SCIENTIFIC ABSTRACT ZAVYALOV, A.S. - ZAVYALOV, I.A.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001964020001-8
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: March 15, 2001
• Sequence Number: 1
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

Contempo=7 jLUO" and Their Heat -Treatment SOV/1558
Perel =A, Ye. 0. Pioper Selection of Steele for Case-harde4ed Parts 93
MirikoIr -the Carburizing and
V.Ti Initial Data,for Selecting Reg*s for
Beat. -Treatpieut of Vase-haidined Parts 104
Kaliain, A.T. A Modern Caxburizing Agent for 'Gas Carburizing and Cy4niung 116
Rakbj3htadt, A.G., O.N. Meshcherinoval, and V.V. Zikiyev. Properties and
Fleat. -Treatment of Boron-alloyed Spring Steels 132
Geller, 1~i* A* Impr6yements in the Compoaition and Heat Treatment of'Tool
Steels 149
Volkov., A&M., An'Investigation. of t3,603 Lw--!~Uqy Steel as a Material for
Cutting Tools 171
Ivanov, A.0, New Types of High-speed Sbdel 17-5
Golo~in,, GJ* Hardening and TesWering-of High-speed Steele With Induction
Heating 178
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~,aw ~_Mluffinlmalxm
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77

CoatmWorary JaIM aid fted Boat -TV A Ilk 1, It
Kbroleyp G#GV - leat-tre&tmant or CyAttlag Too~A In an Atme1*6re of Steam 186
-fao Defor=tion of Steel in quenching RA News of
K"Wkdyp Fe
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Preventing Xt 194
NmwrA.Oyp D *Me Deformation of StAel in Heat -Treatunt 2D7
mdmushin' POP, Heat-resistant SteelA and Allqu Zoloye4 in the Ccmatruction
of Gas Turbines 216
'Voroblyev,, V*G# Changes, in the Surface'Lejer of a Heat-reelstant Anoy During
Machining and Resting in an Oxidizing Yledi=
BbMkcff,, A.A. Rational Kethod of fttwining Controlled Atws]*ares Fr=
Gaseous HydromAms 254
AssdhIov A.D. Modern Autozated Heat lre&ting E(VdVmwt 265
Card 516

Contanpor=7 ILUoya and Their Neat-TresUmit SOV/1558
Shepelyakovskly., NZ, . fttumVfts*cta for the Use ce High.-Frequency Currents
In Machinia,B lding 279
Pondotsnko, N.S. Mecbanization of the Neat Treatmentof.Tools ~92
Pcimersnts., DeM. Magnetic Quality-control MetluA in the Heat Treatment of
N4
Xordanskiy,, V.No' Weldable Al=i==-j(a&*siua Alloys
Yeo Do Fatigue Strength of 1ndustrial Titaniun 314
Ellywheva, M.A. Strengil of Welded Joints Made of VTlD IndxLatrisa
Titanium 319
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ZA:VIYALOV, A,S.# doktor tekhn.nauk# prof.
Clmracteriatics of the~process of steel e--brItt--,e=ent under t-'-e
effect of hoating'and thwinfluence of addition elements on this
process. Metallovedenie 3:3-38 159. WIRA 24:3)
(Steel-Brittlonese)
MI.I.- 1110.1"R., IN

BRUKy B.I*# kand.tkohn.nauk; ZAVIY-ALOV# A.S., doktdr tekbn.naukv prof.1
XAPYRDTv G.I.,, kand.~~9-1-E~n.-i&--
Studying the redistributi6n~bf
-------- joints by the method orautoiadiogrAphy and radiometrya Metal-
16vedenie 30214~-M f59. (MIRA 14:3)
-(Metallography) (lutoradlography)
Nd.ioisoto'pes-Industrial application)
TIT 21
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- - ------- -----
66223
SOV/126-8-3-6/33
.AUTHORS: Z,avlyalov, A..$,and Bruk, B.1,
TITLEi On~ie Factors Determining theDistribution of Elements
Within Metallic Alloy Crystals
PERIODIGALffizika,metallov i metallovedeniye, 1959, Vol 8, Nr 3,
349-361 (USSR)
'ABSTRAGTt -Tho.authorahavo carried out a calculation of the
minimum thickness of the layor ortrichod in radioactive
carbon Along the austenitic grains capable of forming a
preferential blackening zone on a photographic emulsion
(Ref 5). The calculation has shown that In the case of
the normally applied fresh photographic emulsions and the
normal exposures and concentrations of radioactive carbon
in the alloy, the'minimum thickness of such a layer does
not exceed 102 - 10 interatomic distances. The
effectiveness of the application of the radiographic
method to the study of the nature of distribution of
impurities in iron alloys increases considerably if work
is carried out in which a radioactive isotope of carbon
is used. The reason for this is not only that the low
energy of the P-spectrum of the c14 isotope enables
Card 1/6 sufficiently clear radiographs to be obtained but also

