SCIENTIFIC ABSTRACT UMANSKIY, YA.S. - UMANSKIY, YA.S.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001857930007-1
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: March 14, 2001
• Sequence Number: 7
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

Cameras for the URS-50I Apparatus, Adapted for
Photographs at High and Low Temperatures
ASSOCIATION
S"032/60/026/01/037!/052
Bblo/3006
cample is attached. The outer wall also has a projection
sealed by a celluloid films The projection of the inner
viall protrudes into that of the outer wallq thus enabling
the X-rays to be focussed through the celluloid film on
the samp1c. The te,,-jperature of the oample is measured by
a thermocouple. Rapid sample heatin - from - 1770 to room
temperature can be effected by means of emall heating
elements. There are 2 figirrea ~nd 1 referencP-
Moskovskiy inatitut stali im, 1. V. O)trilina (1,400cow
Inotitute of Steel imeni 1. V. 'tilin)
Card 2/2

m - .
UMANMIY, Yakov Semenovich; LYUTTSAU, V.G., red.; GORDON. L.M., rad.izd-va;
- OR re 0
A
W d
[X-ray diffraction techniques for the study of metals) Rentgeno-
grafiia metallov. Moskva, Gos.nBuchno-tekhn.izd-vo lit-ry po
chernoi i tsvetnoi metallurgii, 1960. 448 p. (MIRA 13:12)
(Ketallography) (X rays-Diffraotion)

LWVSKV, Ya. S., XAW) A. S., SONENKOV) V. A.
240:xI. Diffuse Scattering of X-Rays by Alumimua Brasc. "
Steel InBt., Leninsky Prospekt 6, Moscow, USSR.
paper submitted for 5th Gen. Assembly, Symposium. on Lattice Defects, Int.l. Union of
Crystallography, Cambridge U.K. Aug 1960.

18.8100 77703
Sov/148-60-1-26/34
AUTHORS: Kagan, A. S., Umanskiy, Ya. S.
TITLES: Characteristic Temperature of an Ag-Au Alloy Within a
Temperature Range From 279 To 5230 K
PERIODICAL: Izvestiya vysshikh uchebnykh zavedenly. Chernaya metal-
lurgiya, 1960, Nr 1, pp 152-154 (USSR)
ABSTRACT: In order to determine the characteristic temperature
of Ag-Au alloys and of pure Ag.in terms of the drop of
the diffraction intensities with the increasing atomic
thermal vibrations, the authors measured the diffrac-
tion intensities at 279-5230 K by ionization set
URS-50I. When a steady-intensity incident beam is
applied
= - 2Mr, + 2'%lr,,
Card 1/4

Characteristic Temperature of an Ag-Au 77703
Alloy Within a Temperature Range From SOV/148-60-1-26/34
279 To 5230 K
holds, where (4) denote the products of all
T, T2
factors except temperature and
M 121,2 1 _!~ (,)- +IsW 0
Ink 0X 4 1 -"),*
describes the Debye-Waller intensity connections. The
powdered Au and AS, containing traces of Fe. Cu. Al,
were mixed at 15:85 ratio and molten in an induction
furnace with argon atmosphere. The obtained alloy was
deformed, homogenized 0at 9500 C for 2.5 hr, powdered and
recrystallized at 300 C for I hr, after which the
crystals became about 1 to 2 ~L The powder was stuck
on a copper plate, fastened at the crid of an electric
heater, and placed on the axis of the X-ray goniometer.
Two to three diffraction intensity curves were obtained
Card 2/4 for each desired Interval of temperatures which were

Characteristic Temperature of an Ag-Au
Alloy Within a Temperature Range From
279 To 5230 K
Card 3//h
77703
sov/148-6o--1-26/34
controlled by a thermocouple. The method proyIded
compute
+2.5% accuracy of the d 0 The mean%0 for Ag
was found to be 208-50 K which is within 203 ts 2150 K
of values determined by v~~rious investigators by means
other than X-ra9S. The V for the Au-Ag alloy at the
intervals of ( K): 279-370, 279-423, 279-474, and
279-523 were 200, 197, 194, and 2000 K,respectively.
Their average, 1970 K, is close to the value determined
by R. W, James (198' K)Vaccordin� to the elasticity
method. The static or chemical distnrtion of the Ag
structure due to the presence of dissolved Au proved t-,
equal zero. This fact is the obvious result of 0nly
0.17% difference between the atomic radii of Ag and Au.
The Debye-Waller intensity connections proved to remain
valid for the entire temperature interval used in the
experiments. The connections are for many solids,
composed of less heavy atoms, restricted to much
lower temperatures. This is because of the inversel,r
proportional relation of the amplitude of thermal

Characteristic Temperature of an Ag-Au
Alloy Within a Temperature Range From
279 To 523' K
777'03 '
soli/j.48-6o-1-26/3h
vibrations of atoms to the square root or m02 In
which atomic mass in 10 h-Igh for boLh Au and Ag. Th-~-~ r e
is 1 figure; and 9 references, 4 Soviet, 4 U.K., 1
Danish. The U.K. references are; M. Blackman, Phi-,!
Mag., 42, 1951; R. W. James, G. W. Brind~ey, Proc.
Roy. Soc., A 121, 155 1928; R. W. Jameo, F. M. Firth,
Proc. Roy. Soc., A -117, 62, .1927; 11. W. Jameo,
Manchester Memoirs, 71, 9, 1926-1927.
ASSOCIATION: Moscow Steel Institute (Moskovskiy institu~ st-ali)
SUBMITTED: December 15, 1958
Card 4/4

GORELIK., S.S.; PAVLOV, A.M.; UMAMKIY, U.S.
Conroction between the type of crystal lattice., the diffusion
coefficient., the interatomic bcalift forces and the temperature
of recryatallization. Izv., vys. ucheb. zav.; chern. met. no.2:
95-99 160. OUFJi 15:5)
1. Mookovokiy institut.
(Allop.-Metallography) (Crystal latticos)

/,P. '.2 0 0 8/14 6/60/OW/002/007/008
A~~A Mozzhukhin,. Ye.I., Yelyutin, V.P., Umanskiy, Ya.S.
TTIM The Effect of Sinter,4Conditions on the Strength of Carbide
Base Alloys Carb_ur_fz__e& by a NiAl Compound
-;N V
PERIODICALs Izvestiya vyashikh uchebrqkh zavedeniy, Chernaya ~etallurglya,
196o, Nr 2, pp 142 - 147
TEXTt To determine optimup sintering conditions ensuring the pre-
paration of h1P_h-gtrenR,&L_Wjyys,~1 the authors studieq the effect of various
sintering conditions on the properties of Ti-carbideO~tnd TI-W-carbida-4base
alloys oarburized by a Ni-Al compound. Th&, effect of sintering conditions
on the strength of alloys during bending tests at room and elevated tempera-
tures- was mainly studied. Students of the Moskovskly institut stale Qfoscow
Steel Institute). Yg.A- Bychkova, L.V.-Maksimova and Ye.I. Oginskaya took an
active part in the studies. The carburizing alloys contained 54 760% (at)
Hi. The gl~en theoretical compositions of the investigated alloys are con-
tained in Table 1. The specific weight of Ti-W-carbides was calculated from g/c 3
the weight and volume of +.be carbide component In hard alloys. It was 11.4 M
Card 1/ 4 q/

