (4~ a liquid-level controller for the Dewar vessel, and
b)-clamps for fastening the specimen. A functional diagram illustrates operation of.'
the outfit. The following characteristics are given: rate of loading is 2.5 kg/min;-
deformation-time scale factor is 0.5 micron in 1 mm. of the elongation axis or 30,
60, 120 min in 1 mm of the time axis; average daily variation of the light spot
about the horizontal time axis is 0.5 micron; lever sensitivity is 0.1 r'Acronjg;
specimen diameter is 1, 2, or 3 mm-, specimen length is 130 mm; error in deformation
Association: jWA=TM=11M Physico-Tachnical Inst. AN UkrSSR
Card 10i

GARB&R) R.I.; GIUDIN, I.A.; CHIRKINA, L.A.
Twinning and annealing of nonequilibrium iron-nickel alloy of
the Sikhote-Alin iron meteorite. 14eteorLtika no.23:45-55 163.
OURA 16:9)
(Sikhote-Alin Range-41ateorites)

GARUR, R..I.; GIMIN I.A.; SHUBDI, Yu.V.
- Codipreousion of beryllium single crys,tals along the hexagonal axis
in the tem*ature range 4.2 to 9000 K,. Fiz. tver. tela 5 no-621
434-442 F 163. (mu 1615)
(Berylli= crystals) (Strength of materialo)

GINDIN, I.A.; KRAVCHEMKOp S.F.; STARODUBOV, Ya.D.; GODZHAYEV, V.M.
Apparatus for studying the creep of metals at low temperatures.
Prib. i tekh. eksp. 8 no.3sl69-171 I~y-Je 163. (MIRA 16:9)
1. Fiziko-takhnichaskiy institut AN UkrSSR.
(Creep of metals) (Metals at low temperatures)

GARBER, R.II_0,_.21?IDjN, 1,A.; STOLTAROV, v.M.; cHECHFL'NITSKIY, G.G.;
CHIRKIIIA, L.At
Apparatus for studying the damping of low-frequency torsional
oscillations. Prib. i tekh. eksp. 8 no.3:172-174 MY-Je 163.
(MBU 16:9)
1. Fisiko-tekhnichaskiy institut AN UkrSSR.
(Oscillations--Electromechanical analogies)

AZHAM, T.M.;_~INDIff, I.A.; STARODUBOV'f Ta.D.
Comparing the effect of prestreming at 4.2 and 3000 K on the
Oresp eharacteristice of nickel at 700OC6 Fisomet,, J met&J10-
ved. 15 no.18119-124 Ja 163. (MIRA 1612)
1. Fixiko-bekhnichookiy inBtitut M UkrSSR.
(Niakel-Cold working) (Oreep of nickel)

S/126/63/015/003/022/025
E073/E320
AUTHORS: Garber, R.I., Gindin, I.A. and Neklyudov, I.M.
TITLE: Influence of "programmed strengthening" on the creep
and recrystallization of iron'at elevated temperatums
PERIODICALi Fizika metallov i metallovedeniye, v. 15, no. 3,
1963, 473- 475
TEXT: In earlier investigations on calcite. bismuth and
iron, the,author's found that in addition to ordinary atrengthening
cauBed by lattice distortions during the process of plastic
deformation under a continuous load, there is also "programmed
strengthening" due to diffusion-blocking and strengthening of weak.
and overloaded lattice nodes. 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 at t3mperatures lower than or equal to the
temperature of the programmed treatment. In the work described
o were polished and chemically
here, specimens f Fe (0.031a 0
etched, vacuum-annealed at 880 C-for 3 hours and then slowly
2 0
cooled. After "programmed loading" up to 8 kg/mm at 300 C at
Card 1~,

S/126/63/015/003/022/025
Influence of .... E073/E320
2
a rate of 90 g/mm h the specimens were affbjected to a 100-hour
creep-test at 400 C with a load of 7 kg/mm . The creep rate of
previously progE3m-loaded specimens w&s significantly lower
(about 5.6 x 10 %/h) both in,the initial and in the steady-state
stages) than*that of.speciWens to which the final load had been
applied quickly.(1.3 x 10- %/h.in'the steady-state section).
This indicates thatoverheating does not eliminate the effect of
increased resistance to creep of program-strengthened specimens.
Microstructures are.reproduced of both types of specimens after
Annealing at 830 OC for 3-hours: 2f specimens loaded at 400 0 C
with a load increasing'to 16 4g/mm . whereby the 'rate of increase
varied between 22U and 6 x 10" g1mm /h; of specimens loaded
quickly. -The residuai'deformations were 1.3 and 1.6%, respective4
The inicrostructure of specimens which were-subjected directly to
the final load showed signs of selective recrystallization,
Whilst the microstructure 'of the program-loaded specimens was
almost the same as prior to annealing. The authors.consider the
r.esults as a further proof that program-loading leads to a more
Card 2/3

