SCIENTIFIC ABSTRACT DYAKOVA, K.G. - DYAKOVA, T.D.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000411720011-4
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 22, 2000
• Sequence Number: 11
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

DIYAKOVA, K.G.
population dynamics of murine rodents
mountain oak'forests of the Khoper Preserve. Trpdy
zap. no.3197-102 159. -
(1hoper freserve-4fice)
in the
Khop.gos.
(MIRA 161l)

MAKAROV, V.V.: DOYAKOVA K*GO
I
0
Catching deemano in the Khoper Preserve in 1956-1957. Trudy
Khop.gos.zap. no.3s5-14 159., (?URA 16i1)
(Khoper-Preserve-Desmans)

DIYAKOVA, K.G.
- --------
Preliminary results of artificial diistribution of desmahs' in
Kursk and TomsIeTrovinces. Trudy Khop.gos.zap. no.52131-138
161 (MIn 16:2)
iKursk Province-Desmans) (Tomsk Province_ smans)

LOZOVOY. A. V., DIYAKOVA. M. D., STEEPAINTS7,Vl, T. 0.
"On ~e'rtidn ~hys-ical 6onstants of Mixtures of'llydrcc:u-bonil -- IT," L"I'l1r. CbSIX11.
Milm., 9, N.o. 6, 1939. Peceived JL~ jl_lly 1938.
Report U-1517, 22 Clet 1951

USTINOVAy Ye.I.; DIYAKOVA. M.Li SHCHEDIUM) H.N.
---- -- I -.-- ". ,
Development of the embryo and endosperm in Mirabilis jalapa.L.
under conditions of restricted pollination. flauch. dokl-. vys.
shkoly; biol. nauki no-3-*173-179 161. (MIRA 14:7)
1. Rekomendovesm k&fedroy genetiki. i selektsii Moskovskogo gosudar-
stvennogo universiteta, im. M.V.Lomonosova.
(FERTILIZATION OF PLANTS)

-DAYAKOLA, Hj.,
Production of tetraploid buckwheat under natural conditions. Trudy
MOIN Otd.biol 5:173-179 162. (MIRA 16:5)
1. Kafedra genetiki i selektsii biologo-pochvennogo fakullteta
Moekovskogo gosudarstvennogo universiteta.
(BUCKWHEAT EREODG) (POLYPLOIDY)

S/126/6o/olo/oo6/016/022
E193/E483
AUTHORS: JILY~a~" - A ~.a nd Bogachev, I.N.
TITLE: Decomposition of the Beta-Solid Solution in a
Titanium-Manganese Alloy
PERIODICAL: Fizika wetallov i m-atallovedeniye, 1960, Vol.10, No.6,
pp.896-902
TEXT: The object of the present investigation was to study the
kinetics of the solid state transformation taking place in a
titanium-base alloy containing 6.5% Mn, 0.18% Fe, 0.07% Si,
0.05% C, o.o43% N and 0.00596 H; this particular alloy having
been chosen as one in which the 0-phase can be retained by
quenching. The experimental specimens were prepared by melting
the alloy in a vacuum-arc furnace, remelting it in an argon-arc
furnace, forging, rolling to the final size and then vacuum-
annealing at 650OC- The kinetics of the decomposition of the
P-Phase were studied by the dilatometric method, hardness and
electrical resistance measurements and metallographic examination,
Some of the dilatometric measurements were taken on specimens
quenched from 9000C and then heated at the rate of 200'C/h,
Other experiments consisted in heating the specimens to 900"C,
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S/126/6o/oio/oo6/oi6/O22
E193/E483
Decomposition of the Beta-Solid Solution in a Titanium--Manganese
Alloy
transferring it to a salt bath and studying the changes of various
properties as a function of the duration of the isothermal
treatment. It was concluded from the results obtained that
decomposition of the P-phase can take place in two temperature
ranges, separated by a temperature interval within which the
P-phase appears to be stable. One range extends from 420% up to
the temperature of the polymorphic transformation, and decomposition
of the P-phase at these temperatures leads to the formation of the
a-phase. The second range extends from 150 to 4OO'C. the product
of decomposition in this case being an intermediate .o-phase, In
the 420 to 4700C temperature range, these two processes overlap and
the decomposition of the P-phase results most likely in the
formation of the a-phase, via the intermediate w-phase The
formation of the w-phase is not reflected in any changes 1.n the
microstructure of the alloy but is revealed by an increase in
hardness (up to 48 RC), a decrease in volume and a decrease in the
electrical resistivity (down to 1.4 ohm mm2/M)- The decomposition
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s/i~_,6/6o/oio/oo6/oi6/O22
E193/E483
Decomposition of the Beta-Solid Solution in a Titanium-Manganese
Alloy
of the P-phase, leading to the formation of the a-phase via the
intermediate w-phase, is accompanied by an increase in hardness, an
increase in volume and a decrease in electrical resistivity (down
to 1.0 ohm mm2/m). Finally, decomposition of the P-phase, leading
directly to the formation of the a-phase, brings about a decrease
in both hardness (down to 35 RC) and electrical resistivity (down
to 1.0 ohm mm2/m). There are 5 figures and 5 referencesi
2 Soviet and 3 English.
ASSOCIATION: Urallskiy politekhnicheskiy institut im, S.M.Kirova
(Ural Polytechnical Institute imeni S,M,Kirov)
SUBMITTED: July 30, 1960
Card 3/3