,s/l48/6o/boq/Oo2/Oo7/0o8
The Effect of Sintering: Conditions on the Strength of Car-bide Base Alloys
Carburized by a NiAl Compound
for T15 carbide, 6.16 g/cm3 for T60 carbide. The alloys wera prepared of T1-
carbide powder and complex Ti-W-carbides. Powders of the initial material
were mixed in alcohol for 48 hours, dried in air, pressed Into briquets and
drie,d in a vacuum cabinet. Sintering was carried out In argon and hydrogen
atmosphere, in a laboratory vacuum furnace with a graphIte shaft and in a
TVV-2 furnace. Optimum sintering conditions were determined from the. results
of measuring the strength, hardness, specific weight, and changes in the com-
position of the alloys. Greatest changes in the -composition were obaeTNed in
sintering TI-carblde-base alloys in a vacuum. Loss of tndividual components
through sintering was calculated after sintering in a vanuum, hydrogen and
argon for 1 hour at 1,7000C, The loss amounted to 15% T1, 67% Al and 13% C
of the tot&1 amount of the component In the alloy prior to sintering.
Minimum loss was observed in sintering In pure argon, Table 2 contains the
composition of the T100B (15) alloy prior to and after sintering under
different conditions. 1he strength of alloys during bending waQ. Investigated
with the aid of a special device on a two-ton testing machine at high temperature-s
card 2/ 4 ~r

3/148/60/000/002/007/008
The Effect of Sintering Conditions on the Strength of Carbide Base Alloys
Carburized by a NiAl Compound
without shielding atmosphere. Figures 1 5 show the effect of the sintering
temperature on the alloy strength during bending. Highest strength of Ti-
carbide base alloys was obtained by sintering for l.hour at 1,9000C. A raise
of the sintering temperature up to 2,1000C did not affect the strength (Figure
1), although shrinkage and density of the alloys increazed. Extended holding
up to four hours entailed decrease in strength; holding time reduced down to
0.5 hrs entailed a decrease in density. The authors contradict the statement
made In [Ref 4] that the optimum temperature of sintering for a TiC-NiAl alloy
was 1,6500C. They proved experimentally that alloys of highest strength and
density were obtained at 1,9000C and above. It was establi'ahed that optimum
mechanical propertles of the alloys depended on the optimum amount of the
liquid phaie during sintering. To obtain this, alloys with a lesser rzontent
of binder should be sintered at higher temperatures which r9ise -the amount
of the liquid phase due to the dissolving of the carbide component..
Card 3/4

S/148/60/000/002/007/008
The Effect of Sintering Conditions on the Strength of Carbide Base Alloyu
Carburized by a NiAl Compound
There are% 2 tables, 5 graphs and 7 references, 6 of which are English and
1 Soviet.
ASSOCIATIONs Moskovskiy institut stali (Moscow Steel Institute)
SUBMITTEDi May 25, 1959
card 4/4

8583.1
s/i48/6o/ooo/Oo3/oi5/oi8
4.0to A16i/AO29
AUMORS: Mozzhukh1n, Ye.l.; Yelyutin, V.P.; Umanskiy, Ya.S.
A 1,
TITLE: Strength of Carbide Alloys Cemented by iAl and CoAl Compounds
PERIODICAL: Izvestlya vyssh.1kh uchebnykh zavedeniy. - Chernaya metallurglya,
1960, No. 3, PP. 131 - 135 61
TEXT: An investigation was carried out with titani and titanium-tungsten
carbide powder bound with NiAl and CoAl compounds. The effect of the composition
and of different quantities of the binders was determined. The results are illus-
trated by curves. In case of titanium carbide with 15 volume % NiAl the binder
composition had no effect on the alloy strength at room temperature, but a pro-
nounced effect was observed at 1,0000C. Alloys bound with binders of stoichiome-
trio composition proved strongest, and alloys bound with NiAl with 6o atomic %
Ni weakest. Alloys with overo25 volume % NiAl have the maximum strength. The
strength of TiC-NiAl at 1,000 C was in all cases higher -than at room temperature,
which not fully corresponds to statements made in a previous investigation (Ref.3).
The alloy with high NiAl content had a considerably higher heat resistance than
with low NiAl content. Titanium-tungsten carbide T-15 (T-15) and T-6o (T-60) were
bound with CoAl with 60 atomic % Co, with 10 and 15 volume % CoAl, respectively.
Card 1/2

s/i48/6o/ooo/oo3/oI5/Oi8
Strength of Carbide Alloys CL-mented by NiAl andCoAl Cbm - A16l/AO29
pounds
A higher strength was observed in alloys with 15 and 20 volume % of NIAI at 9000C
than in cold which is explained bv higher plasticity of NiAl at 9000C. At higher
temperature the alloy strength dropped. The high strength of TiC-NIAI alloys in
hot state is apparantly also due to the plasticity of NiAl and stress redistribu-
tion. This phenomenon had been observed by G.S. Kreymer, O.S. Wonova and A.I.
Baranov (Ref. 4) in WC-Co alloys (maximum strength at 2000C due to softened cobalt.)
The following conclusions were drawn% 1) Titanium carbide alloys bound with NiAl
have higher bending strength at 1,OOOOC than at room temperature. 2) Titanium-
-tungsten carbide alloys with 16% titanium carbide bound by NiAl retain their
strength up to 900-1,0000C. 3) Titanium-tungsten carbide bound with CoAl has a
higher strength than analogous alloys bound with NiAl. 4) At room temperature
the strength of titanium carbide alloys does not depend on the composition of NiAl,
but at 1,0000C it does. At 1,OOOOC alloys bound with NiAl of stoichiometric com-
position have maximum strength. 5) The carbide base composition is important for
alloys bound with NiAl and CoAl. Alloys with pure titanium carbide and titanium-
tungsten alloys with high titanium content (64% TiC) have low strength at room
temperature, but they retain their strength or even increase it at 1,000 - 1,1000C.
There are 4 figures and 5 references: 3 Soviet, 2 English.
Card 2/2

82340
?.5-0 0 S/139/6o/ooO/03/037/045
EO 9335
AUTHORS: Mirkin, L.I. and UmAn-ctkiy,
TITLE: Investigation of the State of the Crystal Lattice and
the Density of Dislocations in Aust6nite and Ferrite
During Phase Transformations
PERIODICAL: Izvestiya vysshikh uchebnykh zavedeniy, Fizika,
1960, No 3, pp 212 - 217 (USSR)
ABSTRACT: The block dimensions and Type II distoTtions in the
a-phase of carbon ahd alloy steels after various types
of heat treatment were measured and the results were
described in numerous papers by the School of
G.B. KurdNnov. However, only very few papers are
devoted to the intra&Canular structure4f the gamma-
phase (Refs 1,2). The authors consider it of interest
to investigate the intragranular structure of the a-
and y-phases In steels after various heat tr "atments.
The experiments were carried out oil steel 45W6.4%0 C)
and on austenitic manganese steel Mn). which
were quenched from temperatures between 600 and 1 200 C
and tempered at tomperatnres of 200 - 700 OC with a
Cardl/3 wl***'