5/126/63/015/003/022/025
nf'.U'Onc0of
Influence Of'.... B073/E320
e7quilibriated stable structure in that the strengthening does not
5e m to c
seem to be accompanied by an increase in the free energy of the
t 1
crystal. There are 3 I`igures.
SUBMITTED: August 15, 1962

-Loinq-6i EPF (c)/FPF (n) -2tPVP W /PDS AFFTC
ru-b W7.71JD/IJP(C)
ACCESSION NIR: Ap3oo1699 S/0126/63/015/005/0729/0735,1
tq
MOR: AzI ef
VT -iazha, V. M. ;Gindin, 1. A.; Staro&bav, Ya. D.; Shapoval. B. I.
A
MLE: Effect of low-tepperatwe prestraln on the creep wd internal friction of
copper
SCURCE: Fiztka metallov i metallove-deniye, v. 15, no. S, 1963, 729-735
ToPIC TA-02S: com2ercisa-gra0le copper, sijbzero-te---me=a;t=e preatrairling, SwIeal-Ing,
oreep, cb).ar::s~beri-atics, internal friction, microstruat-ure changes
ABSTIMOT- The effect of low-temperatze prebtrain on the ercep, microstruct1we-,
3r"4 intanr--a friction of comarcial-grade copper MS studiied. Test specimens
awnes.I.-d in a high vacuim, for 2 hr at. 85CC were preBtret.-hed 2.5., 5.0, 7.5, 12.5,
C-x 35% at a ca.astant, rate of 0.03 m*sec at tempereh=es of NO or 4.2K. Specimana
prestretched at 4,Z,..( ware araieeled at room temperature for 100 hr. Both gnavp:i of
spenzi-wens ware th~en sibjected to ahort-time. creep tests in a vacl= of 0.02 iaan 'AI -(Z
at SOCY-1 imd:~r a evress of 2 kg/mm sup 2. nae tests ahoved that a pre,,Aredn of up
to 7.5% at roorm tempmture or subzero tengerat'are sharply decreased the rates of
the first and second creep stages. The second.-stAge creep rata, for iwtan~~e,
decreased from 0.95%/br for annealed specimens, 'to 0.09 and 0.05%/hr for sp--~Awns
Card 1/2

-I -Te -3p?w -expr
L 10iog-63
ACCESSION NR: AP3oo.1699
J
prestrained 7.5% at 300 and 4.2K. The rupture strar%th of approximately 6.5 tL- for
annealed speciiiens increased to approximately 10.0 and 12.3 hr for the speecimens
prestreetched 7.5% at 300 and 4.2K. n. e purer t2he metal and the coar-ser the grain,
the higher the effect of prestraining. Ozqygen-frae copper prestretched 7.5% at
300 or 4.2K and test,-d under the above conditions had a creep rate of 0.02 or
0.01%/hr and a rupt=e life of 19.5 or 24 hr. The 10% elongation and reduction of
arep- of the =nealed specir---i decreased to 4% for the speci-menns preatrxeint~d 7.5%
at 4.2 8nd 300K, Prestrain at 4,P-K strengthens grain bow-darieu and adje.-~!ent
grrAn zones and prowtes formation of a subatructzwe. U.-As &.,arply reducces the
number. of microcrag-ka f4--med along grain bolmdrries during creep md inhibits
intergranular failitrellk the metFa. Dow-tempera:'.,xre prestrciin reduzes internal
friction in copper and significantiy increauses the temperat,urelft which it be-gins
to rise sharply, e.g., from approximately 100C for annealed specimens to 320 ar~i
470C for specimens prestraLned at 300 and 4.2K. Orig. art. Ims: 1 table and
8 figures.
ASSOCIATION: Fizikq)-tekhnichei3kiy
AN USSR)
KT7iITTFD: 11Nov62
q
-b-3 CODE: 010
Card 212y'00
institut AN USSR (Physicotechnical Institute,
ME ACQ: 11ju163 FVCT-V 00
NO TU7 SOV: 016 OTM7 '- 003