21362
.12~go' ILI IS_Sl~j 2805 S/126/61/011/004/009/023
E021/E435
AUTHORS: Bogachev, I.N., Mints, R.I., Petukhova, T.M. and
ALy~koXa__,.
TITLE: The Influence of Phase Composition and Structure on the
Cavitation Stability of Titanium and its Alloys
PERIODICAL: Fizika metallov i metallovedeni-je, 1961, V01.11, No.49
pp-557-563
TEXT: Testing was carried out on an erosion stand with a
circumferential speed of rotation of the samples of 78 m/aec,
a constant pressure of water 0.28 atm, diameter of jet 8 mm and
distance 1.8 cm. The cavitation stability was evaluated by the
loss in weight every 5 hours-of testing. Alloys with-a-phase
structure (commercial Ti type ST 1A (VTlD), Ti-3-5 Al,
Ti-2.5 Al-5Sn, Ti-6ki-4V) showed slip'lines and twins in the
initial stages. With increase in time, cracks developed along the
twins, the slip lines and along the grain boundaries. Table 1
shows the influence of alloying on the stability of a alloys.
Solid solutions of the P phase (Ti -3.25 Al -io.45 Cr- 7.95 Mo-
0.11 Fe and Ti -9.6 V -2.84 Al -3.8 Mn) showed some disintegration
simultaneously in the grain boundaries and in the grains (Fig.2).
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21362
S/126/61/011/004/009/023
The Influence of Phase ... E021/E435
Although the 0 solid solutions were more resistant to cavitation
than the a, they were liable to sudden fracture and were
unsuitable for use in such conditions. Alloys with a
martensitic structure were also tested. The martensitic structure
was produced by fast cooling from the 0 region. During testing
the a'-phase was destroyed more uniformly than the a phase.
Disintegration began at the grain boundaries and in the grains at
the boundaries of the martensitic needles. Fig.1 shows the
initial stages of cavitation of the a and a'-phases. The
martensitIc structure has a high resistance to cavitation as shown
by Fig.3, where the loss in weight (mg) is plotted against the
time of testing (hours) for the a, a', a + a' and a + 0 phases of
the same alloy. The presence of a fine acicular martensitic
structure leads to increase in the cavitation stability. The
resistance to cavitation of an alloy consisting of a + 0 was
intermediate between the resistance of a and a'. Disintegration
began at the boundaries of the two phases and developed in the
phase which was less stable towards cavitation. A mixture of
0 and w phases was obtained by heat treatment of the
Ti- 9.6 V- 2.84 Al- 3.8 Mn alloy. The formation of the w phase
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.5/126/61/oll/oo4/oo9/023
The Influence of Phase ... E021/E435
led to an increase in hardness from 360 to 495 kg/mm2.
Cavitation caused a network of slip lines as in the case of the
0 phase. The resistance to cavitation of the 0 + w alloy was.
higher than that of tl~e 0 alloy, but it was liable to sudden
fracture as was the P alloy. Thus the cavitation stability of
titanium alloys depends on the structUre and phase composition
and not on the mechanical properties. There are 4 figures,
2 tables and 2 references: I Soviet and 1 non-Soviet.
ASSOCIATION: Urallskiy politekhnicheskiy institut im. S.M.Kirova
(Ural Polytechnical Institute imeni S.M.Kirov)'
SUBMITTED: July 30, 1960
Card 3/8