8234o
S/139/60/000/03/037/045
Investigation of the State of the CrYENUE222tice and the Density
of Dislocations in Austenite and Ferrite During Phase Transformations
soaking time of I hour. The investigations were carried
out using Fe radiation on URS-50I equipment. The authors
proposed using the method of determination of the density
of dislocations from the widening of the lines on the
X-ray diffraction patterns for studying heat-treatment
processes. Data are given on the change of the dis-
location densities of the austenite and ferrite during
quenching and tempering (Tables 1,2). On the basis of
the obtained results, the authors propose the following
mechanism for the dialocationsf(during quenching and
tempering: during quenching of steel a large number of
point defects and dislocations occur in amphase crystals
during y-a transformation and these are concentrated
at block boundaries and distr buted inside the block,
i.e. distorting the lattice.~nhc increase of the number
and length of the dislocations inside the block corresponds
to the increase of Type II distortions whilst an increase
of the number of closing loops (relaxed defects)
Card2/3 corresponds to an increase of the degree of dispersion az

82340
S/139/60/000/03/037/045
80~J~Ej3kattice and the Density
Investigation of the Sate of the r a
of Dislocations in Austenite and Ferrite During Phase Transformations
of the blocks. Thus, the density of dislocations
characterises both elements of the fine crystalline
structure, namely, the block dimensions and the Type II
distortions. There are 3 figures, 2 tables and
9 references, 7 of which are Soviet and 2 English.
ASSOCIATION: N11 tekhnologii avtomobillnoy promyshlennoBti
'(Scientific Research Inatitute oLl Technology of the
Automobile Industry)
Moskovskly institut stali (Moscow Institute of Steel)
SUBMITTED: July 9, 1959 PK
Card 3/3

805,97
S/148/60/000/005/007/009
/.230
AUTHORS- Skakov, Yu.A., Umanskly, Ya.S.
TITIS% Investigation Into Changes of Fine Intergranul4r Structurdlor
a Composite Cobalt-B~~ ~1M__(j_4ONKhM)%11n Plastic
Deformation and Annealing
PERIODICAL; Izvestiya vyssikh uchebnykh zavedeniy, Chernaya metallurgiya,
1960, Nr 5, PP 150 - 158
TEXT: The K4ONKhM alloy [Refs 1, 2] is strengthened in a high degree
during plastic deformation and is, moreover, subjected to considerable addi-
tional strengthening by low temperature annealing. The authors investigated
the character of structural changes corresponding to strengthening and softening.
The composition of the alloy is given: 0.08% C; 36.4% Co; 20.1% Cr; 15.25%
Ni; 7.05% M6; 16.3% Fe; 0.40% Si; 1.82% Ma. The alloy specimens were sub-
Jected to cold rolling (10, 30, 50 and 70% compression) after water quenching
from 1,1500C. Tempering was carried out at 1000 to 9000C for four hours. At
5001C the tempering time was changed from 2 to 100 hours and at 7000C up to
18 hours. Microhardness of all specimens was measured. The experimental work Vr
Card 1/3

80)7
3/148/60/000/005/007/009
Investigation Into Changes of Fine Intorgranular Structure of a Composite
Cobalt-Base Alloy K40HXM (K40NKhm) In Plastic Deformation and Annealing
was performed with the participation of AN. Sharshatkina-and students of
MIS L.K. Kostlif kid M.M. Arengolld, D I GabEI21yan and other collaborators
of IPS TsNIIChM,_in particular V.A. Sol't , assisted in the selection and pre-
paration of the test items. Results of experiments are described in detail
and the following conclusions are drawn: Strengthening of the alloy by cold
plastic deformation and additional strengthening by heating up to 5000C depend
on the same factors, i.e. crushing of mosaic domains (down A0 10-6 cm) and
large microdeformations of the crystalline lattice of the solid solution
(up to --:~4.10-3). However, the significance of these strengthening factors
is different in deformation and strengthening tempering. If the degree of
compression increases from 50 to 70%, strengthening depends on further
crushing of domains; additional strengthening in low tempering of a strongly
deformed alloy depends mainly on changes in the character of distribution of
microdeformations and their gravrth. Microdeformations of the crystalline
lattice are mainly caused by the fine concentrational heterogeneity in the
solid solution. Differentiation of components (first of all molybdenum and
carbon) takes place in the zones with dimensions of the order of 10-6 cm. A
Card 2/3

S/148/60/000/005/007/009
Investigation Into Changes of Fine Intergranular Structure of a Composite
Cobalt-Base Alloy K40HXM (K4CNKhM) in Plastic Deformation and Annealing
higher degree of compresslon, an extended time or higher temperatures of
tempering, entail enlarged localization zones of microdeformations in the
crystalline lattice of the solid solution; (or enlargement of solid solu-
tion zones with higher concentration of Mo and C). Such a structure precedes
the separation of the carbide phase and corresponds to maximum hardness. The
separation of the carbide phase is accompanied by the elimination of micro-
deformations of the crystalline lattice and by the sharp enlargement of mosaic
structure domains, which causes softening.
There are: 5 sets of graphs, 1 set of microphotos and 6 references, 4 of
which are Soviet, 1 French and 1 English.
ASSOCIATION- Moskovskly institut st ali (Moscow Steel Institute) VK
SUBM1=-. April 1, 1959
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S/07o/60/005/003/024/o24/xx
E132/E46o
AUTHORS: KajKan, A.S., Somenkov, V.A. and Umanskiy, Ya.S.
TITLE., An X-Ray Camer Studying the Diffuse Scattering by
Polycrystalri-ne Materials
PERIODICAL:Kristallograflya, 1960, Vol-5, NO-3, pp.468-469
TEXT~ There are stricter requirements in the use of diffuse
scattering methods in metal physics than in ordinary structure
analysis. Air se-attering and slit scattering must be reduced and
the monochromatization must be of a high standard. An a Y"chment
for the YPC -501 (URS-501) diffractometer which satisfies these
conditions is described. It is basically a cylindrical enclosure
with celluloid windows which surrounds the specimen. The
enclosure can be evacuated. Slits are provided for removing
radiation scattered by the air outside the enclosure from the
primary beam from the monochromator. A crystal of Ge (111 plane)
is used for monochromatization as it gives no 222 reflexion. The
333 reflexion is suppressed by reducing the tube voltage. When
there is no specimen and the direct beam passes straight through
the camera, the count rate recorded is equal to the cosmic ray
Card 1/2

S/07o/60/005/003/024/024/XX
E132/E46o
An X-Ray Camera for Studying the Diffuse Scattering by
Polycrystalline Materials
count rate. The apparatus can be used to record the diffuse
background between 8 and 45% Its operation has been tested with
specimens of fused quartz and Cu. Comparisona with the theoretical
scattering are reproduced and appear satisfactory. There are
3 figures and 4 references: 2 Soviet and 2 English.
ASSOCIATION: Moskovskiy institut stall im. I.V.Stalina
(Ro-sc-ow Steel Institute im. I.V.Stalin)
SUBMITTED: November 18, 1-959
Card 2/2

KAGAN, A.S.; SOHMMV, V.A.; MUNSKIY, YA.S.
Diffuse scattering of X rays by a Cu-A1 alloy. Kristallografiia 5
no.4:540-543 Jl-Ag 160. (MIRA 13:9)
1. Moskovskiy institat stali, im. LV. Stalina.
(Copper-aluminum alloys-Spectra)
(X rays-Seattering)