L 10751-63 EPR/SWT(1)/SWP(q)/iNT(MN/BD.9--AFFTC/ASD--Pa-4- WW/JDr
ACCESSIO# M AP3001TOO' _'_V0126/63/0l5/0O5/0T36AY74T
AUMOR: Gindin, 1. Aj StM~OdUbov~ Yal V5
niobiuAt
TIM: Concernirg tha ductility of polyMstalline helium temperatures:
SOURCE; Mike, Metallov I MetallMdOnlye,. V. 15., no- 5P 196% T36-747
TOPIC TAGS- mechanical properties.of Vb, helium temperatures, microstructure,
crohaVdness,,deformation mechmiemp multiple, nedling,nonductility transitiorn
i
9pperature
ABSTRACT: The mechanical properties of Nb In the temperature razige from 1.4 "CO
300K hw;e been Investigatted. lb wLre (0.1% T& 0-058% TIO 0.05% Fe, 0.0% SO
3 mm iu diazeter was drom to diameters of 1,;&V 1.17, or 1.03 = -4ith process
ftnealing. The specimens were then vacuum annealed at 1BOO_24OOC to. remove
impurities, especially gases-(see Table I of Enclosure). The average grain size
in all annealed specimens was the same, approximately 75-100 g. Tensile tests
at 1.4-300K~at a strain rate of 0.03 wm/sec showed that pure Nb retains sub-
.9tontial du~tftity even at tev*eratures close to absolute zero (see Table 2 of
Enclosure). Between 200 and 140K the elongation drops; at temperatures belov
20K reduction of area rises sharply. At temperatures below 20K the strain-stress
curves have.a. sawlike, shape, vh1ch is caused by multiple necking. Up'to 9 neck-
ings formed on the specimens.tested at 4.2K. The microbardness along the gage
Card

L 18o4g-63 EWP(q)/F.WT(30/BD3 AFFTC/ASD 'JD
ACCESSIM NRs AP9002850 8/0126/63/015/006/0908/0913,
~:AJJT 4/,
HORSt Oarber, R. 1~9j'Oindlnj re A*; Neklyudov, re
TrTLEt Programme]. Wdening of commercial Iron 4A
S qllov I metallovedenlye, v. 159 h
OUPCE:. Fizika,m-qtL o. 6, 19063, 908-913
!TOPIC TAGS s proVammed Isrdeningo Iron, mechanical property
jABSTRACTs One of the possible methods for improving mechanical f solid
M P-e
lbodies consi-stIsor diffusive blocking -and strengthenigg -or 4-ecN or over-s-treared
1parts of a speolmin. Such parts may develop shearindr,, sliding surfaces, twinring
libnnds, or dislocation sources. This method was called "the programming of
ihnrdening. " The, levies used in the programr&ng procedure is described. It -allows
'the stretching of a specimen at high temperatures and at very amall rntes of load
"Increase. The co-limercial iron samples thnt undex-went a programed hardeningilft
?000 rere studied. The tensile test was condreted At the temperature of liquid
and also at room temperature. The ereep tist was also conducted at 'TOG.
i.PreUrAnar
.y defor,qation at high temperatures rnii lo,t rates of loading resultei ins
increase of flow limit and haxdeTd.-nf7 mdul-s; 2) increase Ill plasticity at the
Iterperatize of li-iidd nitrogen; 3) a -i1 deirease in w-eep velocity;

L 1809-63
tACCESSICH NR8 AP3002850
elirdnation of creep at 3000. It is concluded thpt the observed effects are du
I to a diffusive ho-dening of week and overstressed rogions in the salEples. The
euthors expross-Viair appreciation to V, M. Stolvarov and 0, 0. Chechellnitskly for
their help in the construction of this device. Orig. art. has: 6 flMes.
ASSOOTATIONt F1z1,ko-tekhnioheskiy inatitut AN USSR (Inatitute'of P17sios and
Technolompy. Acads,7 of Sciences, MmSSR)
SUBMITTEDs 26Jun62 DATE ACQ: 23Ju163 ENCI-t 00
SUB COM ML NO REP SOVt 008 OMRS 001
I

GINDIN, I.A.; LAZAREV, B.G.; KffVFDCIIUK, I.R.
Dilatometric investigation of the low-temperature deformAf4xn
transition to lithium. Fiz. met. i m9talloved. 16 no.5-793-794
N 163. (141RA 17:2)
1. Fiziko-tekhnicheskiy institut AN UkrSSR.