Fig.?
The Influence of Phase ...
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S/126/61/011/004/009/923
E021/E435
4
-Ir

21362
S/126/6i/oil/004/009/023
The Influence of,Phase ... E021/E435
0
'V
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Fig.2.
Card 5/8
V1\

21362
The Influence of Phase
S/126/61/011/004/009/023
E021/E435
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/10
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70

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Fig-3.
Card 6/8

;eIJ62
S/126/6i/oli/oo4/009/023
The Influence of Phase ... E021/E435
Table 1. Legend:
I alloy
2 quenched in watei
3 hardness kg1mm2
4 weight loss mg
5-after 5 hours test
6 after 10 hours test
7 a phase, MD (commercial TO
8 - a phase Ti- 3.5 Al
9 - a phase Ti- 2.5 Al- 5Sn,
l 0 - a phase BT6 (VT6) (Ti - 6 Al - 4 V)
Card 7/8

The Influence of Phase ...
Table 1.

f~

nio
21362
S/126/61/011/004/009/023
E021/E435
M1 IUTepli a nece, mr
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om
,
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5 mcoti
(41 (0 tacun
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3.11m,lit CH.,ma or BOO, 112 IC9 708
B, I I

2-030 CnA49a'
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BTG
. . I

31055
S/126/61/012/004/015/021
I ZB s-, El-93/E383
AUMORS; Bogachev, I.N. and
TITLE-~ The kinetics of decomposition of P-solid solution
in a heavily-alloyed titanium alloy
PERIODICAL: Fizika metallori metallovedeniye, v. 12, no* 4,
1961, 607 - 612
TEXT-. It has been shown by other workers (e.g. Ref. I -
E.L. Harmon, J. Kozol and A.R. Troiano, Trans. ASM, 1958, 50,
418) that, in the presence of elements stabilizing the P-Ti
phase, decomposition of this phase in solid Ti-base solutions
can be accompanied by the formation of a hexagonal w-phaae
(a = 4.6 kX, c = 2.82 kX), orientated relative to the
P-phase in 8uch a way that a. if [1101 , and c. 11 [1111
The object of the present investigation was to study the
kinetics of decomposition of the P-phase in a Ti-base alloy,
containing 9.6510' V, 3.845/o Mn and 2-57% Al, by hardness,
electrical resistance and dilatometric measurements. In the
first series of experiments, the specimens were bLeated in
Card 1/~Y

31055
5/126/61/012/004/015/021
The kinetics of decomposition .... E193/E383
vacuum for one hour at 900 0C, quenched in a molten nitrate
bath at various temperatures, held at a given temperature for
various times and then cooled to room temperature, after which
the relative change in length, &f/f , of the specimens was
determined. The results are reproduced in Fig. 1, where
Af/f x 10-4 is plotted against time Oirs) at the temperature
(0C) indicated by each curve. It will be seen 0that isothermal
treatment at temperatures between 160 and 380 C brought about
contractlon of the alloy, which indicated the formation of the
w-phase. The results of hardness measurements of similarly-
treated specimens are reproduced in Fig. 4, where Vickers
hardness is plotted against the isothermal-treatment temperature,
the time at temperature being indicated by each curve. In
Fig- 5, the electrical reslstlvity ~P, JX mm /m) o:C the alloy
is plotted against the temperature ( C) of isothermal treatment
of 30 min (crosses), 3 hours (triangles) and 6 hours (circles)
duration. Dilatometr1c heating and cooling curves were also
constructed and metallographic examination of some specimens
was carri d out. Bitsed on tile results obtained, a diagram of
Card 2/ ;r~