XAGAN, A.B.; UMANSKIT, U.S.
--------------
Cameras for taking pictures at high and low temperatures, attached
to the M-50 I unit. Zav.lab. 26 no.1:108-109 160.
(MIRA 13.5)
lo Moskovskiy institut stali imeni I.V.Stalina.
(X rare-Squipment and supplies)

vl*'_~_-
')~o 0
AUTHORS:
TITLE:
PERIODICAL:
ABSTRACT:
Cardl/3
8088-t
S/l26/6o/oo9/o6/oi4/o25
;075/E335
Mirkin, L.I. and Umanskiyj Mae
Crystal Lattice and of
State
pp 897 - 902 (USSR)
of the
Investigation of the
the Density of Dislodations in the Case of Wa-se Trans-
formations in Steels'4
Fizika metallov i metallovedeniye, 1960, Vol 9, Nr 6,
This paper was presented at the Sixth All-Union Conference
n Using X-rays for Investiga.ting Material, held in June,
'1956.
The authors investigated the intracrystalline structure of
steel 45,_containing 0.4a,o C, and of austenitic manganese
steel, containing 0.4% C and 12% Mn 6 after quenching from
temperatures between 600 and 1 200 C and tempering at
temperatures of 200 - 700 0C. They consider the problem
of selection of a standard in determining the dimensions
of blocks and type II distortions in the material. The
authors propose application of the method of determination
of the density of dislocations from the widening of the
lines on X-ray patterns for the purpose of investigating
processes taking place during heat treatment. As a result
4/

8088-7
s/i26/6o/oo9/o6/oi4/025
2?7~4f~jge
Investigation of the State of the Crysta and of the
Density of Dislocations in the Case of Phase Transformations in
Steels
of the experiments, data were obtained on the changes
in the density of dislocations in the austenite and in
ferrite during quenching and tempering of the steels.
The authors propose a probable dislocation mechanism of
the processes taking place in a and y phases during
quenching and tempering of steelst during quenching of
steel a large number of point defects and dislocations
occur in the a phase during y-a transformation, which
are concentrated at the block boundaries and distributed
inside the block, i.e. distorting the lattice; increase
of the number and the extent of such dislocations inside
the block will bring about an increase in "type II"
distortions, whilst an increase in the number of closed
chains (relaxed defects) will correspo'nd to an increase
of the degree of dispersion of the blocks. Thus, the
density of the dislocations characterises both the block
dimensions and the type II distortions. In the case of
Card2/3 quenching of steels with a mixed y +~a structure, the

80887-
s/126/6o/ooq/o6/oi4/O25
Investigation of the State of the CryJ013tEj~ Ice and of the
a a
Density of Dislocations in the Case of Phase Transformations in
Steels
mechanism of these processes changes to some extent.
There are 5 giguvs and 11 references, 9 of which are
Soviet and 2 English.
ASSOCIATION: Moskovskiy institut stali im. I.V. Stalina
(Moscow Steel Institute imenL_L.V, in)
SUBMITTED: July 25, 1959
Card 3/3

S/020J60/132/01/28/064
BO14/B014
AUTHORS: Kalikhman, V.L., Umanskiy, Ya.S.
TITLE: Investigation of the Initiql Stages of ithe Formation of Diffusion"
Porosity in the Alloys L621$and N8OKh2d by Using the Metho-di-o-f-
Small-angle Scattering f X-Raya
PERIODICAL: Zoklady Akademii nauk SSSR) 19609 Vol. 132, No. 1, ppo 108-109
TEXT: The formation of porosity by elimination of the volatile component of
alloys was studied in a vacuum chamber by using 0. Kratkyls method (Ref- 4).
As a result of the elimination of zinc, the samples of the L62 alloy were in
an atmosphere saturated with zinc when they were annealed at 7500. Similarlyg
the samples of the alloy of the type N8OKh2O were in an atmosphere saturated
with chromium when they were annealed at 12000. The results and the X-ray
pictures shown in Fig. 2 are discussed. From the results obtained it follows
that the pores begin to form on the surface of impurities. First, thin cracks
are produoedq which expand along the surface of the impurities. These results
agree with the fact that the tendency to form pores is closely connected with
Card 1/2

Investigation of the Initial Stages of the 7ormation 8/020/6C)/132/01/28/064
of Diffusion Porosity in the Alloys L62 and N8OKh20 by BO14/BO14
Using the Method of Small-angle Scattering of X-Rays
the amount of impurities. There are 2 figures and 6 references, 2 of which are
Soviet.
ASSOCIATION: Mookovskiy institut stali im. I.V. Stalina (Moscow Steel
Institute imeni I.V.Stalin)
PRESENTED: December 29, 1959, by Cr.V. lurdyumovq Academician
SUBMITTED: December 28g 1959
Card 2/2

/A
AUTHORS:
TITLE:
PERIODICAL:
S/020/60/132/02/22/067
B014/13007
Kagan, AaS.9 Umanskiy. U.5.
The Anomalies 'of the Thermal Paotor of the Scattering of X-Rays by
Cr'V1CU - Zn and Ni - 7 Alloys
71
Doklady Akademii nauk SSSt, 116o, Vol. 132, No. 2, Pp- 326-328
TEXT: In the introduotion. the authors refer to the assumption of the Debye-
distribution of thermal waves according to frequency, which was made when
determining the characteristic temperature. The actual spectrum in all oases
deviates more or less considerably from this assumption. In the present aper
the results obtained by investigations on a nickel-ohrome alloy with 21 Cr, on
a-brass with 31.6% Zn, and on a nickel-alloy with 8% V are given. The X-ray
diffraction studies were carried out by means of CuKa-emission; determination
of the characteristic temperature by means of the modulus of elasticit carried
out according to a method previously described by the authors (Ref. 16~. The
investigations on the niokel-chrome alloy were carried out both on samples,
which were in the K-state and on such in which there was no K-state. Investi-
Card 1/3

The Anomalies of the Thermal Factor of the Scattering 5/020J60/132/02/22/067
of X-Rays by Ni - Or, Ou - Zn and Ni - V Alloys BO14/B0O7
gation of the Cu-Zn-alloy was carried out both on samples which had a regular lat-
tice and on samples with a disordered lattice. The pre-treatments of the samples
are briefly discussed, and measuring results are shown in the diagrams of
Figs. 1-3, in which the dependence of the logarithm of relative intensity on
temperature is graphically represented. In tables 1-3 the calculated oharacteris-
tic temperatures are given. It is found that the characteristic temperature
of the samples determined in two ways differs, and besides, %e characteristic
temperature determined by means of X-ray diffraction study in the temperature
range of liquid nitrogen up to room temperature and in the temperature range
from room tempe~oature up to higher temperature differs. Only for brass in the
ordered state is this difference near the measured error. When discussing the
results obtained, the authors point out the fact that in high-temperature
measurements it is not the shape of the spectrum but the maximum frequency that
exerts an influence upon the thermal factor. The causes of the anomalies of
the thermal factor must be explained by investigations of the diffuse scattering
on monocrystals. The authors thank Yu.A. Rymashevskiy for his assistance in
measuring the moduli of elasticity. Theri-are -3figuresp 3 tables, and 18
references, 7 of which are Soviet.
Card 2/3 q1