ACCESSION NRt AP4037066 S/01291641000/005/004410046:
AUTHORs And-im'-Z.-A.; Lazarevs, H. B.; NikLshov, A. S.; Rink,,
L. P.; Starodubov, Ya, D,j Yarov, I* A*
TITLEt HechanLcal properties of structural alloys at low tempers- i
ture
SOURCE: Hetallovedeniye j termicheskaya obrabotka metallov, no. 5,
111964, 44-46
TOPIC TAGS: alloy structural alloy, austenitLc iron alloy, ji
KhM46G7AR alloy,oKhl2N2OT3R alloy, Khl6G9AN4 alloy, KhN35VTYU at 'Ye
titanium alloy, OT4 alloy, copper alloy, BrKhO8 alloy, ZhS6KP alloy
steel, martenditic etee.1, VNS2 steel, E1659 steel, cryogenic alloy
ABSTRACTs 'Mechanical properties and fracture tests of KhM16VAR,
Khl2N20T3R, Khl7G9AN4p KhN35VTYu; austenitic iron base alloys VNS2
(EP22S) and 81659, martensitic steels, ZhS6KP high-strength alloys
OT4 titanium alloy, BCKh08 copper alloy. and other (unidentified]
alloys vere investigsted.at temperatures in the 4.2-300K range*
1CeM 1/3

ACCESSION NRs AP4037066
Specimens (either flat with a cross section of 1o5 x 2 mm or round
nd 2.2 ma in diameter) were tested in a heat-treated condition
shown In the article). With a decreasing test temperature the
I
resistance to plastic deformation and the tensile strength of all'
alloys increased. This was found to be particularly pronounced
in the case of VNS2 alloy which at 293. 77, and 20K had a tensile
strength of 97.5. 155.0, and 180.0 kR/aul (annealed at;950C, air
cooled, and tempered at 620C for I hr). All alloys were found
to maintain some ductility at temperatures as low an that of
liquid hydrogen except for E1659 steel and OT4 alloy which failed
with respective elongations of OZ(at 200 and 0.7% (at 77K). The
elongation of the VNS2 alloy, on the contrary, was found to incresse'
with a decrease of temperature from 15% at 293K to ZOZ at 20K.
BGKh08 copper-base alloy was also very ductile at low temperatures
(at 4.29 an elongation of 18*6%)o A simultaneous increase of the
ductility and strength of VNS2 alloy might be explained by some
changes of phase composition under the effect of low-temperature
daformatkons All tile materials tested at temperatures down to 20%,
yielded uniformly, some 41tho some without necking. Only in., the case"
of the VNS2 steel did the strain-stress curve at 20K have a saw-lLke,
C,.,d 2 / 3

ACCESSION NRI AP40370'66
shape. However, at temperatures above 20K the steel yLelde uni-
formly. The fracture mode was ductile with clearly express:d
neckino even at 20K~ Orig. art. hast I figure and I table.
ASSOCIATIONs FLziko-t*khnLcheskLy instLtut AN USSR (Physica-
technical Institute, AN USSR)
SUBMITTEDs 00 DATE ACQs 05jun64 ENCLs 00
SUB CODES 00 MY SOV: 002 OTHERs 000
Com 3/3
L

GARBERP R.I.; GINDINS I.A.; MOGILINIKOVA, T.T.; NEKLYTEDOV, 1.1-1.
Internal friction of iron hardened by programming. Fiz. met. i
metalloved. 18 no.3:443--447 S 164. (MIRA 17;]J)
1. Fiziko-tekhnicheskly institut AN UkrSSR.