3-1-055)
S/126/61/012/Oo4/015/021
The kinetics of decomposition .... E193/E383
the isothermal transformation (TTT curves) of the P-phase in
the alloys studied was constructed. It is reproduced in Fig- 3,
showing the constitution of the alloy as a function of
temperature (vertical axis, 0C) and time (horizontal axis, see);
the experimental pointsdenoted by circles are based on metallo-
graphic examination; the dilatometric data we represented by
x - x and x -- x lines indicating, respectively, the beginning
and end of volume expansion, and by dots indicating the beginning
and end of the volume contraction. The results of the present
investigation indicate that there are two distinct modes of
decomposition of the P-phase in the alloys studied. Decomposition
at temperatures a8ove 500 OC entails the formation of the a-phase.
In the 160 - 370 C range, the w-phase is formed which brings
about a considerable increase in hardness and causes embrittlement
of the alloy. Between 380 and 480 0C the formation of the a-phase
is proceded by the formation of the w-phase, the latter also
being accompanied by an Increase in hardness. It was also found
that the P--.Vw transformation 0was reversible. Specimens,
hardened,by quenching from 900 and isothermal treatment at
Card 34/83//
/ I

31055
S/126/61/012/004/015/021
The kinetics of decomposition .... E193/E383
300 0C, can be fully restored to their soft condition by 30 see
holding at 500 OC, followed by wator-quenchIng. Partial
restoration only can be attained 0in the case of material iso-
thermally treated at 350 or 370 C or when the duration of the
treatment is excessii4y long.
There are 5 f1gures, I table and 5 references~. 2 Soviet-bloc
and 3 non-Soviet-bloc..
ASSOCIATION-. Urallskiy politekhnicheskiy institut im.
S.M. Kirova. (Ural Polytechnical Institute
im. S.M. Kirov)
SUBMITTED- March 21, 1961
Card

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Investigating the Chan" Composition, properties and
00 j methods of treating fdmsq tan from Chelyablalk brown '-so
00 Weis. 1. Destructive hydrogenation of the primary ur '-00
ham CkrAyabbuk brown coals. A. V. Umavul &mI
M ~ kffiakovit- J. A pphdd Chm. (U. S. S. R.) S.
'o
at In French 5w)(10M). l4re C, A. 29. liCs'.
11. The choodW wspositim at the light fraction from !,a
the primary CRr km Chelyabinsk brown co&ls and the
00 atmbillcatim of the hydrocuboa part of the "benzine." -00
At. K. D.yak~*, A. V. Lasavol and S. 1. Cherik.,va.
J. A pphird ClOm. (U. S. S. R.) 8, 60,',705(iti Frrmh 71 -00
(1935) Swe C. A.". 70451. A. A. Merhilinxit not
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09 are suitable raw ni2teri.AN lot l1w AID 0
of
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06 burnic-ulinpvtitc, (V. Aitflir4erfle -I (if). J. "W'1;
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v)-!,; V, IV. 1, 79.7: oil shAle, V11. 4. N 1. 1. C., It. Y. I-A
Separation process in the Rhoolavour lcoal washerl.
R. Scinlxil. Glikkaml 73, WI 701W). The
vatjou% stages of wpa. are examd. The Applicaliall) (if
I lie data obtaincti to coni. practice is diwusied. moo
if. C. 11. A.
woo
Als-SLA__!gT&L~URCKAL_LlltlAtt&f CLOSOICATIOM
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Solutions. 1. Bartass sapiromotit. WYALOVS,
A. V. Liwivul and V. 11. Kjr4txw%-ich.
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lius 111311irf still.; 04 "q of -11 (IM the wit
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