66273
SOV/126-8-3-6/33
On the Factors Determining the Distribution of Elements Within
-Metallic Alloy.Crystals
that the distribution of carbon in iron alloys 13 closely
associated with the distribution or alloy elements. For
instance,-carbon tends to segregate in alloy zones which
aro enriched with carbido-forming elements, which can be
seen from the radio-autograph shown in Fig 1, taken from
a bimetallic specimen, tempered at 600*C, containing
radioactive carbon. Fig 2 shows the microstructure of
carbon steel containing 0.21% C after its surface had
been-saturated with silicon for 30 hours at 1050 ac.
F19 3 shows the microstructure of a carburized layer of
steel containing 4.4% silicon which had been slowly
cooled after carburization. Fig 4 shows the
,distribution of carbon in an iron alloy containing
19.5%, Si: a -.optical exposure, b - radio-autograph.
Fig 5 shows the distribution of carbon-in an iron alloy
containing 9.2% Wi a - optical exposure, b - radio-
autograph. Fig 6 shows the distribution of carbon in an
iron-alloy containing-1.9% W (radio-autograph). Fig 7
shows the dist,~,ibution of' carbon in an iron alloy
__ - __F_ c-
Card 2 -containing go a o p Vi it 1-0 X po-s u11W
_jp

66223
SOV/126-8-3-6/33
On the Factors Determining the Distribution of Elements Within
Metallic Alloy Crystals
b radio-autograph. Fig 8 shows the microscopic
-distribution carbon in an iron a lloy containing
4.4,09 Si (radio-autographs a - s owly cooled from
9700C, b - que nched from 250 0C and B - quenched from
IPOOOC and tempered at 590 C for 10 hours. Fig 9 shows
the diBtl4butio-n-of-carb-on in un-alloyed iron containing0
0.035% C after quenching from 1200*C and tempering at 590 C
for 10 hours (radio-autograph). Fig 10 shows the
microscopic distribution of carbon in iron alloys
containing 15% Mo (radio-autograph): a - slowly cooled
after crystallization 0 b - quenched from 1250*C,
B - quenched from 125; C and tempered at 800% for
15 hours. Fig 11 shows the microscopic distribution of
carbon in iron alloys containing 12% W (radio-autographs):
a - slowlI cooled after crystallization, b - quenched
from 1250 C, B - quenched from 1~50 and tempered at
800*C for 15 hours. The authors arrived at the following
conclusions: The-experimental data given in the present
article and in papers by ZavIyalov et alii (Ref 5 and 6)
Card 3/6 testify to the fact that the following general mechanisms

66223
SOV/126-8-3-6 3
On'the Factors Determining the Distribution of Elements With~ln
Metallic Alloy Crystals
operate in the distribution of elements in metallic
alloys: 1. If at a-given temperature the element
content does not exceed its limiting solubility in the
solvent metal, then this element is distributed
throughout the crystal body relatively evenly and does
not exhibit a tendency to preferential segregation along
the periphery,or centre of the crystal. 2. If the
element content at a given temperature exceeds its
limiting solubility in the solvent metal, then the excess
of this element will segregate along the alloy crystal
boundaries in the form of a phase enriched with the given
element or in a structurally free state. If the I
temperature of the alloy is changed its components, in
accordance with the equilibrium diagram, can either
concentrate in the grain boundary zones (it the limiting
solubility of the element decreases) or they can
distribute themselves within the crystal more evenly (if
the solubility of the element increases)- 3- If a one-
-phase alloy hasreached a stage, as a result of change in
-Card 4/6 temperature or concent do
ration conditions, which-procc,
'J