L Pad IJF(c)
I-TJU/JD/JT-1/ff4
ACCESSION NR., AP4048767 S/0126/64/018/004/0511/0517
A=OR: Azhazha, V. M.; Gindint 1. A ; Starodubov, Ya. D.
TITLE: Effect of stress and temperature on creepAn nickel Liminarily
deformed at 4. 2 K.
SOURCE: Fizika metallov i metallavedeniye, v. 18, no. 4, 511-517
-TOPIC TAGS! ratur ffect, nickel deformationr
-pe e-e
16~v-t-diaoeratur-e--de;-ormation
ABSTRACT: The effect of stress and temperature was investigated on creep in
nickel which underwent a deformation at 4. 2 K. It was found that this low temp-
erature deformation increases the life of N-0- ickel during creep. In the in-
vestigated temperature range (4. 2 to 300 K) e liletime of nickel is an exponen-
tial func,tion cf the stress and of the inverse ernper-ature. The tensile strength
;is also increasing. The activat* of creep in mckel corresponds to the
lonenergy
activation energy of seLfqffjsion.AThe increased residLance to creep is connect-
ed with the formation of fine-grained, disoriented aubstructure which resists
Card 1/ 2

NR REF SOV: 017 OTHER: 002
t
i
2/2 1

-T. afl- (q)[ENT /VA ANT (t JD
Alu
Cal tW6 ~c
H i i.1 M-ect obaervatfon of the 6mmeratim and growth of meellmd
at low tcmj~-rature tenuiaa of purls jMn
(1, no. 4. 1964. 605-611
TO-2-1C TAGS.* mech=icpi twfanft, Iovr temperiture iron tenst-o'n., pure iron
-AESTIRACTt The generatiom and 1grawth of a twin !ayer in pure (99. 99%) iron
wzz stucHed under tenzion at 78 K . It-is-shown viat as the twin thickens upon
z-c-lic-ation of a continuous: load, the coefficient ol meclumical strengthening ooff th
'-clindary decreasea. Annealing at 300 K, restareEt the ox-iginal. high strengthefti4
The dem obtakaed show that the boundary and Lhe ne-gion near the
ch-anre In m dffferent mamer on the twti-layer appearance, at its grelld)
MR r -ztica indicate zitaLt Lhare Is no
g, =1 r ar -n -ealing. The pattern c:f microderstru o
eizzct, c=actioa bcUmoa the q n,,=.d tim twinning of pure iron.

22898-;62 IJP(c) JD
ACCESSION NR: AP5-00_1246 5/0126/C-4/01,q/005/0762/0769
AUTHOR: Gindin, I.A.;Staroduibov, Ya..D.
-d"
TrrLE: Extending the life of pre-twinned pure iron and the development of twins In the
course
SOURCE: Fizika metallov.1 metatllovedeniye, v. 18, no. 5, 1964,.762-769
TOPIC TAGS: iron life, pretwitined irom high temperature creep, iron creep, Iron
twinning, iron icrostructu.L~ It ' I
ABSTRACT: The kthors studiedthe influence! of small preliminary deformations at low
temperatares (300i 77~ and 4. 214.) on the high~ternperature (600C) creep of pure iron
(99, 99%). The microetructure of the deformed samples and itz change in the course of
creep was studied by the metallographic, and microinterferential method at room temper-
ature. It was found that the small preliminary deformation at low temperatuxes causses
an appreciable increase In the creep, strength wid life of iron; this hardening effect is
explained by the interaction of Miming and gl13sile dislocations. A new type of shear
plasticity was observed during tka high-temperature creep of the iron. Creep after a
small low-temperriture deformation Is charactarized by an increase in the plastic:fty
Card 1/2

ASSOCIATION: Fiziko-tekhnichadiy institut AN *UkrSM
SUBItUTTED: IgAug63 . ENCL: 00
NO RE F SOV: 014
Card 2/2 .
OTHER: 000
SUB CODE: Ml
tm

IJP
ACCESSION NR: AP50023,16 S/0126164/018/006/0904/0908
A UTHOR: Garb r, R. 1. - Gindirt, 1. A. Za'ivadiyy, S. Ya. Mikii4ylovskiy
_~! be
V. N'T. ', Malik A. K. ; Ne!~1~dov;
TITLE: Effect of programmed hardening on creep of polycrystalline zinc and
stability during cyclic heat treatment
SOURCE: Fizika metallov i metallovedeniye., v. 18, no. 6, 1964, 904-908
-programmed hardening, 4tat-treat-_'-~
TOPIC TAGS: polycrystalline zinc-, creep,
ruent; - -cyclic -Wdt'treatment -
ABSTRACT: The effect of pogrammed hardening (hardening-, bv controlled a2pli-
cation of stress at slow rate&) on the creep of polycrystalline zinc at room tem-
perature and on its resisiance to forming during cyclic iieat treatment was stud-
ied. The linear deformation of annealed polycrystalline zinc and of samples sub-
jected to loading (1-6x,0-4 kg/mrn2/min) an'd to loading beyond the yield point
(2. 5 kg/mm2/min) was compared. The elongation of the programmed samples
,Card 1/2