The Anomalies of the Thermal Factor of the Scattering
1/02Y60 132/02/22/067
of X-Rays by Hi - Or, Ca - Zn and Ni - V Alloys B01 , B007
ASSOCIATION: Moskovskiy institut stali im. I.V. Stalina (Moscow Steel Institute
imeni I.V. Stalin)
PRESENTED: December 29, 1959, by N.V. Belov, Academician
SUBMITTED: December 26, 1959
Card 3/3

83560
S102016011341001101 2/021
t13 ~(o B004/BO60
AUTHORS: Bogorodskiyq 0. V., Umanskiyq Ya. S., 11il'shteyn, S. 8h.
Mffv~_ N.
TITLE: On the Nature of the Mosaic Structure of Single Crystals
of Germaniumand Silicon
PERIODICAL: Doklady Akademii nauk SSSR, 1960, Vol. 134, No. 1,
PP- 114 - 116 LY
TEXT: The authors wanted to check the dislocation character of the
Mosaic Structure (Figo- I)q and studied single crystals of germanium and
silicon that were drawn from the melt along the (Ill)-axis. The samples
used.were 2-3 mm thick foils cut perpendicular to the (Ill)-axis. It
was established by etching that almost all of the dislocations exhibited
the Burgers vector a/2 (lfO). In.some cases, the authors observed lines
which corresponded to_small-anffle boundaries. The2densiIyaof2surface
dislocations was 102 100 for germanium, 10 - 10 m for
silicon. The principle of the X-ray analysis is described (Fig. 2). The
monochromatiq X-ray beam is reflected from the crystal I, and hits on
crystal II whioh is rotated around small angles. The authors used the
Card 1/3

83560
On the Nature of the Mosaic Structure of
Single Crystals of Germanium and Silicon
s/o2o/60/134/001/012/021
B004/BO60
W-500 (URS-50I) apparatus with Geiger counter. The curve of the in-
tensity of double reflection of I as a function of the angle of rotationp
is defined as rotation curve. The authors constructed a special gonio-
meter head which allowed rotations around small angles rith an accuracy
of 0-5". The rotation curves obtained experimentally are shown in Fig-3o
the data are given in Table 1. The distances between'the iaxima equal
the'disorientation angle of the crystal blocks. Experimental data show
that the Ge single crystals have a mosaic structure with all disloca-
tion densitiea~ while'the diaorient4tion angles of the blocks change
-.littlao'although the disloeation densities diffei by four orders of
magnitude. This cannot be explained by the Burgers m6ael. In silicon,
the blocks are considerably smaller; which likewise contradict's the
Burgers model, since the lattice constants of Ge and Si are little
different. The germanium crystals with small-angle boundary showed
fragment structure. The authors arrived at the conclusion that the block
boundaries in Ge and Si may be connected with dislocationsk but not ac-
cording to the meohanism of the sm&ll-angle boundary. Also structural
defects might play a role here. The interfaces between the fragments,
on the other hand, nonsist of dislocations in agreement with the
Card 2/3

8 3 56 0-
On the Nature of the Mosaic Structure of S/020/60/134/001/012/021
Single Crystals of Germanium and Silicon B004/Bo6o
Burgers model. Thus, the nature of the block- and,fragment boundaries
is different. There are 3 figures, I table, and 5 references: 2 Soviet,
I US, and 1 German.
ASSOCIATION: Moskovskiy institut stali im, I. V. Stalina (Mos0ow
Steel Institute imeni 1. V. Stalin)
PRESENTED: April 26, 196o, by P. A. Rebinder, Academician
SUBMITTED: March 2, 1960
Card 313

GALIFERIV, Ye.L. [translatorl- U14MISKIY, Ya.S., red.; MMKOV, Ye.A.,
red.; ELIKIND, L.M., reY. Tz7--va;-=MViCH, M.K., tekhn. red.
(Theory of phases in alloys; collection of articles on reports read
at a conference on the theory of phases in alloys. Translated from
the Englishl TeoriJa faz v splavakh; sbornik statei po dokladam, pro-
chitannym na seminare po teorii faz v splavakh. Moskva, Gos.nauchno-
tekhn.izd-vo lit-ry po chernoi i tsvetnoi, metallurgii,, 1961. 353 Pe
(MIU 14.-412)
(Phase rule and equilibrlum) (Alloyo.-.Metallograpby)

"' " V *
MIRKINg Lev Iosifovich; UMANSMV Ya S , prof.t red.j GOLIDERp G.A.# red.;
MAKAROV, Ye.F.t Fe~,-"~~I* ~qia,t teklm, red,; TUMARWA, N*Aop
tekbn, red,
(Manual on X-ray diffraction amlyaiB of polyerystals] Spravoohnik po
rentgenostruktumomu analizu polikristallov. Pod red. IA.S.Umanakogo.
MosWaj Goa, izd-vo fizikb-inatem. lit~-ryg 1961. 863 p. (KUIA 14:8)
(X-ray crysta;logtapby)

S113 9/61/000/004/018/023
E021/E480
AUTHORS-, Kalikhman, V..L, and Umanskiy, Ya,S.
TITLE: X-Ray measurement of total sub,microporosity and of
pore size, arising during the mutual diffusion of
copper and nickel
PERIODICAL:. Izvestiya vysshikh uchebnykh zavedeniy- Fizika,
no.4. ig6l,. 14o-145
TEXT, Studies were carried out on the increase in 3ub~,microporosity
during the process of mutual diffusion of copper and nickel. using
the apparatus for recording low-angle reflections with a slit
arrangement proposed by O~Kratky (Ref,2~ Kolloid-Zeitschrift, 144.,
110, 1955) with slight modifications, Samples were prepared in
the following way. 10 micron thick ni~~kel foil was annealed for
2 hours at 1000% and placed between two sheets of 20 micron thi:-k
,copper foil- The surface of the foil was electropolished and
washed in a,-;etone, The sandwich was clamped and heated in vacuo
at 9000C for 15 minutes, This was suffi:~ient for diffusion
welding to take plar_e~ Diffusion traotmant was carried out at
10000C for 5 to 160 minutes and at 900"'C for 15 to 240 minutes in
Ira Cuo IThe ciampIcs worp tJir_-, Low angle
G;-Ird 1/3

s/i3q/6i/ooo/oo4/oi8/o23
X- Ray e !-,I en t ~~f L., L a I E021/E480
reflections were obtained from the samples before and after,
heating, Tlic. lour iningle effect was :~aus_--d by imperfections of the
foil surface, as 3hown by its in-crease with an increasing number of
fo-L1 layers, The lcw angle refle--tions were 3 to 4 times more
lntc-nz_~c -nfller sintering, being 2 x 1o,3 of the intensity of the
In z
itla.l bc:aul'. Thus, the effee;t must be --aus6d, in the main, by
submi-.rop.7,~-r~3 formed as a result of the difference in part3al
,;Oeffi~_,ents of diffusion of the sintered metal3, Generation of'
pores had already started even after 15 minutes at 900C. The
min.imum size of pore was a-bout 300A after this time, Obvioualy,
this must have been :~Iose to the ~ritir_al size for nuicAeation,
With increasing time the pore size -Ln.:.reased because of
coagv_lation of po_rz;3. Tbi~ pxc.-es_= of )_ncr,~~ase in pore sizs, in
the initial stages, wa3 ob-riou6iy auto-la-:a-Lyt!~:, The total
~Polume of Subnacros--c-pL_ por.,:~-Ity ivas of' the o_-der of lo-3 of tha
volume of '-he -zampl-_ S.T ml-r-tioned in the
Th.,-,~ and 9 3 Soviet and
6 non rii,~. fniii- to Engli3h language
publi_~iition-i -~Cad 13 fOll-;~WSI: Ref~4 A, (.%Uj,nic-r. G,, Fournett.
Small -angle ---attaring of X -_raya , L-_-rckn, 1955,
Ca:~ d 2/3