66223
SOV/126-8-3-6/33
On the Factors Determining the Distribution of Elements Within
Metallic Alloy Crystals
separation of a new phase, then those components of the
alloy,concentrate along the grain boundaries of this alloy
or along the boundaries of finer -crystal formations, e&g.,
"V ., mobaic blocks, with which the precipitating Phase
has become enriched. 4. The presence in the alloy of sonic
elements exerts an influence on the distribution within
the crystals of other elements. 5. The investigation
carried out shows that when considering the grain boundary
layers of multi-atomic thickness it is not possible to
assume that some elements are horophilic and others
horophobic with respect to the solvent metal (horophilic
elements are those which lower the surface energy of
phases, horophobic elements are those which raise it).
The tendency of the components of metallic alloys to
segregation along grain boundaries, or to diffusion from
the peripheral to the central layers of the grains, cannot
be determined by any conistant property of a giver), elemiunt
in relation to the fjolvent element but it can from the
relationship between the concentrations of components in
Card 5/6 alloys at a given temperature, which can be found fr ti

66223
Chri the Factors.Determining the DistrIibuti SOV/126-8-3-6/33
on of Elements Within
Metallic Alloy Crystals
equilibrium diagram-. -'In systems of more.than two
componentsi this relationship can also be found from the
difference in the bond forces between the elements furming
a given alloy, In accordnnce with tho equilibrium diagrnm
of a given alloy, the samo element in various
temperature ranges and at various component concentrations
of a one-phase system-can segregate preferentially either
in the surface layers or in the centres of crystAls.
There are 11 figures and 6 Soviet referenceti.
SUBMITTEDi August 6, 1958
Card 6/6

S1659162VO0910001008JO30
1003/1203
AUTHORS Bruk, B. 1. and Zav'yalov, A, &
TITLE: Redistribution of carbides as one of the forms of structural instability of ferrous alloys
SOURCE. Akademiya nauk SSSR, Institut metallurgii. Issledovaniya po zharoprochnym splavarn.
v. 9.1962. MaterialyNauchnoysessil pozharoprochnymsplavam (1961 g.), 60-66
TEXT; - The movements ofthe excess phase (in this case the carbide phase) towards the grains boundaries is
one of the forms of structural changes rarely mentioned in the literature. Structural changes taking place on
beating of ferric and austenitic steels I x 19H 10(l Kh I 9N 10), 1 x 15H25M5(I Kh I 5N25M5) 10 x M(D(IOKhMF)
10 x MOO (IOKhMFS3) to various temperatures were investigated by using the C14 isotope as a radioactive
indicator. The photomicrographs taken show that a concentration of the excess phase may take place along
the grain boundaries and crystal planes, The presence of the cabide-forming elements in constructional
steels inhibits the movement of the above phases towards the grain boundaries during prolonged heating
In a Cr-Mo-V-Si pcrlitic steel such a process takes place most rapidly in the range of temperatures from
350* to 500*C. The data on the temperature range and on the kinetics of the process of redistribution of
carbides in steel, obtained in this work clarify the nature of the process by which the steels become brittle.
when subjected for a long time to high temperatures. There are 6 figures and I table.
Card 1/1

34842
VaV62/ooo/m/m/ooq
E021/1',335
AUTHORS; Bruk, D.I., Candidate of Technical Sciences and
ZIIxIvaj.Q&j..A.S. , Doctor of Technical Sciences.
Profossor
TITLE~ ItedistribuLion of carbidois as a form oV mtructural
-instability of stool
PERIODICAL: Metallovedeniye i tormichoskaya obraboLka metallov.,
no. 3, 1962t 14 - 18
TEXT, The structural instability of the following steels
was studied by autoradiography, using C,4 as the indicator.
C Cr Mo v Mn Ni.
Ix-IqjAIO(.IKh19NlO) 0, 07104 19.3 0.30 0.22 10.1
lK.I5H25N5W(II(hl5N25M5)