7
J
L 36625-65-
ACCESSION NR: AP5002348
was less than in the annealed and rapidly stressed samples, was reduced two
times as the programmed rate was decreased from 5 to L 5 x 10-4 kg/MM2.
J
cy-y--i-,
Samples- subjected to normal treatment -were less resistant to heating-~ cooling--
cles than programmed samples.: !rhe hardening increased as the maximum
temperature of the cycle was reduced. The maximum temperature approached tf-~
melting temperature (0. 9TM KY The creep in progra4 harden6d samples was
less than in those otherwise deformed. Metallographic%nalysis showed slip
bands and the formation of substructures -in -,t smal! number of the grains. Small
migration of the boundaries occurred in saMDles after programmed and after or-
dinary hardening prior to thermal cycling; after that the mifsration in the program-
rned saiaples was much less noticeable. Thus programmed hardening of polvery-
stalline zinc increased its creep strength and its resiqtan(,e to forming during
cvch(- heat treatment. Orig. ari.. has: 3 figi. res and I table
ASSOCITTION: Fiziko-tekhnicheskiy institut All LkrSSR (F'hysical- technical Insti-
tute AIN Lr;,:r65R)
SUBMITTED: OlAug63 ENCL: 00 SUB CODE: MM
NR REF SOV: 009 OTHER: 00 1
Card 2/2

Ranieri rq~ a r, Cl C
lotided to

L 39679-6~ EWT(m)/FtlVP(w)/EWASJYT/M7P(t)/E;IIP(z)/E'RP(b) Pad 1JP(C)
j
ACCESSION NR: AP5008790 JD/HV(' S/0126/65/019/003/0439/0442
AUTHOR: Azhazha, V. 11,; GindLn, T. A.; Kozinets.-V. V.;
Stargdubov, Ya.-D.
TITLEt Effgct of annealing temperature an the substructure and
strength of nickel deformed at 4.2K
SOURCE: FizLka m Ata lov L metallcvedeniye, v. 19, no. 3, 1965,
439-442
TOPIC TAGS: nickel, preliminary nickel deformation, nickel process
annealin'g, nickel property, nickel creep esistance, nickel sub-
structure
ABSTRACT: The effect of annealing temperature on the substructure
and mechanical properties of H-0-tyAe nickel stretched 3.5% at -
4.2K has been studied. Ann~'a_iin?611"a done at 300, 500, 700, 900,
or 10OOK. Annealing a~_ 300 to 700K slightly reduced the subgrain
size. while annealing at 9G0 or 1000K increased it. The optimal
annealing temperature was 500K at which a fine polygonized sub-
structure with a large disorientation angle between the subgrain
Card

L 39679-65
ACCESSION M AP5008790
IZ
fragnents and subgrains van formed. Nickel with sucti a atabstructure
has the highest resistance to plastic deformation at roan temperature,
the longest rupture lifeand the highest creep resistance. Specimens
annealled at 50OK' showed almo6t no first creep stage and the creep
rate in the second stage was stx times lower than that of the initial
metal and five times lower than that of ntckel annealed at 1000K.
The Gubgrain size was found to be practically the same with any
annealing temperature, and to be congiderabl7 smaller than that of
the initial metal. Orig. art. has: 3 figures.
ASSOCIATION: Fiziko-tekhnicheskiy institut All UkrSSR (Physico-
technical Institute. AN UkrSSjt): Khar'kovskf-ygosuniversitet
(RE`a-r'V`avState University)
SUBMITTED: 07Jan64 ENCL: 00 SUB CODE: MH

GINDIN, I.A.; NEMMOV, I.M.; SME'LOVA, D.F.
11 ........... .
Influence of grain size on the effect of iror, hardening durin.v,
programmed loading. Piz. met. i meta.1loved. 19 no.4:6,!7-629
Ap 165, (jI.J1.11A -J~t:5)
1. Fiziko-tekhnicheskiy institut AN UkrSER-