S/139/61/000/004/018/023
X-Ray measurement of total E021/E480
Ref.5P A. Guinier. J. of Appl. Phys- 30, No-5. 1959:
Ref-7: W.T.Ogier, R.L.Wild, J.C.Nickel. J. of Appl. kys., No-3,
19591 R6f.8g R.H.Neyamber, W.G.Brammer, W.W.Beeman, J. of Appl,
Phys., No.5, 1955.
ASSOCIATION? Moskovskiy inatitut atali imeni I.V.Stalina
(Moscow Steel Institute imeni I.Y.Stalin)
SUBMITTEDg
july 4, ig6o
Card 3/3

2U99
8/1-29/61/000/007/014/Olb
L07 VE5 35
~-,vtrAkhantxov. j.M., Gromova. $.V., Kalikhman, V.L.
and Umanskin Is.
knCittence of viffusion Porosity in a Ntchrome Alloy
on the Sintering of Ntckel and Chromium Powders
VARIOPICACv Met4liovedenlye i termicheakaya obrabotka m*t4ilov,
k9bl, No,7, pp,12-14
N:.:,1, in *tudylng the procoms of sintering of nIckel and
t~hromtxjm the authors dxacoverad some unusual. changes or the latti,ce
pre.,od and the shape of the linem on X-ray ditTraction patterns
of tho nichromo Hr;QX'aC) INSO%20). Vor the j.nvestigations,
Apecanens ou varioum densities tporositles W-1.5, J5-3U and
40-/Oillk) weru prepared by cold previh%ng., The specimens were
61rit.vred in it hydrogen stream at 1150"'C for 8 hours. X-ray
diff'racti,on pattorns were made ustnig a molybdonum i,eforence
RtAndArd with cappor radiation.. Th# lattice poriol woo calculated
from the Itno (4~40, It was found that during wintering thip
14t0ce period did not change monotonously bul, in jumps, Fig,,l
shovA the dependance of' the lattice period, A. of' aLntered
f.;ard I/#

211"99
LnfLuence of r)ilrunion Porosity 5/129/6i/ooo 007/014/ol6
9(173/9533
niz.hrnme an the Rintering time, hours. for the following initial
periodsi curve I - 15-UK', curve 2 - '5W, curve 3 - 40-41%.
During xho L'ire~t three hours of sinter:ing, thin mnxkma and minima
of the lattice perlodt- did not coinvide for spectmens with various
pot-014 it ieh Ihowover, during the later st;dgov oC aintering they
are synchi-onous for all the mpec-imens. There Is a similar change
in the blurring or the lines on the .1-ray diffrnction patternv,~
the lines are blurred or sharp right up to the division of the
KOL doublet, 1he sharp lines correspond to larger lattice
periods. S,imilcir phenomena were observed by n,, S. Gorplik
(flef,L-, Nauchnyye daklady vysahey shkoly, Metallurglya, No.2, 19i9)
during sintertng of LunLCO alloy. These phenomena indicate that
sinter.tng of nickel anti chromium powders does not changb
monotonously the uniformity of the solid solution, This can be
explained on the basis of results of the study of the formation
and growth of sub-microporosities in the nichrome aLloy, Porosity
wafc nhaarvod in An alloy of a similar compositton 1211-1~ Cr) (luring
the distillation f chromium in vacuum at various temperatures.
The dxmensions of' the sub-micropores were determined by studying
the low angle scattering of X-rays. Fig.2 shows the text-rig
Card 2/6

Influence of Diffusion Porosity
2)t199
S/129/61/000/007/01/i/oi6
r-073/E535.
used for studying the low angle scattering (1 - X-ray tube,,
.2 - monochromator, 3 specimen, 4 - collimator, 5 - Cieiger-
Muller counter,, 6 - counting circuit). it was found that sub-
.microscopic pores of a size of several hundred Angstrom form in
the nichrome during the process of evaporation of chromium. Fig-3
shows the dependence of the average pore dimensions, r1o, A, and
of the total porosity (loss in weight),AA P, mg, in nichrome
subjected to vacuum evaporation at various temperatures as a
function of time, T min for the sintering ternijeratures
12000C (plot a) and 13500C (plot The dimensions of the
sub-micropores also did not change monotonously; the lower the
evaporation temperature the larger will be the number of extremal
points on the curve R f(FT The observed phenomenon can be
explained only by the healing of the formed sub-micropores, since
the maximum dimension of the pores was considerably below 10(h)
Healing proceeds as a result of chromium difftision; its partial
diffusion coefficient in nichrome is considerably higher than the
diffusion coeffici'ent of nickel (Ref.4. S. Dashman: 116cientific
fundamentals of vacuum engineering", Russian translation, 195u).
Card 3/6

Influence of Diffusion Porosity
21
s 12 96 1 /0 0 00 0 71 ji o 16
EOWE535
-T-
In this case healing is possible if the flow of chromium atomt.
to the pore is larger than the flow of~vacancies. After the
pores have healed, section4 will remain which are chromium
enriched and the internal flow of vacancies will cease. The
~appearance of concentration non-uniformitiet; leads to blurring of
a reduction of' the lattice
the lines on the X-ray pattern and to .
period. By means of low angle scattering it is also possible to
detect the decrease in the pore dimensions. Then, the chromium
concentration begins to equalize in the alloy and the concentra-
tion of vacancieswill. increase; this prodtices a narrowing of the
lines on the Debye pattern. An increase in the concc-atration of
the vacancies leads to the formation of new and growth of
-remaining pores. The concentration of vacancies will decrease in
jumps and the.process of healing of the pores will start afresh..,
This process appears to continue until a certain quantity or
chromium is evaporated rro m the alloy. Ther%tare 3 figures
and 4-references: 3 Soviet and 1 a Russian tra. slation.
..ASSOCIATION: Moskovskiy institut stali (Moscowl5teel-jinstitute)
Card 4/6

KALI191MAN, V.L.; UMANSKIY, U.S.
Determining the orientation of the diffusion submicropores in
ci-brass by the method of omall-angle scattering of I rays.
Fiz.'tver.-tela 3 no.2031-335 F 161. (MIRA 14-,6)
1. Institut stali, Moskva.
(Diffusion)
(X rays-Industrial applications)

KAGAN, A.S.; UMANSKIY, U.S.
Relation between the X-ray characteristic temperature and
the spectrum of slastie vibrations. Fiz. tvar. tela 3 no.g:
2683-2687 3 161. (MMA 14:9)
1. Moskovskiy institut stali imeni I.V. Stalina.
(Crystals) (X-rays)

ASTRAKROTSEV, S.M.; MOZZHUKHIN, Ye., I.;
Investigation of sintered alloys on the basis of HiAl meta2lic
compounds. Izv. vys. ucheb. zav.; tavet. met.4 no.2*.110-115 161.
(MIRA 14:6)
1. Moskovskiy institut stali, kafedra rentgenografii.
(Nibkel-aluminum allova-Testing)
(Powder metallurgy)