WTIM-i "tJTF,-WP-(b-VW_A(C)XjP(C) JD/jo
AP5027148 UR/0126/65/6~6/601;/06oVo607
Za
AUTHOR: Garber, R.I,-; a I.A Chirkina, L.A.
ORG: Phyalcotechnioal Institute,_AIT UkrSSR (Flzlko-tel~hnlcheskly
institut AN UkrSSR)) V
TITLE: Low temperature "deformation" polymorphism in lithium by the
~nlernal Lr-y,, method 5_~
SOURCE: Fizika metallov I metallovedeniye, v.20, no.4, 1965, 603-607
TOPIC TAGS: lithium, phase transition, Internal friction
AVA
ABSTRACT: Meag~rem4nts were made by the method of damping free tor-
sional vibratikne of the samples in the temperature Interval embracing
the transitionkYrom a body-centered cubic lattice to a face-centered
cubic lattice (78-2000K), at frequencies of 0.7, 0.8 and 1.3 cycles, in
the region Independent of amplitude. The logarithmic decrement of
damping was taken as Ahe measure of internal friction. The lithium
samples, of a Purity kf 99.3%, were prepared by pressing in the mold at
room temperature undeg a layer of kerosene for protection from oxidatia
The length of the effective cylindrical section of each sample was 30
mm and the diameter 3 mm. Por stress measurements, the sample was
annealed for 2-3 days at 3000K, then pickled In methyl alcohol and
UDC: 548-33:539.67

ACC NRs A2502714d ef
cooled to the temperature of liquid nitrogen (780K), at which temper-
ature it does not oxidize or undergo phase transition, and was mounted
in the apparatus for measurement of Internal friction in the single
phase state (body-centered cubic). To Induce the polymorphic transi-
tion from the body-centered cubic to the face-centered cubic lattice
and to investigate internal friction, part of the samples were previ-
ously deformed by torsion at 780K up to the relative shear, 5.2 X 10-2.
The martensite nature of the "deformation" nature of the transition
from a body-centered to a face-centered cubic lattice in lithium is
marked in an especially clear manner in experiments on measurement of
internal friction during heating of the samples to determined tempera-
tures above and below the temperature of the reverse transitions with
intermediate cooling to 780K, as well as in a study of the frequency
dependence of internal friction. Orig. art. has: 3 figures.
SUB CODE: MMJC/ SUBM DATE: 28oct64/ ORIG REP: 010
OTH REP: 005
vj~

L 24575-66 EWT(m)/T~t~Vt) 1,TP(c) JD/JH
,ACC NR: AP6ooq671____ SOURCE CODE:-uR/ol8l/66/oo8/oO3/0842/0845~,
KUTHORS: P. A.; Gindin.,.,
Bezuglyy, Neklyudov, 1. M.
Rabukhin, V.B~.
ORG: Phvsicotecbnical Institute of Low M-mnP_rqf-mrA.R AN Mr-PPRR
__aD.d_~K y~kriziKo-reKnnicneskly InstItut nizkikh temperatur AN UkrSSR)l
Securing of disjocaftonA. point defects during programmed
Joading of aluminum single crystals
i1SOURCE: Fizika tv4dogo tela, v. 8, no. 3, 1966, 842-845
~TOPIC TAGS: hardening, crystal dislocation phenomenon, crystal
defect, static load test, ultrasonic absorpti.on, aluminum, single
':crystal
;kbSTRACT: This is a continuation of earlier work (FMM v. 18, 443P
11964 and earlier papers) dealing with various hardening mechanisms
!that can be activated by varying the rate of increasing an external
I
istress on a crystal and the possibility of programming the hardening
,on the basis of such mechanisms. The present paper presents the re-
-Card 113

L 2.1457 5~
NR: 4P6009 1
4 5
Fig. 1. Block diagram of pulsed ultrasonic
installation. 1 Master ulse generator,!
p
2 -- modulator, 3 high frequency
generator., 4 -- sample, 5 -- superhetero-
dyne receiver, 6 -- oscilloscope, 7
controlled pulse delay, 8 -- pulse
generator, 9 -- standard hf generator,
10 -- attenuator.
sults of an investigation of the dependence of absorption of longi-
tudinal.ult'tasound on the level of prestressing attained during pro-
grammed (slow) hardening of single-crystal aluminum, and the results
obtained with fast loading are also given for comparison.' Both an-
,nealed and non- annealed samples-were tested. The absorption was
measured by comparing two successive reflected pulses, using an
ultrasonic pulsed setup (Fig. 1). All measurements were made With a
longitudinal compre asion- rare faction wave operating at 72.Me. From
Card 213