S/126/61/011/002/023/025
E073/E335
AUTHORSs Kalikhman, V.L., Umanskiy, U.S. and Chirikov, N.V.
TITLE- Study of the Diffusion Purobity occurring During
Distillation of Chromium From Single Crystals of
the Alloy 3'A'07E (EI437B)
PERIODICALz Fizika metallov i metallovedeniye, 1961, Vol. 11,
No. 2, Pp. 314 - 316
TEXTt As shown in other work by the authors (to be published
in 1-1,etallovedeniye i termicheskaya obrabotka metallov) diffusion
porosity occurs during distillation of chromium from the alloy
(Kh20N80), whereby the pores are equally oriented
witnin the limits of I grain, By means of a method described
in an earlier paper (Ref. 3), the authors attempted to determine
the orientation of the pores in the initial stages of their
growth with respect to the crystal lattice of the alloy. Since
they did not manage to grow sufficiently large crystals of the
alloy Kh2ON80 by recrystallisation, the authors used large
crystals obtained accidentally in scrap material from the
alloy EI437B, the composition of which is similar to that of
r" - - 1 4,46.
SM

s/126/61/011/002/023/025
Study of .... E073/E335
Kh20N80. The single-crystal film which is required for
investigating the pores by the method of small-angle X-ray
scattering was obtained by mechanical grinding to a thickness
of 150 0, followed by electropolishing to a thickness of
60 p, The electi-olytic thickness-reduction did not ensure total
removal of the work-hardened layer and the Laue pattern is
blurred ( Fig. 1 - pertaining to a single-crystal film of the
alloy E1437B, the surface plane of' which is near to the plane
(100) ).However, specimens produced from thicker sheet by
electrolytic polishing were considerably nonuniform as regards
thickness' The Cr distillation was effected in a quartz
ampule (which was connected continuously to a pre-vacuum
punip) at 1 3300C for 2.5 hours. Shorter distillation times
did not produce porosities. After Lerminating the distillation
process, the specimen was rapidly thrown into the cooled part
of the ampule to eliminate falling-out of the ordered phase.
Some of the 9pe ciwens crystallised during distillation
and broke up into a number of small grains, whilst others
remained single crystals. Curves of the drop in intensity of
Card 2/f

S/126/61/011/002/023/025
Study of .... E073/9335
the small-angle scattering as a function of the distance
from the edge of the primary beam were plotted by photo-
metering the X-ray diffraction patterns which were obtained
by means of slot equipment built as described by Kratky (Ref.
The slot was located in differing crystallographic directions.
Specimens were investigated, the surfaces of which were near
to the plane (111) and (100) . The photometric curves were
standardised in such a way that the intensities at a distance
of 11 from the edge of the primary beam were equal for all the
X-ray diffraction patterns taken from the same specimen,
Following that, lines of' equal intensity were plotted in the
polar coordinates (angles-intensity). The thus obtained
graphs are plotted in Figs. 2a and b (curves of equal
intensity of low-angle scattering in various directions:
Fig 2a. - specimen surface near to the plane (111), 1, 2, 3, .--8,/
mini Fig. 2b - specimen surface near to the plane (100).
1, 2, 3, ...6 min). It can be seen that the intensity of low-
angle scattering of X-rays drops more slowly for a specimen,
the surface plane of which is near to the plane (111) if the
Card 3/

Study of .... S/126/61/011/002/023/025
E073/E335
Blot is ill the directioll
metering direction ~.2-111((corresponding to the photo-
This means that in the direction
~110~ the dimension 'of -tile 130170 nucleus is at n minimum (Ref. 3)4_/
The anisotropy of the drop In intensity for specimens with the
surface plane near to the plane (100) confirms these
conclusions,, It is pointed out that the anisotropy of low-
angle scattering for the alloy EI437B is not as pronounced as
it is for brass, This is attributed to the fact that the
alloy is strongly contaminated with nonmetallic inclusions
with irregular boundaries, which can be clearly seen in
unetched polished cuts. They can serve as a basis for forming
arbitrarilv oriented pores,
There are 2 figures and 4 Soviet references.
ASSOCIATION: Moskovskiy institut stali im. 1.V. Stalina
Moscow Institute of Steel im. I.V. Stalin)
SUBMITTED: September 8, 196o
card

UMANSrIY, U.S.
Present-day problems In the x-ray study zaterials. Zav.lab. 27
no.6t635-637 161. (KMA 14:6)
(Materials,.Testing)
(X raya- -Industrial applications)

KALIKHMAN, V.L.; UMANSKIY9 Ya.s.
Application of the method of small-Angle scattering of
x rays in the study of submicroscopic inhwegenei-.ies in
materials; survey. Zav.lab. 27 no.6a.691-698 061. (MIRA 14:6)
(X rays-Industrial applications)
(Materials-Testing)

S/659/62/608/000/018/028
1048/1248
AUTHORS: Kalikhman, V.L., Umanskiy,, Ya*S*,, and Chirikov, N.V.
TITLE: A study of the appearance and growth of diffusion poro-
sity during the evaporatlon of the volatile component
from some nickel-based alloys
SOUPCE: Akademiya nauk SSSR, Institut metallurgii, Issliedovaniya
po zharoprochnym splavam. v,.8.- 1962. 127-131
TEXT: Equations for calculating the size and amount of submicro
diffusion pores in metals and alloys from small-angle x-ray scatter-
Ing data are derived. These equations were used to calculate the
diffusion porosity of Ni-26.9% Mn and Ni -: 27.6% Zn alloys. The
alloy specimens (foil 30 microns thick) were heated in vacuo to 800-
11000C to evaporate the more volatile component, The pore size In-
creased at 'first with increasing time at the,,qlevated temperature,
'reached a maximum and decreased thereafter. , The pores could be
classif:Led into two groups according to size;the maximum sizes are
400 angstrom in the first.and 1500 angstrom in the second group.
Card 1/2

S/65~9
,/62/008/000/018/028
1048/1248
A study of the appearance_and growth...
It is assumed thst the gro'wth of the pores ig'an autocatalytic pro-
cess during,the first stnge~ of evaporation; the rate of growth de-
creases with time during to the exhaustion of the vacancy sources
within the alloy. The frnation of diffusion porosity in the total
porosity amounts to 18-20i'of in the specimens subjected to evaporat-
ion at 8000C and decreases with both time and increasing temperatureo
There are 4 figures,,
Card 2/2

S/181/62/004/006/011/051
B125/BI04
AUTHORS; Semenovskaya, S. V., and Umanskiy, Ya. S.
TITLEz Radiographic determination of Focht's elastic constants and
the transverse branches of the phonon spectrum for dis-
ordered substitution solid solutions with cubic structure
PE.HIODICALt Fizika tverdogo tela, v. 4, no. 6, 1962, 1455 - 1465
4
.TEXT: Focht 18 constants and the transverse branches of the phonon spectrum
for disordered subatitution-solid solutions (8 at% Al in Cu) with cubic
structure (faoe-centered,'body-centered, or simply cubic) were determined
by an isothermal method. After measuring the absolute intensity of the
diffuse X-ray scattering,fo;_fsmall wave vectors 121 (that means, when the
classical theory of elasticl,4,.-~an be applied), one obtains the frequency
bf the transverse branches~o e phonon spectrum by using the formula
for the intensity of thermak4.4
,,I-ffuse single-phonon scattering. The
velocities of sound c(E in thd different directions are obtained f~rom four
0 -1.
diffusion equations (two transverse branches for k along 1101 and one
Card 1/2

S/181/62/004/006/011/051
Radiographic determination of ... H125/BI04
transverse branch each for k along ~10 and ~115). The elastic constants
c c , and a are calculated from the values of c(s). To obtain' the
112 12 44 0
ratio between the elastic constants it is sufficient to determine three
v
ratios of diffuse scattering intensities around a 116] reflex in the
directions ~0011, ~,iTol, and FITO. The determination of ihe absolute
value for the consi-ants--of elasticity also requires a knowledge of the
absolute value of one of the isotropic macroscopic moduli (Young's modulus,
shear modulus, or compressibility). To obtain the transverse branch of
U '000~,
the phonon spectrum for a wave vector directed along ~110j, and
jill-*~ it is necessary to measure the intensity of diffuse scattering around
the (200) reflex in the directions 0], and [011-1, around the (220)
L109, 9- 1
reflex in the directions ~110 -OT03, and LiT13, and around the (111)
reflex in the directions I There is 1 figure.
11 ~~
ASSOCIATIONs Moskovskiy institut stali (Moscow St.eel~,Inetjtute
SUBMITTEDs January 6, 1962
Card 2/2

3/048/62/026/003/r,04/015
B107/B102
/A
AUTHORS: Ol'shanakaya, E. Ya., Nekrasov, Yu. V., and Umanskiy, Ya. S.
TITLE: Examination of order in the alloy W + 44 atom~a Mo by
measuring the diffuse X-ray scattering
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Seriya fizicheskaya, v. 26,
no. 3, 1962, 349-351
TEXT: The degree of order in the alloY W + 44~* Mo at 1100, 1350, and
17000C was studied. A VC-500 (URS-50I) diffractometer and CuKa radiation
monochromatized by a plane germanium crystal, were used for the examinatiorL
Radiation was recorded with an MCTP-4 (MSTR-4) argon counter. The.angular
range from 8 to 200 was measured; scattering from air was eliminated by
the use of a vacuum chamber (Ref. 1: A. S. Kagan, V. A. Somenkovt Ya. S.
Umanskiy, Kristallografiya, 5-, 468 (1960)). Temperature effect, Compton
effect, and Bragg scattering were mathematically eliminated. Ground
samples with etched surfaces were used for the examination, since absorp-
tion was considerable. The intensity distribution was determined
experimentally. The ourve for 17000C was calculated from
Card 113

S/048/62/026/003/004/01
Examination of order in the ... B107/.B102
I = N.CACB (A - /A)' a, sin Sr,
The short-range order coefficients ai resulting from it, are given
numerically. The positive signs of a 1and a 2 show the atoms of the same
type to prevail in the neighborhood of one atom, i.e. the Mo - W system
tends to segregate. Purthermore,the radial distribution of the atom
density of tungsten was determined from the formula
Rr) S2T (S) !Ial! As.
Sr
In general, the results of Fig. 2 agree with those of the first method.
The additional minimum between r3 and r 4 is explained by the fact that the
UPPOIr limit of integration, So, is 2.6 instead of co (Ref- 4, see belcw);
The degree of order increases slightly as temperature decreases, but still
is very low at all temperatures. The mixing energy appears to be very
low: it is 0-079 ev for 17000 C according to Ref- 5 (M. A. Krivoglaz, A. A.
Card 2/3

Examination of order in the ...
S1046162102610031004101"
B107/B102
Smirnov, Teoriya uporyadochivayushchikhsya splavov (Theory of ordering of
allots), At., 1958). There are 2 figures, I table, and 5 references:
3 Soviet and 2 non-Soviet. The two English-language references are:
Ref. 3: P. S. Rudman, B..L. Averbach, Acta metallurg.,I, 575 (1954);
Ref. 4: P. A. Flinn, B. L., Averbach, P. S. Rudman, Acta crystallogr.,
153 (1954).
Fig. 2: Curves of radial
distribution of the atom
density of W, (a tungsten
atom in the sphere center).
Card 3/3
Emma

S/048/62/026/003/005/015
B107/B102
AUTHORS: Vishnyakov, Ya. D., and Umanskiy, Ya. S.
TITLE: Formation of packing defects in alloys during the distillation
of the volati.le component
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Seriya fizicheskaya, v. 26,
no. 3, 1962, 352-353
TEXT: Zinc was distilled from a silver - zinc alloy with t face-centered
cubic lattice (,v Mt by weight of Zn) at 600-6500C and 10- mm Hg. The
0.08 mm thick plateewere cooled in air. A standard sample was cooled to
room temperature within 12 hrs in a furnace. The reflection patter4s
((111) and (200)) were recorded with aSPG-500 (URS-50I) diffractometer and
CuK emission. The distance between the two reflexes from the standard was
by 41 larger than that from the chilled sample. This is probably due to
packing defects. Since distillation changes the lattice constant, the ratio
si,,~200/,in~'111 (sines of the reflection angles) which is independent of the
lattice constant, is suggested for quantitative characterization of lattice
defects. In packing defects in a face-centered cubic lattice, (200)
Card 1/2

S/048/62/026/003/005/015
Formation of packing defects ... B107/B102
is displaced toward smaller, and (111) toward wider angles. The sine ratio
decreases by 0.026, whereas the greatest possible error in the determination
of this ratio is 0-015. Two competing processes of defeat concentrations
in the alloys are assumed to occur, since in some papers (Ref. 4: V. L.
Kalikhman, Ya. S. Umanskiy, K. V. Chirikov, Fizika metallov i metallovedeniy,
11, no. 2, 314 (1961)) channels with a (110) orientation were found to
appear when the volatile component is distilled off. The results of the
present paper show a concentration of defects in the (111) plane. The two
English-language references are: W. T. Read, Dislocations in crystals,
C. X. J., Wagner, metallurg., 5-, 427 (1957).
Card 2/?

39~85
1
S/0 145/002/009/016
B178/BIO4
AUTHORS: Seme4gy6kaya, S. V., and Umanakiy, Ya. S.
TITLE: Separate determination of dynamic and stati-c distortions
from weakening of the interference maxima of solid solutions
in any phonon spectrum
PERIODICAL: Akademiye, nauk SSSR. Doklady, v. 145, no. 2, 1962, 312-314
TF,XT-.- When solid solutions are formed or are thermally tr.eated,their
interference maxima are weakened by a'ohange in the mean aquarocdisplaoe-
ment.- of the elastic Atomic vibrations and by a statjo displacement of
atoms:
I = I exp(-(L + L
0 dyn stat
2 2 2 2
16n sin Q 2 16z sin 0
L U L U
dyn 2 dyn' stat 2 stat
2 3X 2 3X. 2
The quantities udyn and ustat can be determined separately as udyn is
temperature-dependent whereas u2 is not. The qUantity Z2 is
stat dy n
Card 1/3

S
/020
J62/145/002/009/018.
Separate determination of dynamic,,* B178/BI04
determined by
do.
+
Ron 0
C C
where m is the effective atomic mass of the solid solution a .
CID 1 2
gMdo is the number of vibrations of frequency ti; g M dtj 3. When
0
'A4kT
UM